CA2187269C - Semiconductor substrate and producing method thereof - Google Patents

Semiconductor substrate and producing method thereof Download PDF

Info

Publication number
CA2187269C
CA2187269C CA002187269A CA2187269A CA2187269C CA 2187269 C CA2187269 C CA 2187269C CA 002187269 A CA002187269 A CA 002187269A CA 2187269 A CA2187269 A CA 2187269A CA 2187269 C CA2187269 C CA 2187269C
Authority
CA
Canada
Prior art keywords
porous
layer
substrate
semiconductor substrate
producing method
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Expired - Fee Related
Application number
CA002187269A
Other languages
French (fr)
Other versions
CA2187269A1 (en
Inventor
Nobuhiko Sato
Takao Yonehara
Kiyofumi Sakaguchi
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Canon Inc
Original Assignee
Canon Inc
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Canon Inc filed Critical Canon Inc
Publication of CA2187269A1 publication Critical patent/CA2187269A1/en
Application granted granted Critical
Publication of CA2187269C publication Critical patent/CA2187269C/en
Anticipated expiration legal-status Critical
Expired - Fee Related legal-status Critical Current

Links

Classifications

    • HELECTRICITY
    • H01ELECTRIC ELEMENTS
    • H01LSEMICONDUCTOR DEVICES NOT COVERED BY CLASS H10
    • H01L21/00Processes or apparatus adapted for the manufacture or treatment of semiconductor or solid state devices or of parts thereof
    • H01L21/02Manufacture or treatment of semiconductor devices or of parts thereof
    • H01L21/02002Preparing wafers
    • H01L21/02005Preparing bulk and homogeneous wafers
    • H01L21/02032Preparing bulk and homogeneous wafers by reclaiming or re-processing
    • HELECTRICITY
    • H01ELECTRIC ELEMENTS
    • H01LSEMICONDUCTOR DEVICES NOT COVERED BY CLASS H10
    • H01L21/00Processes or apparatus adapted for the manufacture or treatment of semiconductor or solid state devices or of parts thereof
    • H01L21/02Manufacture or treatment of semiconductor devices or of parts thereof
    • H01L21/04Manufacture or treatment of semiconductor devices or of parts thereof the devices having at least one potential-jump barrier or surface barrier, e.g. PN junction, depletion layer or carrier concentration layer
    • H01L21/18Manufacture or treatment of semiconductor devices or of parts thereof the devices having at least one potential-jump barrier or surface barrier, e.g. PN junction, depletion layer or carrier concentration layer the devices having semiconductor bodies comprising elements of Group IV of the Periodic System or AIIIBV compounds with or without impurities, e.g. doping materials
    • H01L21/20Deposition of semiconductor materials on a substrate, e.g. epitaxial growth solid phase epitaxy
    • HELECTRICITY
    • H01ELECTRIC ELEMENTS
    • H01LSEMICONDUCTOR DEVICES NOT COVERED BY CLASS H10
    • H01L21/00Processes or apparatus adapted for the manufacture or treatment of semiconductor or solid state devices or of parts thereof
    • H01L21/02Manufacture or treatment of semiconductor devices or of parts thereof
    • H01L21/04Manufacture or treatment of semiconductor devices or of parts thereof the devices having at least one potential-jump barrier or surface barrier, e.g. PN junction, depletion layer or carrier concentration layer
    • H01L21/18Manufacture or treatment of semiconductor devices or of parts thereof the devices having at least one potential-jump barrier or surface barrier, e.g. PN junction, depletion layer or carrier concentration layer the devices having semiconductor bodies comprising elements of Group IV of the Periodic System or AIIIBV compounds with or without impurities, e.g. doping materials
    • H01L21/30Treatment of semiconductor bodies using processes or apparatus not provided for in groups H01L21/20 - H01L21/26
    • H01L21/322Treatment of semiconductor bodies using processes or apparatus not provided for in groups H01L21/20 - H01L21/26 to modify their internal properties, e.g. to produce internal imperfections
    • H01L21/3221Treatment of semiconductor bodies using processes or apparatus not provided for in groups H01L21/20 - H01L21/26 to modify their internal properties, e.g. to produce internal imperfections of silicon bodies, e.g. for gettering
    • HELECTRICITY
    • H01ELECTRIC ELEMENTS
    • H01LSEMICONDUCTOR DEVICES NOT COVERED BY CLASS H10
    • H01L21/00Processes or apparatus adapted for the manufacture or treatment of semiconductor or solid state devices or of parts thereof
    • H01L21/02Manufacture or treatment of semiconductor devices or of parts thereof
    • H01L21/04Manufacture or treatment of semiconductor devices or of parts thereof the devices having at least one potential-jump barrier or surface barrier, e.g. PN junction, depletion layer or carrier concentration layer
    • H01L21/18Manufacture or treatment of semiconductor devices or of parts thereof the devices having at least one potential-jump barrier or surface barrier, e.g. PN junction, depletion layer or carrier concentration layer the devices having semiconductor bodies comprising elements of Group IV of the Periodic System or AIIIBV compounds with or without impurities, e.g. doping materials
    • H01L21/30Treatment of semiconductor bodies using processes or apparatus not provided for in groups H01L21/20 - H01L21/26
    • H01L21/322Treatment of semiconductor bodies using processes or apparatus not provided for in groups H01L21/20 - H01L21/26 to modify their internal properties, e.g. to produce internal imperfections
    • H01L21/3221Treatment of semiconductor bodies using processes or apparatus not provided for in groups H01L21/20 - H01L21/26 to modify their internal properties, e.g. to produce internal imperfections of silicon bodies, e.g. for gettering
    • H01L21/3223Treatment of semiconductor bodies using processes or apparatus not provided for in groups H01L21/20 - H01L21/26 to modify their internal properties, e.g. to produce internal imperfections of silicon bodies, e.g. for gettering using cavities formed by hydrogen or noble gas ion implantation
    • HELECTRICITY
    • H01ELECTRIC ELEMENTS
    • H01LSEMICONDUCTOR DEVICES NOT COVERED BY CLASS H10
    • H01L21/00Processes or apparatus adapted for the manufacture or treatment of semiconductor or solid state devices or of parts thereof
    • H01L21/02Manufacture or treatment of semiconductor devices or of parts thereof
    • H01L21/04Manufacture or treatment of semiconductor devices or of parts thereof the devices having at least one potential-jump barrier or surface barrier, e.g. PN junction, depletion layer or carrier concentration layer
    • H01L21/18Manufacture or treatment of semiconductor devices or of parts thereof the devices having at least one potential-jump barrier or surface barrier, e.g. PN junction, depletion layer or carrier concentration layer the devices having semiconductor bodies comprising elements of Group IV of the Periodic System or AIIIBV compounds with or without impurities, e.g. doping materials
    • H01L21/30Treatment of semiconductor bodies using processes or apparatus not provided for in groups H01L21/20 - H01L21/26
    • H01L21/322Treatment of semiconductor bodies using processes or apparatus not provided for in groups H01L21/20 - H01L21/26 to modify their internal properties, e.g. to produce internal imperfections
    • H01L21/3221Treatment of semiconductor bodies using processes or apparatus not provided for in groups H01L21/20 - H01L21/26 to modify their internal properties, e.g. to produce internal imperfections of silicon bodies, e.g. for gettering
    • H01L21/3226Treatment of semiconductor bodies using processes or apparatus not provided for in groups H01L21/20 - H01L21/26 to modify their internal properties, e.g. to produce internal imperfections of silicon bodies, e.g. for gettering of silicon on insulator
    • HELECTRICITY
    • H01ELECTRIC ELEMENTS
    • H01LSEMICONDUCTOR DEVICES NOT COVERED BY CLASS H10
    • H01L21/00Processes or apparatus adapted for the manufacture or treatment of semiconductor or solid state devices or of parts thereof
    • H01L21/70Manufacture or treatment of devices consisting of a plurality of solid state components formed in or on a common substrate or of parts thereof; Manufacture of integrated circuit devices or of parts thereof
    • H01L21/71Manufacture of specific parts of devices defined in group H01L21/70
    • H01L21/76Making of isolation regions between components
    • H01L21/762Dielectric regions, e.g. EPIC dielectric isolation, LOCOS; Trench refilling techniques, SOI technology, use of channel stoppers
    • H01L21/7624Dielectric regions, e.g. EPIC dielectric isolation, LOCOS; Trench refilling techniques, SOI technology, use of channel stoppers using semiconductor on insulator [SOI] technology
    • H01L21/76251Dielectric regions, e.g. EPIC dielectric isolation, LOCOS; Trench refilling techniques, SOI technology, use of channel stoppers using semiconductor on insulator [SOI] technology using bonding techniques
    • HELECTRICITY
    • H01ELECTRIC ELEMENTS
    • H01LSEMICONDUCTOR DEVICES NOT COVERED BY CLASS H10
    • H01L21/00Processes or apparatus adapted for the manufacture or treatment of semiconductor or solid state devices or of parts thereof
    • H01L21/70Manufacture or treatment of devices consisting of a plurality of solid state components formed in or on a common substrate or of parts thereof; Manufacture of integrated circuit devices or of parts thereof
    • H01L21/71Manufacture of specific parts of devices defined in group H01L21/70
    • H01L21/76Making of isolation regions between components
    • H01L21/762Dielectric regions, e.g. EPIC dielectric isolation, LOCOS; Trench refilling techniques, SOI technology, use of channel stoppers
    • H01L21/7624Dielectric regions, e.g. EPIC dielectric isolation, LOCOS; Trench refilling techniques, SOI technology, use of channel stoppers using semiconductor on insulator [SOI] technology
    • H01L21/76251Dielectric regions, e.g. EPIC dielectric isolation, LOCOS; Trench refilling techniques, SOI technology, use of channel stoppers using semiconductor on insulator [SOI] technology using bonding techniques
    • H01L21/76254Dielectric regions, e.g. EPIC dielectric isolation, LOCOS; Trench refilling techniques, SOI technology, use of channel stoppers using semiconductor on insulator [SOI] technology using bonding techniques with separation/delamination along an ion implanted layer, e.g. Smart-cut, Unibond
    • HELECTRICITY
    • H01ELECTRIC ELEMENTS
    • H01LSEMICONDUCTOR DEVICES NOT COVERED BY CLASS H10
    • H01L21/00Processes or apparatus adapted for the manufacture or treatment of semiconductor or solid state devices or of parts thereof
    • H01L21/70Manufacture or treatment of devices consisting of a plurality of solid state components formed in or on a common substrate or of parts thereof; Manufacture of integrated circuit devices or of parts thereof
    • H01L21/71Manufacture of specific parts of devices defined in group H01L21/70
    • H01L21/76Making of isolation regions between components
    • H01L21/762Dielectric regions, e.g. EPIC dielectric isolation, LOCOS; Trench refilling techniques, SOI technology, use of channel stoppers
    • H01L21/7624Dielectric regions, e.g. EPIC dielectric isolation, LOCOS; Trench refilling techniques, SOI technology, use of channel stoppers using semiconductor on insulator [SOI] technology
    • H01L21/76251Dielectric regions, e.g. EPIC dielectric isolation, LOCOS; Trench refilling techniques, SOI technology, use of channel stoppers using semiconductor on insulator [SOI] technology using bonding techniques
    • H01L21/76259Dielectric regions, e.g. EPIC dielectric isolation, LOCOS; Trench refilling techniques, SOI technology, use of channel stoppers using semiconductor on insulator [SOI] technology using bonding techniques with separation/delamination along a porous layer
    • HELECTRICITY
    • H01ELECTRIC ELEMENTS
    • H01LSEMICONDUCTOR DEVICES NOT COVERED BY CLASS H10
    • H01L31/00Semiconductor devices sensitive to infrared radiation, light, electromagnetic radiation of shorter wavelength or corpuscular radiation and specially adapted either for the conversion of the energy of such radiation into electrical energy or for the control of electrical energy by such radiation; Processes or apparatus specially adapted for the manufacture or treatment thereof or of parts thereof; Details thereof
    • H01L31/18Processes or apparatus specially adapted for the manufacture or treatment of these devices or of parts thereof
    • H01L31/1892Processes or apparatus specially adapted for the manufacture or treatment of these devices or of parts thereof methods involving the use of temporary, removable substrates
    • YGENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02EREDUCTION OF GREENHOUSE GAS [GHG] EMISSIONS, RELATED TO ENERGY GENERATION, TRANSMISSION OR DISTRIBUTION
    • Y02E10/00Energy generation through renewable energy sources
    • Y02E10/50Photovoltaic [PV] energy

Abstract

A method is provided for producing, with high reproducibility, an SOI substrate which is flat and high in quality, and simultaneously for achieving resources saving and reduction in cost through recycling of a substrate member. For accomplishing this, a porous-forming step is performed forming a porous Si layer on at least a surface of an Si substrate and a large porosity layer forming step is performed for forming a large porosity layer in the porous Si layer. This large porosity layer forming step is performed by implanting ions into the porous Si layer with a given projection range or by changing current density of anodization in said porous-forming step. At this time, a non-porous single-crystal Si layer is epitaxial-grown on the porous Si layer.
Thereafter, the surface of the porous Si layer and a support substrate are bonded together, and then separation is performed at the porous Si layer with the large porosity. Subsequently, selective etching is performed to remove the porous Si layer.

Description

CA
1 - 2 1 ~ 72 CqFO 11733 ~

SEMICONDUCTOR SUBSTRATE AND PRODUCING METHOD THEREOF

BACKGROUND OF THE INVENTION
Field of the Invention The present invention relates to a semiconductor substrate and a producing method thereof. More specifically, the present invention relates to dielectric isolation or a producing method of a single-crystal semiconductor on an insulator and a single-crystal compound semiconductor on an Si substrate, and further relates to a producing method of a semiconductor substrate suitable for an electronic device or an integrated circuit formed at a single-crystal semiconductor layer.
Related Background Art Formation of a single-crystal Si semiconductor layer on an insulator is widely known as a silicon on insulator (SOI) technique and has been researched to a large extent since a device utilizing the SOI technique has a number of advantageous points which can not be achieved by a bulk Si substrate forming the normal Si integrated circuit. Specifically, for example, the following advantageous points can be achieved by employing the SOI technique:
1. Dielectric isolation is easy and high integration is possible;
2. Radiation resistance is excellent;

21 8726q 3. Floating capacitance is reduced and high speed is possible;
4. Well process can be omitted;
5. Latch-up can be prevented;
6. Fully depleted (FD) field effect transistor is achieved through film thickness reduction.
These are described in detail, for example, in the literature of Special Issue: "Single-crystal silicon on non-single-crystal insulators"; edited by G.W. Cullen, Journal of Crystal Growth, volume 63, no 3, pp 429-590 (1983).
Further, over the past few years, the SOI has been largely reported as a substrate which realizes the acceleration of a MOSFET and the low power consumption (IEEE SOI conference 1994). Since an element has an insulating layer at its lower part when employing the SOI structure, an element separation process can be simplified as compared with forming an element on a bulk silicon wafer so that a device process can be shortened. Specifically, in addition to achieving the higher performance, reduction of the wafer cost and the process cost is expected in total as compared with a MOSFET or IC on bulk silicon.
Particularly, the fully depleted (FD) MOSFET is expected to achieve the higher speed and the lower power consumption through improvement in driving force.
In general, a threshold voltage (Vth) of a MOSFET is determined by the impurity concentration at a channel portion. On the other hand, in case of the FD MOSFET
using the SOI, a depletion layer is also subjected to an influence of a film thickness of the SOI. Thus, for producing the large scale integrated circuits at the high yield, uniformity of the SOI thicknesses has been strongly demanded.
On the other hand, a device on a compound semiconductor has the high performance, such as, high speed and luminescence, which can not be achieved by Si. Presently, such a device is normally formed in an epitaxial layer grown on a compound semiconductor substrate, such as a GaAs substrate.
However, there is a problem that the compound semiconductor substrate is expensive while low in mechanical strength so that the large area wafer is difficult to be produced.
Under these circumstances, an attempt has been made to achieve the heteroepitaxial growth of a compound semiconductor on an Si wafer which is inexpensive and high in mechanical strength so that the large area wafer can be produced.
Referring back to the SOI, the researches on formation of the SOI substrates have been active since the 1970s. In the beginning, the researches were well performed in connection with the SOS (sapphire on silicon) method which achieves the heteroepitaxial growth of single-crystal silicon on a sapphire substrate being an insulator, the FIPOS (fully isolation by porous oxidized silicon) method which forms the SOI structure by dielectric isolation based on oxidation of porous Si, and the oxygen ion implantation method.
In the FIPOS method, an n-type Si layer is formed on a surface of a p-type Si single-crystal substrate in the island shape through the proton ion implantation (Imai and collaborator, J. Crystal Growth, vol 63, 547 (1983)) or through the epitaxial growth and the patterning, then only the p-type Si substrate is rendered porous so as to surround the Si island from the surface by means of the anodizing method in a HF
solution, and thereafter the n-type Si island is dielectric-isolated through accelerating oxidation. In this method, there is a problem that the isolated Si region is determined in advance of the device process so that the degree of freedom of device designing is limited.
The oxygen ion implantation method is a method called SIMOX first reported by K. Izumi. After implanting about 1017 to 1018/cm2 of oxygen ions into an Si wafer, the ion-implanted Si wafer is annealed at the high temperature of about 1,320C in the atmosphere of argon/oxygen. As a result, oxygen ions implanted with respect to a depth corresponding to a projection range 2 1 8~269 (Rp) of ion implantation are bonded with silicon so as to form a silicon oxide layer. On this occasion, a silicon layer which has been rendered amorphous at an upper portion of the silicon oxide layer due to the S oxygen ion implantation is also recrystallized so as to be a single-crystal silicon layer. Conventionally, there have been a lot of defects included in the silicon layer on the surface, that is, about 105/cm2.
On the other hand, by setting an implantation amount of oxygen to about 4xl017/cm2, defects are successfully reduced to about 102/cm2. However, since the ranges of implantation energy and implantation amount for maintaining the quality of the silicon oxide layer, the crystalline property of the surface silicon layer and the like are so narrow that thicknesses of the surface silicon layer and the buried silicon oxide (BOX: buried oxide) layer were limited to particular values. For achieving a desired thickness of the surface silicon layer, it was necessary to perform sacrificial oxidation and epitaxial growth. In this case, there is a problem that, since the degradation caused through these processes is superposed on the distribution of thicknesses, the thickness uniformity is deteriorated.
It has been reported that a formation failure region of silicon oxide called a pipe exists in the BOX
layer. As one cause of this, the foreign matter upon implantation, such as dust, is considered. In the 2 1 87~6~

portion where the pipe exists, the deterioration of the device characteristic is generated due to leak between an active layer and a support substrate.
Further, since the ion implantation in the SIMOX
is large in implantation amount as compared with the ion implantation in the ordinary semiconductor process, implantation time is long even after the apparatus to be used exclusively for that matter has been developed.
The ion implantation is performed by raster-scanning an ion beam of a given current amount or expanding the beam so that increment of the implantation time is predicted following increment in area of the wafer.
Further, in the high temperature heat treatment of the large-area wafer, it has been pointed out that a problem of occurrence of slip due to the temperature distribution in the wafer becomes severer. In the SIMOX, the heat treatment is essential at the high temperature, that is, 1,320C, which is not normally used in the silicon semiconductor process, so that there has been concern that this problem including the development of the apparatus becomes more significant.
On the other hand, apart from the foregoing conventional SOI forming method, attention has been recently given to the method which forms the SOI
structure by sticking an Si single-crystal substrate to a thermal-oxidized Si single-crystal substrate through the heat treatment or using adhesives. In this method, ~ ~ 7 ~ 2l 8 726 9 it is necessary to form an active layer for the device into a uniform film. Specifically, it is necessary to form an Si single-crystal substrate of a thickness of as much as hundreds of microns into a film of several microns or less. There are three kinds of methods for thickness reduction as follows:
1. Thickness reduction through polishing;
2. Thickness reduction through local plasma etching;
3. Thickness reduction through selective etching.
In the polishing of 1, the uniform thickness reduction is difficult. Particularly, in case of thickness reduction to submicrons, the irregularity amounts to as much as tens of percents so that uniformalization is a big problem. If the size of wafer is further enlarged, the difficulty is increased correspondingly.
In the method of 2, after reducing the thickness to about 1 to 3,um through the polishing of 1, the thickness distribution is measured at many points.
Thereafter, by scanning the plasma using the SF6 of a diameter of several millimeters based on the thickness distribution, etching is performed while correcting the thickness distribution, so as to reduce the thickness to a given value. In this method, it has been reported that the thickness distribution can be within the range of about +lOnm. However, if the foreign matter (particles) exists on the substrate upon plasma 2 1 872~

etching, the foreign matter works as an etching mask so that projections are formed on the substrate.
Since the surface is rough immediately after the etching, touch polishing is necessary after completion of the plasma etching. The polishing amount is controlled based on the time management, and hence, the final film thickness control and the deterioration of film thickness distribution due to polishing have been pointed out. Further, in the polishing, abrasives such as colloidal silica directly rub the surface working as an active layer so that there has been concern about formation of a fracture layer due to polishing and introduction of processing distortion. Further, if the wafer is increased in area to a large extent, since the plasma etching time is increased in proportion to increment of the wafer area, there is concern about extreme reduction of the throughput.
In the method of 3, a film structure capable of selective etching is formed in advance in a substrate to be formed into a film. For example, a p+-Si thin layer containing boron in the concentration no less than 1019/cm3 and a p--Si thin layer are formed on a p~
substrate using the method of, for example, the epitaxial growth so as to form a first substrate. The first substrate is bonded with a second substrate via an insulating layer such as an oxide film, and then the underside of the first substrate is ground or polished - 9 - 2 1 8 72~ ~

in advance so as to reduce in thickness. Thereafter, the p+ layer is exposed through the selective etching of the p~ layer and further the p~ layer is exposed through the selective etching of the p+ layer, so as to achieve the SOI structure. This method is detailed in the report of Maszara.
Although the selective etching is said to be effective for uniform thickness reduction, it has the following problems:
The ratio of etching selectively is 102 at most, which is not sufficient.
Since the surface property after etching is bad, the touch polishing is required after etching.
However, as the result thereof, the film thickness is reduced and the thickness uniformity tends to be deteriorated. Particularly, although the polish amount is managed based on time, since dispersion of the polish speed is large, the control of the polish amount is difficult. Thus, it becomes a problem particularly in forming an extremely thin SOI layer of, for example, lOOnm.
The crystalline property is bad because of using the ion implantation, the epitaxial growth or the heteroepitaxial growth on the high-concentration B dope Si layer.
The surface property of a surface to be bonded with is inferior to the normal silicon wafer (C.

_ - 10 ~ 2 1 8 7 ~ 6 q Harendt, et. al., J. Elect. Mater. Vol. 20, 267 (1991), H. Baumgart, et. al., Extended Abstract of ECS 1st International Symposium of Wafer Bonding, pp-733 (1991), C.E. Hunt, Extended Abstract of ECS 1st International Symposium of Wafer Bonding, pp-696 (1991)). Further, the selectivity of selective etching largely depends a difference in concentration of impurities such as boron and sharpness of the profile in the depth direction. Accordingly, if the high-temperature bonding annealing for increasing thebonding strength or the high-temperature epitaxial growth for improving the crystalline property is performed, the depth direction distribution of the impurity concentration expands so that the selectivity of etching is deteriorated. That is, it is difficult to improve both the ratio of etching selectively and the crystalline property or the bonding strength.
Recently, in view of the foregoing problems, Yonehara and collaborators have reported the bonded SOI
which is excellent in thickness uniformity and crystalline property and capable of batch processing.
Brief explanation about this will be given using Figs.
6A to 6E. In this method, a porous layer 62 formed on an Si substrate 61 is used as a material for selective etching (Fig. 6A). After epitaxial-growing a non-porous single-crystal Si layer 63 on the porous layer 62 (Fig. 6B), the three-layer composite is bonded with -11- 218~269 a support substrate 64 via the oxidized Si layer 63 (Fig. 6C). The Si substrate 61 is reduced in thickness through grinding or the like from the underside so as to expose the porous Si 62 all over the substrate (Fig.
6D). The exposed porous Si 62 is removed through etching using a selective etching liquid, such as, KOH
or HF+H202 (Fig. 6E). At this time, since the ratio of etching selectively porous Si relative to bulk Si (non-porous single-crystal silicon) can be set fully high, that is, 100,000 times, the non-porous single-crystal silicon layer grown on the porous layer in advance can be left on the support substrate without being hardly reduced in thickness, so as to form the SOI substrate.
Accordingly, the thickness uniformity of the SOI is substantially determined during the epitaxial growth.
Since a CVD apparatus used in the normal semiconductor process can be used for the epitaxial growth, according to the report of Sato and collaborator, the thickness uniformity is realized, for example, within lOOnm _ 2%.
Further, the crystalline property of the epitaxial silicon layer is also excellent and has been reported to be 3.5xlO2/cm2.
In the conventional method, since the selectivity of etching depends on the difference in impurity concentration and the depth direction profile, the temperature of the heat treatment (bonding, epitaxial growth, oxidation or the like) which expands the 2 1 8~269 concentration distribution is largely limited to approximately no higher than 800C. On the other hand, in the etching of this method, since the difference in structure between porous and bulk determines the etching speed, the limitation of the heat treatment temperature is small. It has been reported that the heat treatment at about 1,180C is possible. For example, it is known that the heat treatment after bonding enhances the bonding strength between the wafers and reduces the number and size of voids generated at the bonded interface. Further, in the etching based on such a structural difference, the particles, even if adhered on porous silicon, do not affect the thickness uniformity.
On the other hand, in general, on a light transmittable substrate, typically glass, the deposited thin Si layer only becomes amorphous or polycrystalline at best, reflecting disorderliness in crystal structure of the substrate, so that the high-performance device can not be produced. This is due to the crystal structure of the substrate being amorphous, and thus an excellent single-crystal layer can not be achieved even by merely depositing the Si layer.
However, the semiconductor substrate obtained through bonding normally requires two wafers one of which is removed wastefully for the most part through polishing, etching or the like, so that the finite 218~269 resources of the earth are wasted.
Accordingly, in the conventional method, the bonded SOI has various problems about controllability, uniformity and economics.
A method is proposed in Japanese Patent Application No. 7-045441 for recycling the first substrate which is wasted in such a bonding method.
In this method, the following method is adopted, in the foregoing bonding and etch-back method using the porous Si, instead of the step for reducing in thickness the first substrate through grinding, etching or the like from the underside so as to expose the porous Si. This will be explained using Figs. 7A to 7E.
After forming porous a surface layer 72 of an Si substrate 71 (Fig. 7A), a single-crystal Si layer 73 is formed thereon (Fig. 7B). Then, the single-crystal Si layer 73 along with the Si substrate 71 is bonded to a main surface of another Si substrate 74, working as a support substrate, via an insulating layer therebetween (Fig. 7C). Thereafter, the bonded wafers are separated at the porous layer 72 and the porous Si layer 72 exposed on the surface at the side of the Si substrate 74 is selectively removed so that the SOI substrate is formed. Separation of the bonded wafers is performed, for example, a method selected from the following methods that the tensile force or pressure is - 14 - 21 ~ 726 sufficiently applied to the bonded wafers perpendicularly relative to the in-plane and uniformly over the in-plane; that the wave energy such as the ultrasonic wave is applied; that the porous layer is exposed at the wafer end surfaces, the porous Si is etched to some extent, and what is like a razor blade is inserted thereinto; that the porous layer is exposed at the wafer end surfaces and a liquid such as water is impregnated into the porous Si, and the whole bonded wafers are heated or cooled so as to expand the liquid.
Alternatively, separation is performed by applying the force to the Si substrate 71 in parallel to the support substrate 74.
Each of these methods is based on the fact that, although the mechanical strength of the porous Si layer 72 differs depending on the porosity, it is considered to be much weaker than the bulk Si. For example, if the porosity is 50%, the mechanical strength can be considered to be half the bulk. Specifically, when a compressive, tensile or shear force is applied to the bonded wafers, the porous Si layer is first ruptured.
As the porosity is increased, the porous layer can be ruptured with a weaker force.
However, if the porosity of porous silicon is increased, it is possible that distortion is introduced due to the ratio of bulk silicon relative to the lattice constant being increased so as to increase 2 1 8726~

warpage of the wafer. As a result, the following problems may be raised, that is, the number of void bonding failure regions called void is increased upon bonding, the crystal defect density is increased and, in the worst case, cracks are introduced into the epitaxial layer, and slip lines are introduced on the periphery of the wafer due to influence of thermal distortion upon the epitaxial growth.
When applying the force in the vertical or horizontal direction relative to the surface of the wafer, since the semiconductor substrate is not a fully rigid body but an elastic body, the wafer may be subjected to elastic deformation depending on a supporting fashion of the wafer so that the force escapes and thus is not applied to the porous layer effectively. Similarly, when inserting what is like a razor blade from the wafer end surface, unless the razor blade is fully thin and fully high in rigidity, the yield may be lowered.
Further, if the bonding strength at the bonded interface is weaker as compared with the strength of the porous Si layer or if weak portions exist locally, the two wafers may be separated at the bonded interface so that the initial object can not be achieved.
Further, since, in any of the methods, the position where separation occurs in the porous layer is not fixed, if the ratio in etching speed between the 2 1 8~269 porous Si and the bulk Si is not sufficient, the epitaxial silicon layer is first etched more or less at a portion where the porous layer remains thin rather than at a portion where the porous layer remains thick.
Thus, the thickness uniformity of the SOI layer may be deteriorated. Particularly, when the final thickness of the SOI layer is reduced to about lOOnm, the thickness uniformity is deteriorated so that a problem may be raised when forming the element such as the fully depleted MOSFET whose threshold voltage is sensitive to the film thickness.
Japanese Patent Application No. 5-211128 (corresponding to United States Patent No. 5,374,564) discloses a method for producing the SOI. In this method, hydrogen ions are directly implanted into a single-crystal Si substrate, and then the single-crystal Si substrate and a support substrate are bonded together. Finally, the single-crystal Si substrate is separated at a layer where hydrogen ions are implanted, so as to form the SOI. In this method, since hydrogen ions are directly implanted into the single-crystal Si substrate which is then separated at the ion-implanted layer, the flatness property of the SOI layer is not good. Further, the thickness of the SOI layer is determined by the projection range, so that the degree of freedom of the thickness is low. Further, it is necessary to select an implanting condition satisfying - 17 - 218 7~6 9 both of the layer thickness and the separation, which creates a difficulty in the control. Further, in case of aiming at obtaining a thin layer the thickness of which can not be determined by the ion implantation, it is necessary to carry out a reducing process in thickness such as grinding and etching, which process is nonselective, so that there is a fear of deteriorating the thickness uniformity.
In view of the foregoing, the method has been demanded for producing, with high reproducibility, the SOI substrate which is high in quality and whose SOI
layer has the excellent flatness property, and simultaneously for achieving resources saving and reduction in cost through recycling of the wafer.
On the other hand, in general, on a light transmittable substrate, typically glass, the deposited thin Si layer only becomes amorphous or polycrystalline at best, reflecting disorderliness in crystal structure of the substrate, so that the high-performance device can not be produced. This is due to the crystal structure of the substrate being amorphous, and thus an excellent single-crystal layer can not be achieved even by merely depositing the Si layer.
The light transmittable substrate is important for constituting a contact sensor as being a light-receiving element or a projection-type liquid-crystal image display device. For achieving further 2 ~ 8:7~6q densification, further high resolution and further fineness of picture elements of the sensor or the display device, the high-performance drive element is required. As a result, it is necessary to produce the element on the light transmittable substrate using the single-crystal layer having the excellent crystalline property.
Further, when using the single-crystal layer, reduction in size and acceleration of a chip can be achieved by incorporating a peripheral circuit for driving the picture elements and an image processing circuit into the same substrate having the picture elements.
Specifically, in case of amorphous Si or polycrystalline Si, it is difficult, due to its defective crystal structure, to produce the drive element having the performance which is required or will be required in the future.
On the other hand, for producing the device of the compound semiconductor, the substrate of the compound semiconductor is essential. However, the compound semiconductor substrate is expensive and further is very difficult to be increased in area to a large extent.
Further, an attempt has been made to achieve the epitaxial growth of the compound semiconductor such as GaAs on the Si substrate. However, due to difference 21 8726~

in lattice constant or thermal expansion coefficient, the grown film is poor in crystalline property and thus is very difficult to be applied to the device.
Further, an attempt has been made to achieve the epitaxial growth of the compound semiconductor on porous Si for reducing misfit of lattice. However, due to low thermostability and aged deterioration of porous Si, the stability and the reliability are poor as the substrate during or after production of the device.
However, there is a problem that the compound semiconductor substrate is expensive and low in mechanical strength so that the large-area wafer is difficult to be produced.
In view of the foregoing, an attempt has been made to achieve the heteroepitaxial growth of the compound semiconductor on the Si wafer which is inexpensive and high in mechanical strength so that the large-area wafer can be produced.
Further, recently, attention has been given to porous silicon als~ as a luminescent material for photoluminescence, electroluminescence or the like, and many research reports have been made therefor. In general, the structure of porous silicon largely differs depending on the type (p, n) and the concentration of impurities contained in silicon. When the p-type impurities are doped, the structure of porous silicon is roughly divided into two kinds 21 ~7269 depending on whether the impurity concentration is no less than 1013/cm3 or no more than 10l7/cm3. In the former case, the pore walls are relatively thick, that is, from several nanometers to several tens of nanometers, the pore density is about 1011/cm2 and the porosity is relatively low. However, it is difficult for this porous silicon to serve for luminescence. On the other hand, in the latter case, as compared with the former case, porous silicon whose pore wall is no more than several nanometers in thickness, whose pore density is greater by one figure and whose porosity exceeds 50%, can be easily formed. Most of luminous phenomena, such as photoluminescence, are mainly based on the formation of porous silicon using the latter as a starting material. However, the mechanical strength is low corresponding to the largeness of porosity.
Further, since a lattice constant deviation relative to bulk Si is as much as 10-3 (about 10-4 in the former case), there has been a problem that, when epitaxial-growing the single-crystal silicon layer on such porous silicon, defects are largely introduced into the epitaxial Si layer and cracks are further introduced thereinto. On the other hand, for utilizing the fine porous structure, which is suitable for a luminescent material, as a luminescent element, it has been desired that the epitaxial Si layer be formed on porous silicon for providing a contact or the MOSFET or the like as a - 21 - 2 1 8 726~

peripheral circuit be formed on the epitaxial silicon layer.

SUMMARY OF THE INVENTION
The present invention has an object to provide a semiconductor substrate and a forming method thereof which can solve the foregoing various problems by superposing a finer porous structure in a porous layer.
As a result of assiduous efforts made by the present inventors, the following invention has been achieved.
Specifically, a semiconductor substrate of the present invention is characterized by having a porous Si layer at a surface layer of an Si substrate, and a porous Si layer with large porosity existing in a region of the above-mentioned porous Si layer, which region is at a specific depth from the surface of the above-mentioned porous Si layer. In the semiconductor substrate, a non-porous Si portion may exist on the surface of the porous Si layer and an electrode may be formed on respective surfaces of the Si substrate and the non-porous Si layer, so that the semiconductor substrate constitutes a luminescent element.
According to a semiconductor substrate of the present invention, for example, a structure can be easily achieved, wherein a porous layer having a fine structure to work as a luminescent material is sandwiched in a porous layer having a high mechanical strength, such as porous silicon formed on a p~-Si substrate. Although the porous layer having such a fine structure differs from bulk Si in lattice constant, by sandwiching it in the large porous Si layer having intermediate lattice constant, stresses can be relaxed and introduction of cracks or defects can be suppressed. Specifically, since the luminescent layer which is stable in structure can be formed, it is not only possible to serve for formation of peripheral circuit or wiring, but also possible to provide a material which is excellent in long-term stability.
Further, according to a semiconductor substrate of the present invention, an extremely thin porous layer corresponding to a projection range of ion implantation can be formed. Since the pore size of such a porous layer can be set small, that is, no greater than several tens of nanometers, even the small foreign matter contained in gas and exceeding several tens of nanometers in diameter can be removed. Further, a thickness of such a porous layer can be set small, that is, no greater than 20~m, the conductance of the gas can be ensured. Specifically, when using it as a filter for particles in the gas, it is possible to produce a filter which can remove the particles greater than several tens of nanometers in diameter and whose pressure loss is small. Further, if high purity Si 21 8726~
which is used in the semiconductor process is used as a substrate, there is no worry about contamination from the filter itself.
The present invention includes a producing method of a semiconductor substrate.
Specifically, a producing method of a semiconductor substrate of the present invention comprises a porous-forming step for forming an Si substrate porous and forming a porous Si layer on at least a surface of the Si substrate, and a high-porosity layer forming step for forming a porous Si layer with large porosity in the region at the specific depth from the porous layer in the porous Si layer.
The high-porosity layer forming step can be carried out as an ion implanting step for implanting ions into the porous Si layer with a given projection range. It is preferable that the ions comprises at least one kind of noble gas, hydrogen and nitrogen. It is preferable that a non-porous layer forming step is provided for forming a non-porous layer on a surface of the porous Si layer before the ion implanting step. It is preferable that a bonding step is provided for bonding a support substrate on a surface of the non-porous layer after the high-porosity layer forming step and that a separating step is provided for separating the Si substrate into two at the porous Si layer with the large porosity after the bonding step. It is _ - 24 -2i 8726~
preferable that the separating step is performed by heat-treating the Si substrate, by pressurizing the Si substrate in a direction perpendicular to a surface thereof, by drawing the Si substrate in a direction perpendicular to a surface thereof or by applying a shearing force to the Si substrate.
It is preferable that the non-porous layer is made of single-crystal Si, single-crystal Si having an oxidized Si layer on a surface to be bonded or a single-crystal compound semiconductor. It is preferable that the support substrate is an Si substrate, an Si substrate having an oxidized Si layer on a surface to be bonded or a light transmittable substrate. It is preferable that the bonding step is performed by anode bonding, pressurization, heat treatment or a combination thereof. It is preferable that a porous Si removing step is provided, after the separating step, for removing the porous Si layer exposed on a surface of the support substrate and exposing the non-porous layer. It is preferable that the porous Si removing step is performed by an electroless wet etching using at least one of hydrofluoric acid, a mixed liquid obtained by adding at least one of alcohol and hydrogen peroxide water to hydrofluoric acid, buffered hydrofluoric acid, and a mixed liquid obtained by adding at least one of alcohol and hydrogen peroxide water to buffered hydrofluoric 2 1 8~69 acid. It is preferable that a flattening step is provided for flattening a surface of the non-porous layer after the porous Si removing step. It is preferable that the flattening step is performed by heat treatment in the atmosphere including hydrogen.
It may be arranged that the porous-forming step forms porous Si layers on both sides of the Si substrate, and that the bonding step bonds two support substrates to the porous Si layers formed on both sides of the Si substrate. It may be arrange that a second non-porous layer forming step is provided, after the separating step, for forming a non-porous layer again on the surface of the porous Si layer exposed on the surface of the Si substrate, and that a second ion implanting step is provided, after the porous layer forming step, for implanting ions into the porous Si layer with a given projection range and forming a porous Si layer with large porosity in the porous Si layer. It is preferable that the porous-forming step is performed by anodization. It is preferable that the anodization is performed in an HF solution.
The high-porosity layer forming step can be carried out by also altering the current density, during the porous-forming step.
After removing the remaining porous layer, the Si substrate separated by the foregoing method may be reused as an Si substrate by performing the surface flattening process if the surface flatness property is insufficient. The surface flattening process may be polishing, etching or the like normally used in the semiconductor process. On the other hand, the heat treatment in the atmosphere including hydrogen may also be used. By selecting the condition, this heat treatment can achieve the flatness to an extent where the atomic step is locally presented.
According to the producing method of the semiconductor substrate of the present invention, upon removal of the Si substrate, the Si substrate can be separated at one time in large area via the porous layer. Thus, the process can be shortened. Further, since the separating position is limited to within the porous layer with large porosity due to the ion implantation, thicknesses of the porous layer remaining on the support substrate side can be uniform so that the porous layer can be removed with excellent selectivity.
According to the producing method of the semiconductor substrate of the present invention, the Si substrate can be separated in advance at one time in large area via the porous layer. Thus, the grinding, polishing or etching process which was essential in the prior art for removing the Si substrate to expose the porous silicon layer can be omitted to shorten the process. Further, since the separating position is limited to within the porous layer with large porosity by implanting ions of at least one kind of noble gas, hydrogen and nitrogen into the porous layer so as to have the projection range, thicknesses of the porous layer remaining on the support substrate side can be uniform so that the porous layer can be removed with excellent selectivity. It is hard to happen that the thickness of the remaining porous layer is thin locally, so that the non-porous layer appears on the surface earlier and is etched accordingly. In the case, the forming method of the porous layer having a high porosity is not restricted to the ion implantation, but the formation can be realized by also altering the electric current at the anodization.
Specifically, not only the grinding or etching process which was essential in the prior art for exposing porous silicon can be omitted, but also the removed Si substrate can be reused as an Si substrate by removing the remaining porous layer. If the surface flatness property after the removal of porous silicon is insufficient, the surface flattening process is performed. Since the position where the bonded two substrates are separated is regulated by the projection range, the dispersion of the separating positions within porous silicon does not occur as opposed to the prior art. Thus, upon removal of porous silicon, the single-crystal silicon layer is prevented from being ~ - 28 -21 ~7269 exposed and etched to deteriorate the thickness uniformity. Further, the Si substrate can be reused in the desired number of times until its structural strength makes it impossible. Further, since the separating position is restricted to around the depth corresponding to the projection range of the ion implantation, the thickness of the porous layer can be set smaller as compared with the prior art. Further, it is capable of making the layer having a high porosity a layer having a specific depth constant from the surface of the porous layer to separate it, so that such a quality as the crystalizability of the porous layer is not deteriorated.
Alternatively, without removing the remaining porous layer, the separated Si substrate can be reused again as an Si substrate of the present invention by forming a non-porous single-crystal Si layer. Also in this case, the Si substrate can be reused in the desired number of times until its structural strength makes it impossible.
In the conventional method of producing the bonded substrates, the Si substrate is gradually removed from one side thereof through grinding or etching. Thus, it is impossible to effectively use both sides of the Si substrate for bonding to the support substrate. On the other hand, according to the present invention, the Si substrate is held in the initial state other than its surface layers so that, by using both sides of the Si substrate as the main surfaces and bonding the support substrates to the sides of the Si substrate, respectively, two bonded substrates can be simultaneously produced from one Si substrate. Thus, the process can be shortened and the productivity can be improved. As appreciated, also in this case, the separated Si substrate can be recycled as an Si substrate after removing the remaining porous Si.
Specifically, the present invention uses a single-crystal Si substrate which is excellent in economics, flat and uniform over a large area and has an extremely excellent crystalline property, and removes from one side thereof to an Si or compound semiconductor active layer formed on the surface which thus remains, so as to provide a single-crystal Si layer or a compound semiconductor single-crystal layer with extremely less defects on an insulating material.
The present invention provides a producing method of a semiconductor substrate which is capable of achieving an Si or compound semiconductor single-crystal layer with a crystalline property as good as a single-crystal wafer on a transparent substrate (light transmittable substrate), with high productivity, high uniformity, excellent controllability and reduced cost.
Further, the present invention provides a producing method of a semiconductor substrate which is replaceable for an expensive SOS or SIMOX upon producing a large scale integrated circuit of an SOI
structure.
According to the present invention, the single-crystal compound semiconductor layer with excellent crystalline property can be formed on porous Si, and further, this semiconductor layer can be transferred onto the large-area insulating substrate which is excellent in economics. Thus, the foregoing problem of the difference in lattice constant and thermal expansion coefficient can be sufficiently suppressed so as to form the compound semiconductor layer with excellent crystalline property on the insulating substrate.
Further, since porous Si has a low mechanical strength and an extensive surface area, removal of the porous Si layer of the present invention can also be performed by selective polishing using the single-crystal layer as a polishing stopper.
According to the producing method of the semiconductor substrate, since the porous layer of a fine structure can be formed after formation of the single-crystal silicon layer on the porous layer, the epitaxial growth condition of the single-crystal layer can be set free of influence of the structural change of the porous layer. Specifically, since the fine-structure porous layer, working as a luminescent layer, _ - 31 - 2187269 which tends to change due to thermal treatment, can be formed after completion of thermal treatment for the film formation, the characteristic of the element can be stable.
According to the producing method of the semiconductor substrate, upon removal of the Si substrate, the Si substrate can be separated at one time in large area via the porous layer, the process can be shortened. Further, since the separating position is limited to within the porous layer by means of the ion implantation, thicknesses of the porous layer remaining on the support substrate side can be uniform so that the porous layer can be removed with high selectivity. Thus, even when the etching is unstable due to the size of the apparatus or the change of the environment, the non-porous thin film, such as the single-crystal Si layer or the compound semiconductor single-crystal layer, which is excellent in economics, flat and uniform over the large area and has the extremely excellent crystalline property, can be transferred onto the support substrate with high yield. Specifically, the SOI structure with the single-crystal Si layer formed on the insulating layer can be obtained with high uniformity of film thickness and high yield. Further, since the separating position is regulated by the projection range of the ion implantation so as to be within the porous layer, the _ 32 - 2l~ 726 q thicknesses of the porous layer remaining on the support substrate side can be uniform so that the porous layer can be removed with high selectivity.
Further, the removed Si substrate can be reused as an Si substrate by removing the remaining porous layer.
If the surface flatness property after removal of porous silicon is insufficient, the surface flattening process is performed.
The present invention provides a producing method of a semiconductor substrate which is capable of achieving an Si or compound semiconductor single-crystal layer with a crystalline property as good as a single-crystal wafer on a transparent substrate (light transmittable substrate), with high productivity, high uniformity, excellent controllability and reduced cost.
According to the producing method of the semiconductor substrate of the present invention, since the selective etching which is excellent in a ratio of etching selectively can be performed, by performing the bonding with the support substrate, the SOI substrate or the compound semiconductor single crystal on the support substrate, which is flat and uniform over the large area and has an extremely excellent crystalline property, can be achieved.
Further, according to the producing method of the semiconductor substrate, the single-crystal compound semiconductor layer with high crystalline property can - 33 ~ 21~7269 be formed on porous Si, and further, this semiconductor layer can be transferred onto the large-area insulating substrate which is excellent in economics. Thus, the foregoing problem of the difference in lattice constant and thermal expansion coefficient can be sufficiently suppressed so as to form the compound semiconductor layer with excellent crystalline property on the insulating substrate.
Further, even if non-formation regions of the implanted layer are formed due to presence of the foreign matter on the surface upon the ion implantation, since the mechanical strength of the porous layer itself is smaller than bulk Si, the separation occurs in the porous layer. Thus, the bonded two substrates can be separated without causing damages such as cracks in the non-porous single-crystal silicon layer.
Further, since the gettering effect is available at the ion-implanted region, even if metal impurities exist, the bonded two substrates are separated after achieving the gettering of the impurities into the ion-implanted region, and then the ion-implanted region is removed so that it is also effective against the impurity contamination.
Further, since the separating region is limited to the ion-implanted region within the porous layer, the depths of the separating region do not disperse within _ - 34 -21 8726q the porous layer. Accordingly, even if the ratio of etching selectively porous silicon is insufficient, a time for removing porous silicon can be rendered substantially constant so that the thickness uniformity of the single-crystal silicon layer transferred onto the support substrate is not spoiled.

BRIEF DESCRIPTION OF THE DRAWINGS
Figs. lA and lB are schematic diagrams for explaining a semiconductor substrate producing process according to a first preferred embodiment of the present invention;
Figs. 2A to 2C are schematic diagrams for explaining a semiconductor substrate producing process according to a second preferred embodiment of the present invention;
Figs. 3A to 3C are schematic diagrams for explaining a semiconductor substrate producing process according to a third preferred embodiment of the present invention;
Figs. 4A to 4F are schematic diagrams for explaining a semiconductor substrate producing process according to a fourth preferred embodiment of the present invention;
Figs. 5A to 5F are schematic diagrams for explaining a semiconductor substrate producing process according to a fifth preferred embodiment of the 2 1 87~69 present invention;
Figs. 6A to 6E are schematic diagrams for explaining a semiconductor substrate producing process which has been proposed before;
Figs. 7A to 7E are schematic diagrams for explaining a conventional semiconductor substrate producing process;
Figs. 8A to 8E are schematic diagrams for explaining a semiconductor substrate producing process according to a sixth preferred embodiment of the present invention;
Figs. 9A to 9G are schematic diagrams for explaining a semiconductor substrate producing process according to a seventh preferred embodiment of the present invention;
Figs. lOA to lOG are schematic diagrams for explaining a semiconductor substrate producing process according to an eighth preferred embodiment of the present invention;
Figs. llA and llB are schematic diagrams for explaining anodization; and Figs. 12A to 12D are sectional views showing a process of a EL element.

DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENTS
The present invention simultaneously solves the foregoing various problems by superposing a finer ~ - 36 - 218726~

porous structure in the foregoing porous layer.
It has been reported that, by performing ion implantation of helium or hydrogen into bulk silicon and applying heat thereto, micro-cavities having diameters in the range from several nanometers to several tons of nanometers are formed at the implanted region in the density of as much as 1016 to 1017/cm3 (for example, A. Van Veen, C.C. Griffioen, and J. H. Evans, Mat. Res. Soc. Symp. Proc. 107 (1988, Material Res.
Soc. Pittsburgh, Pennsylvania) p. 449). Recently, it has been researched to utilize these micro-cavity groups as gettering sites of metal impurities.
V. Raineri and S.U. Campisano implanted helium ions into bulk silicon and applied a heat treatment thereto so as to form the cavity groups, then exposed the sides of the cavity groups by forming grooves in the substrate and applied an oxidation treatment thereto. As a result, the cavity groups were selectively oxidized so as to form a buried silicon oxide layer. That is, they reported that the SOI
structure could be formed (V. Raineri and S.U.
Campisano, Appl. Phys. Lett. 66 (1995) p. 3654).
However, in their method, thicknesses of the surface silicon layer and the buried silicon oxide layer were so limited as to achieve both formation of the cavity groups and relaxation of stresses introduced due to volume expansion upon oxidation and further the 2 1 8726q formation of the grooves were necessary for selective oxidation so that the SOI structure could not be formed all over the substrate. Such formation of the cavity groups have been reported as a phenomenon following the implantation of light elements into metal along with an expansion or separation phenomenon of the cavity groups as a part of the research about a first reactor wall of the nuclear fusion reactor.
Porous Si was found in the course of the research of electropolishing of the semiconductor in 1956 by Uhlir and collaborator (A. Uhlir, Bell Syst. Tech. J., vol. 35, 333 (1956)). Porous silicon can be formed by anodizing the Si substrate in the HF solution. Unagami and collaborator researched the dissolution reaction of Si in the anodization and reported that positive holes were necessary for the anodizing reaction of Si in the HF solution and the reaction was as follows (T.
Unagami, J. Electrochem. Soc., vol. 127, 476 (1980)):
Si + 2HF + (2-n) e+ ~ SiF2 + 2H+ + ne~
SiF2 + 2HF ~ SiF4 + H2 SiF4 + 2HF ~ H2SiF6 or Si + 4HF + (4-~) e+ ~ SiF4 + 4H+ + ~e~
SiF4 + 2HF ~ H2SiF6 wherein e+ and e~ represent a hole and an electron, respectively, and n and ~ represent the numbers of holes necessary for dissolution of one Si element, ~ - 38 ~ 218726~

respectively. It was reported that porous Si was formed when n>2 or ~>4 was satisfied.
As appreciated from the foregoing, p-type Si having the holes is rendered porous while n-type Si is not rendered porous. The selectivity while getting porous has been proved by Nagano and collaborators and Imai (Nagano, Nakajima, Yasuno, Oonaka, Kajiwara, Engineering Research Report of Institute of Electronics and Communication Engineers of Japan, vol. 79, SSD79-9549 (1979)), (K. Imai, Solid-State Electronics, vol.
24, 159 (1981)).
However, there have also been reports that high-concentration n-type Si can be rendered porous (R.P.
Holmstrom and J.Y. Chi, Appl. Phys. Lett., vol. 42, 386 (1983)) so that it is important to choose the substrate which can be rendered porous, irrespective of p- or n-type.
Porous silicon can be formed by anodizing the Si substrate in the HF solution. The porous layer has a structure like sponge including holes of about 10~1 to lOnm in diameter arranged at intervals of about 10~1 to lOnm. The density thereof can be changed in the range of 1.1 to 0.6g/cm3 by changing the HF solution concentration in the range of 50 to 20% and by changing the current density, as compared with the density 2.33g/cm3 of the single-crystal Si. That is, the porosity can be changed. Although the density of ~ 39 ~ 2 1 8 7269 porous Si is no more than half as compared with the single-crystal Si as described above, the monocrystalline property is maintained so that the single-crystal Si layer can be epitaxial-grown at the upper part of the porous layer. However, at the temperature no less than 1,000C, rearrangement of the internal holes occurs to spoil the accelerating etching characteristic. In view of this, it has been said that the low temperature growth, such as the molecular beam epitaxial growth, the plasma CVD, the vacuum CVD, the optical CVD, the bias sputtering or the liquid deposition, is suitable for the epitaxial growth of the Si layer. On the other hand, if a protective film is formed in advance on the pore walls of the porous layer by means of the method of low temperature oxidation or the like, the high temperature growth is also possible.
Further, the porous layer is reduced in density to no more than half due to the formation of a lot of the internal cavities therein. As a result, since the surface area is greatly increased as compared with the volume, the chemical etching speed thereof is extremely increased as compared with the etching speed of the normal single-crystal layer.
Although the mechanical strength of porous Si differs depending on porosity, it is considered to be smaller than that of bulk Si. For example, if porosity is 50%, the mechanical strength can be considered to be half the bulk. Specifically, when a compressive, tensile or shear force is applied to the bonded wafers, the porous Si layer is first ruptured. As the porosity is increased, the porous layer can be ruptured with a weaker force.
The present invention simultaneously solves the foregoing various problems by superposing a finer porous structure in the foregoing porous layer.
It has been found that, when ion implantation of at least one kind of noble gas, hydrogen and nitrogen is performed into the porous layer with a projection range ensured, the porosity of the implanted region is increased. When observing in detail the implanted layer using an electron microscope, a lot of micro-cavities were formed in the pore walls of the porous layer formed in advance. Specifically, the fine porous structure was formed. Upon irradiation of ultraviolet light, the luminous phenomenon at the wavelength around 700nm was confirmed.
If choosing further implantation conditions, porous silicon can be separated at a depth corresponding to the projection range of the ion implantation.
The separation can be improved in uniformity or achieved with less implantation amount by forming in advance a thin film on the pore walls of porous silicon using the method of particularly low temperature oxidation. The separation can be facilitated by applying the heat treatment after the ion implantation.
By ion-implanting at least one kind of noble gas, hydrogen and nitrogen into the porous layer with a projection range ensured after formation of at least one layer of non-porous film, such as a non-porous single-crystal silicon layer, on porous silicon or without such formation, the porosity of the implanted is increased. If such an Si substrate is bonded to the support substrate and then the bonded substrates are subjected to the mechanical force or the heat treatment, or even without such processes, the bonded two substrates can be separated into two at a portion of the porous silicon layer where ions are implanted.
By supporting both sides of the ion-implanted layer with a fully thick elastic or rigid body, the separation can be achieved uniformly over the large area. Further, it is possible to facilitate the separation of the substrates by applying the heat treatment, the force or the ultrasonic wave to the substrates.
Even if non-formation regions of the implanted layer are formed due to presence of the foreign matter on the surface upon the ion implantation, since the mechanical strength of the porous layer itself is smaller than bulk Si, the separation occurs in the porous layer. Thus, the bonded two substrates can be _ - 42 - 2187269 separated without causing the cracks or the line in the non-porous single-crystal Si layer. In other words, the phenomenon of the separation can be selected by selecting a timing for the manifestation from the time of implantation and the time of heat treatment; and a condition of implantation such as an amount of implanted beam and energy thereof. Further, the layer having a large porosity may be formed at a region of a constant depth from the surface of the porous layer by controlling the condition at the anodization.
Further, by selectively removing the porous Si layer re~; n; ng on the surface of the separated substrate using the method of etching, polishing or the like, the single-crystal Si layer is exposed on the support substrate. On the other hand, after removing the remaining porous Si, the Si substrate can be again formed with porous silicon, then formed with a single-crystal Si layer and subjected to the ion implantation of at least one kind of noble gas, hydrogen and nitrogen into the porous layer with the projection range ensured, and then bonded to a support substrate.
That is, the Si substrate can be recycled. Further, if the Si substrate, with the porous silicon layer remaining, is subjected to the heat treatment in the reduction atmosphere including hydrogen or the like, the porous silicon surface is rendered flat and smooth so that the single-crystal silicon layer can be formed ~ 3 ~ 21 87269 successively. By bonding the single-crystal silicon layer to the support substrate, the Si substrate can also be recycled.
According to this method, since the portion to be separated is limited to the ion-implanted region in the porous layer, the depth of the separated region is not dispersed in the porous layer. Thus, even if the ratio of etching selectively porous silicon is insufficient, porous silicon can be removed for substantially a constant time so that the uniformity of thickness of the single-crystal silicon layer provided on the support substrate is not spoiled.
In the conventional method of producing the bonded substrates, the Si substrate is gradually removed from one side thereof through grinding or etching. Thus, it is impossible to effectively use both sides of the Si substrate for bon~;ng to the support substrate. On the other hand, according to the present invention, the Si substrate is held in the initial state other than its surface layers so that, by using both sides of the Si substrate as the main surfaces and bonding the support substrates to the sides of the Si substrate, respectively, two bonded substrates can be simultaneously produced from one Si substrate. As appreciated, also in this case, the Si substrate can be recycled as an Si substrate after removing the remaining porous Si.

_ ~ 44 ~ 2 1 8 72 69 The support substrate may be, for example, a light transmittable substrate, such as an Si substrate, an Si substrate with a silicon oxide film formed thereon, a silica glass substrate or a glass substrate, or a metal substrate, but not particularly limited thereto.
The thin film formed on the porous Si layer on the Si substrate may be, for example, a non-porous single-crystal Si film, a compound semiconductor film of such as GaAs or InP, a metal film or a carbon film, but not particularly limited thereto. Further, the thin film is not necessarily formed all over the porous Si layer, but may be partially etched by the patterning process.
[First Embodiment]
As shown in Fig. lA, an Si single-crystal substrate 11 is first prepared and then rendered porous at its surface layer. Numeral 12 denotes the obtained porous layer. As shown in Fig. lB, at least one kind of noble gas, hydrogen and nitrogen is ion-implanted into the porous layer 12. Then, a porous layer 13 having large porosity is formed in the porous layer 12.
The charge condition of the implanted ions is not particularly limited. The acceleration energy is set such that the projection range corresponds to a depth at which the ion implantation is desired. Depending on the implantation amount, the size and the density of the micro-cavities to be formed are changed, but approximately no less than lxlO13/cm2 and more _ 45 - 2 1 8 72 6 9 preferably lxl014/cm2. When setting the projection range to be deeper, the channeling ion implantation may be employed. After the implantation, the heat treatment is performed according to necessity. In case of the heat treatment atmosphere being the oxidizing atmosphere, the pore walls are oxidized so that attention should be given to prevent the Si region from being all changed into silicon oxide due to overmuch oxidation.
When the light of a mercury lamp, a xenon lamp or the like is applied to the thus produced sample as the light of shorter wavelength, the sample emits the red light around 780nm. That is, the photoluminescence is confirmed. Or an EL (Electroluminescence) element can be formed.
In Fig. lB, the semiconductor substrate of the present invention is shown. The layer 13 is the porous Si layer with the large porosity obtained as the result of the foregoing ion implantation. The fine porous structure showing the luminous phenomenon is formed uniformly in large area all over the wafer. Further, the metallic luster is held on the surface, that is, not showing the stain manner as in the prior art, so that metallic wiring can be easily arranged.
[Second Embodiment]
As shown in Fig. 2A, an Si single-crystal substrate 21 is first prepared and then rendered porous - 46 - 2 1 8 72 6 ~

at its surface layer. Numeral 22 denotes the obtained porous layer. As shown in Fig. 2B, at least one kind of noble gas, hydrogen and nitrogen is ion-implanted into the porous layer 22. Then, a porous layer (ion-implanted layer) 23 having large porosity is formed inthe porous layer 22. The charge condition of the implanted ions is not particularly limited. The acceleration energy is set such that the projection range corresponds to a depth at which the ion implantation is desired. Depending on the implantation amount, the size and the density of the micro-cavities to be formed are changed, but approximately no less than lxlO14/cm2 and more preferably lxlO15/cm2. When setting the projection range to be deeper, the channeling ion implantation may be employed. After the implantation, the heat treatment is performed or at least one of compressive, tensile and shear stresses is applied to the wafer in a direction perpendicular to the surface according to necessity, so as to divide the semiconductor substrate into two at the ion-implanted layer as a border. In case of the heat treatment atmosphere being the oxidizing atmosphere, the pore walls are oxidized so that attention should be given to prevent the Si region from being all changed into silicon oxide due to overmuch oxidation.
In ~ig. 2C, the extremely thin porous substrate obtained by the present invention is shown. Since the division of the substrate starts spontaneously upon the heat treatment or the like as a trigger due to the internal stress introduced upon the implantation, the extremely thin porous structure can be formed uniformly all over the substrate. The pores of the porous structure are formed from one main surface of the substrate toward the other main surface. Accordingly, when the gas is implanted under pressure from the one main surface, it is ejected out from the other main surface. In this case, since the pore size of the porous structure is in the range from several nanometers to several tens of nanometers, the particle greater than this can not pass therethrough. On the other hand, although the pressure loss is caused depending on the pore size, the pore density and a thickness of the extremely thin porous substrate, the strength of the substrate and the pressure loss can be both within the practical range if the thickness of the porous layer is approximately no more than 20,um.
[Third Embodiment]
As shown in Fig. 3A, an Si single-crystal substrate 31 is first prepared and then rendered porous at its surface layer. Numeral 32 denotes the obtained porous layer. Subsequently, as shown in Fig. 3B, at least one layer 33 is formed on the porous layer. The film to be formed is arbitrarily selected from among a single-crystal Si film, a polycrystalline Si film, an 2 1 ~7269 amorphous Si film, a metal film, a compound semiconductor film, a superconductive film and the like.
As shown in Fig. 3C, at least one kind of noble gas, hydrogen and nitrogen is ion-implanted into the porous layer 32. Then, a porous layer 34 having large porosity is formed in the porous layer 32. The charge condition of the implanted ions is not particularly limited. The acceleration energy is set such that the projection range corresponds to a depth at which the ion implantation is desired. Depending on the implantation amount, the size and the density of the micro-cavities to be formed are changed, but approximately no less than lxlO14/cm2 and more preferably lxlO15/cm2. When setting the projection range to be deeper, the channeling ion implantation may be employed. After the implantation, the heat treatment is performed according to necessity. In case of the heat treatment atmosphere being the oxidizing atmosphere, the pore walls are oxidized so that attention should be given to prevent the Si region from being all changed into silicon oxide due to overmuch oxidation.
When the light of a mercury lamp, a xenon lamp or the like is applied to the thus produced sample as the light of shorter wavelength, the sample emits the red light around 780nm. That is, the photoluminescence is confirmed. Or an EL element can be formed.
The EL element is realized by forming a construction where a voltage is applied to a porous layer having a large porosity formed in the porous layer by means of ion implantation and so forth. ~or example, when turning p+ substrate 121 porous, the EL
element is realized by implanting phospho-ion and so forth in porous layer 122 including porous layer 123 having a large porosity from the surface in a manner of making the ion reach a region of a constant depth from the surface, or by diffusing the ion by means of heat diffusion etc., to form a p-n junction in porous layer 123 having a large porosity or in neighborhood thereof.
A portion 127 is an n-region of the porous layer having a large porosity, which region is obtained as a result of the above-mentioned process.
Electrodes 125 and 126 are secured with the substrate and the surface of the porous portion. The electrodes may be formed in the side of the surface of the porous portion by a process comprised of forming epitaxial Si layer 124 on the porous portion prior to the formation of the electrode and then forming the electrode thereon (see Fig. 12C). Further, as shown in Fig. 12D, the epitaxial Si layer may be removed partly as the occasion demands so as to facilitate the penetration of the light of the EL.
In Fig. 3B, the semiconductor substrate of the _ - 50 ~ ~l 87 2 69 present invention is shown. The fine porous structure showing the luminous phenomenon is formed uniformly in large area all over the wafer. Further, the metallic luster is held on the surface, that is, not showing the cracks or the like as in the prior art, so that metallic wiring can be easily arranged.
[Fourth Embodiment]
As shown in Fig. 4A, an Si single-crystal substrate 41 is first prepared and then rendered porous at its surface layer. Numeral 42 denotes the obtained porous layer. Subsequently, as shown in Fig. 4B, at least one non-porous thin film 43 is formed on the porous layer. The film to be formed is arbitrarily selected from among a single-crystal Si film, a polycrystalline Si film, an amorphous Si film, a metal film, a compound semiconductor film, a superconductive film and the like. Or an element structure such as a MOSFET may be formed.
As shown in Fig. 4C, at least one kind of noble gas, hydrogen and nitrogen is ion-implanted into the porous layer 42 so as to form an implanted layer 44.
When observing the implanted layer by a transmission electron microscope, formation of numberless micro-cavities can be seen. The charge condition of the implanted ions is not particularly limited. The acceleration energy is set such that the projection range corresponds to a depth at which the ion -implantation is desired. Depending on the implantation amount, the size and the density of the micro-cavities to be formed are changed, but approximately no less than lxl014/cm2 and more preferably lxl015/cm2. When setting the projection range to be deeper, the channeling ion implantation may be employed. After the implantation, the heat treatment is performed according to necessity. In case of the heat treatment atmosphere being the oxidizing atmosphere, the pore walls are oxidized so that attention should be given to prevent the Si region from being all changed into silicon oxide due to overmuch oxidation.
As shown in Fig. 4D, after abutting a support substrate 45 and the surface of the first substrate with each other at room temperature, they are bonded to each other through anodic bonding, pressurization, heat treatment or a combination thereof. As a result, both substrates are firmly coupled with each other.
When single-crystal Si is deposited, it is preferable to perform the bonding after oxidized Si is formed on the surface of single-crystal Si through thermal oxidation or the like. On the other hand, the support substrate can be selected from among an Si substrate, an Si substrate with a silicon oxide film formed thereon, a light transmittable substrate such as quartz, a sapphire substrate and the like, but not limited thereto as long as the surface serving for the bonding is fully flat. The bonding may be performed in three plies with an insulating thin plate interposed therebetween.
Subsequently, the substrates are divided at the ion-implanted layer 44 in the porous Si layer 42 (Fig.
4E). The structure of the second substrate side includes the porous Si layer 42, the non-porous thin film (for example, the single-crystal Si layer) 43 and the second substrate 45.
Further, the porous Si layer 42 is selectively removed. In case of the non-porous thin film being single-crystal Si, only the porous Si layer 42 is subjected to the electroless wet chemical etching using at least one of the normal Si etching liquid, hydrofluoric acid being the porous Si selective etching liquid, a mixed liquid obtained by adding at least one of alcohol and hydrogen peroxide water to hydrofluoric acid, buffered hydrofluoric acid, and a mixed liquid obtained by adding at least one of alcohol and hydrogen peroxide water to buffered hydrofluoric acid, so as to render the film formed in advance on the porous layer of the first substrate remain on the second substrate.
As described above in detail, only the porous Si layer can be selectively etched using the normal Si etching liquid due to the extensive surface area of porous Si.
Alternatively, the porous Si layer 42 may be removed through selective polishing using the single-crystal Si ` ~ 53 - 2 1 87269 layer 43 as a polishing stopper.
In case of the compound semiconductor layer formed on the porous layer, only the porous Si layer 42 is subjected to chemical etching using the etching liquid which has the greater etching speed for Si relative to the compound semiconductor, so as to render the thickness-reduced single-crystal compound semiconductor layer 43 remain on the insulating substrate 45.
Alternatively, the porous Si layer 42 is removed through selective polishing using the single-crystal compound semiconductor layer 43 as a polishing stopper.
In Fig. 4F, the semiconductor substrate of the present invention is shown. On the insulating substrate 45, the non-porous thin film, such as the single-crystal Si thin film 43, is formed in large area all over the wafer, flatly and uniformly reduced in thickness. The semiconductor substrate thus obtained can be suitably used also in view of production of the insulated electronic element.
The Si single-crystal substrate 41 can be reused as an Si single-crystal substrate 41 after removing remaining porous Si and after performing surface-flattening if the surface flat property is bad to an extent which is not admissible.
Alternatively, a non-porous thin film may be again formed without removing porous Si so as to provide the substrate as shown in Fig. 4B, which is then subjected to the processes shown in Figs. 4C to 4F.
[Fifth Embodiment]
As shown in Fig. 5A, an Si single-crystal substrate 51 is first prepared and then rendered porous at both surface layers thereof. Numerals 52 and 53 denote the obtained porous layers. Subsequently, as shown in Fig. 5B, at least one non-porous thin film 54, 55 is formed on each of the porous layers. The film to be formed is arbitrarily selected from among a single-crystal Si film, a polycrystalline Si film, anamorphous Si film, a metal film, a compound semiconductor film, a superconductive film and the like. Or an element structure such as a MOSFET may be formed.
As shown in Fig. 5C, at least one kind of noble gas, hydrogen and nitrogen is ion-implanted into the porous layers 52 and 53 so as to form implanted layers 56 and 57. When observing the implanted layers by a transmission electron microscope, formation of numberless micro-cavities can be seen, and accordingly the porosity enlarges. The charge condition of the implanted ions is not particularly limited. The acceleration energy is set such that the projection range corresponds to a depth at which the ion implantation is desired. Depending on the implantation amount, the size and the density of the micro-cavities to be formed are changed, but approximately no less _ ~ 55 ~ 2 1 87 2 69 than lxl014/cm2 and more preferably lxl015/cm2. When setting the projection range to be deeper, the channeling ion implantation may be employed. After the implantation, the heat treatment is performed according to necessity. In case of the heat treatment atmosphere being the oxidizing atmosphere, the pore walls are oxidized so that attention should be given to prevent the Si region from being all changed into silicon oxide due to overmuch oxidation.
As shown in Fig. 5D, after abutting two support substrates 58 and 59 and the surfaces of the non-porous thin films 54 and 55 of the first substrate with each other at room temperature, they are bonded to each other through anode bonding, pressurization, heat treatment or a combination thereof. As a result, the three substrates are firmly coupled with each other.
Alternatively, the bonding may be performed in five plies with insulating thin plates interposed therebetween.
When single-crystal Si is deposited, it is preferable to perform the bonding after oxidized Si is formed on the surface of single-crystal Si through thermal oxidation or the like. On the other hand, the support substrate can be selected from among an Si substrate, an Si substrate with a silicon oxide film formed thereon, a light transmittable substrate such as quartz, a sapphire substrate and the like, but not - 56 - 2 1 g 7 2 6 9 limited thereto as long as the surface serving for the bonding is fully flat.
The bonding may be performed in three plies with an insulating thin plate interposed therebetween.
Subsequently, the substrates are divided at the ion-implanted layers 56 and 57 in the porous Si layers 52 and 53 (Fig. 5E). The structure of each of the two support substrate sides includes the porous Si layer 52, 53, the non-porous thin film (for example, the single-crystal Si layer) 54, 55 and the support substrate 58, 59.
Further, the porous Si layer 52, 53 is selectively removed. In case of the non-porous thin film being single-crystal Si, only the porous Si layer 52, 53 is subjected to the electroless wet chemical etching using at least one of the normal Si etching liquid, hydrofluoric acid being the porous Si selective etching liquid, a mixed liquid obtained by adding at least one of alcohol and hydrogen peroxide water to hydrofluoric acid, buffered hydrofluoric acid, and a mixed liquid obtained by adding at least one of alcohol and hydrogen peroxide water to buffered hydrofluoric acid, so as to render the film formed in advance on the porous layer of the first substrate remain on the support substrate.
As described above in detail, only the porous Si layer can be selectively etched using the normal Si etching liquid due to the extensive surface area of porous Si.

~1 87269 Alternatively, the porous Si layer 52, 53 may be removed through selective polishing using the single-crystal Si layer 54, 55 as a polishing stopper.
In case of the compound semiconductor layer formed on the porous layer, only the porous Si layer 52, 53 is subjected to chemical etching using the etching liquid which has the greater etching speed for Si relative to the compound semiconductor, so as to render the thickness-reduced single-crystal compound semiconductor layer 54, 55 remain on the insulating substrate.
Alternatively, the porous Si layer 52, 53 is removed through selective polishing using the single-crystal compound semiconductor layer 54, 55 as a polishing stopper.
In Fig. 5F, the semiconductor substrates of the present invention are shown. On the support substrates, the non-porous thin films, such as the single-crystal Si thin films 54 and 55, are formed in large area all over the wafer, flatly and uniformly reduced in thickness, so that the two semiconductor substrates are simultaneously formed. The semiconductor substrates thus obtained can be suitably used also in view of production of the insulated electronic elements.
The first Si single-crystal substrate 51 can be reused as a first Si single-crystal substrate 51 after removing remaining porous Si and after performing -surface-flattening if the surface flat property is bad to an extent which is not admissible. Alternatively, a non-porous thin film may be again formed without removing porous Si so as to provide the substrate as shown in Fig. 5B, which is then subjected to the processes shown in Figs. 5C to 5F. The support substrates 58 and 59 are not necessarily identical with each other.
[Sixth Embodiment]
The sixth preferred embodiment will be described with reference to Figs. 8A to 8E.
First, a single-crystal Si substrate 100 is anodized to form a porous Si layer 101 (Fig. 8A). In this case, a thickness to be rendered porous is in the range from several micrometers to several tens of micrometers on one surface layer of the substrate. It may be arranged to anodize the whole Si substrate 100.
The method of forming porous silicon will be explained using Figs. llA and llB. First, as the substrate, a p-type single-crystal silicon substrate 600 is prepared. An n-type may also be used. However, in this case, it is necessary that the substrate is limited to a low-resistance substrate or that the light is applied onto the surface of the substrate so as to facilitate generation of the holes. The substrate 600 is set in an apparatus as shown in Fig. llA.
Specifically, one side of the substrate is in contact _ ~ 59 ~ 2187269 with a hydrofluoric acid solution 604 having therein a negative electrode 606, while the other side of the substrate is in contact with a positive metal electrode 605. On the other hand, as shown in Fig. llB, a positive electrode 605' may also be provided in a solution 604'. In any case, the substrate is first rendered porous from the negative electrode side abutting the hydrofluoric acid solution. As the hydrofluoric acid solution 604, concentrated hydrofluoric acid (49%HF) is used in general. As diluted by pure water (H20), although depending on current values, etching occurs from a certain concentration so that it is not preferable. During anodization, bubbles are generated from the surface of the substrate 600. Alcohol may be added as a surface active agent for effective removal of the bubbles. As alcohol, methanol, ethanole, propanol, isopropanol or the like is used. Instead of the surface active agent, an agitator may be used to agitate the solution so as to achieve anodization. The negative electrode 606 is made of a material, such as gold (Au) or platinum (Pt), which does not corrode relative to the hydrofluoric acid solution. A material of the positive electrode 605 may be metal which is used in general. On the other hand, since the hydrofluoric acid solution 604 reaches the positive electrode 605 when anodization is achieved relative to the whole substrate 600, it is ~ - 60 - 218726~

preferable to coat the surface of the positive electrode 605 with a metal film which is resistive to the hydrofluoric acid solution. The maximum current value for anodization is several hundreds of mA/cm2, while the minimum current value therefor is arbitrary other than zero. This current value is determined in the range where the good-quality epitaxial growth is achieved on the surface of porous silicon. In general, as the current value increases, the anodization speed increases and the density of the porous Si layer decreases. That is, the volume of the pores increases.
This changes the condition of the epitaxial growth.
On the porous layer 101 thus formed, a non-porous single-crystal silicon layer 102 is epitaxial-grown (Fig. 8B).
Subsequently, the surface of the epitaxial layer 102 is oxidized (including thermal oxidation) so as to form an SiO2 layer 103 (Fig. 8C). This is necessary because, if the epitaxial layer is directly bonded to the support substrate in the next process, impurities tend to segregate at the bonded interface and dangling bonds of atoms at the interface increase, which will be causes for rendering unstable the characteristic of the thin film device. However, this process is not essential, but may be omitted in case of a device structure wherein such phenomena are not serious. The SiO2 layer 103 works as an insulating layer of the SOI

- 61 - 2 1 8 7~ 69 substrate and should be formed on at least one side of the substrate to be bonded. There are various manners for formation of the insulating layer.
Upon oxidation, a thickness of the oxidized film is set to a value which is free of influence of contamination taken into the bonded interface from the atmosphere.
Thereafter, the foregoing ion implantation is performed so as to form a layer with large porosity in the porous Si layer 101.
The substrate 100 having the foregoing epitaxial surface with the oxidized surface and a support substrate 110 having an SiO2 layer 104 on the surface are prepared. The support substrate 110 may be a silicon substrate whose surface is oxidized (including thermal oxidation), quartz glass, crystallized glass, an arbitrary substrate with SiO2 deposited thereon, or the like. A silicon substrate without the SiO2 layer 104 may also be used as the support substrate.
The foregoing two substrates are bonded together after cleaning them (Fig. 8D). The cleaning is performed pursuant to the process of cleaning (for example, before oxidation) the normal semiconductor substrate.
By pressurizing the whole substrates after the bonding, the bonding strength can be enhanced.
Subsequently, the bonded substrates are subjected - 62 - 2~8726~

to the heat treatment. Although the higher temperature is preferable for the heat treatment, if it is too high, the porous layer 101 tends to cause the structural change or the impurities contained in the substrate tend to be diffused into the epitaxial layer.
Thus, it is necessary to select temperature and time which does not cause them. Specifically, about 600 to 1,100C is preferable. On the other hand, there is such a substrate that can not be subjected to the thermal treatment at the high temperature. For example, in case of the support substrate 110 being made of quartz glass, it can be subjected to the thermal treatment only at the temperature no greater than 200C due to difference in thermal expansion coefficient between silicon and quartz. If exceeding this temperature, the bonded substrates may be separated or ruptured due to stress. The thermal treatment is sufficient as long as it can endure the stress upon grinding or etching of the bulk silicon 100 performed in the next process.
Accordingly, even at the temperature no greater than 200C, the process can be performed by optimizing the surface processing condition for activation.
Then, by the foregoing method, the substrates are separated into two at the porous Si layer having the large porosity. The layer having the large porosity can be formed by altering current in the anodization, besides the ion implantation.

-- - 63 ~ 2 18 726 ~

Subsequently, the silicon substrate portion 100 and the porous portion 101 are selectively removed with the epitaxial layer 102 remaining (Fig. 8E). In this fashion, the SOI substrate is obtained.
The following processes may be added to the foregoing processes:
(1) A thickness of the wall between the adjacent holes in the oxidized (preoxidation) porous silicon layer of the pore internal walls of the porous layer is very small, that is, several nanometers to several tens of nanometers. Thus, if the high-temperature process is applied to the porous layer upon formation of the epitaxial silicon layer or upon heat treatment after bonding, the pore wall may agglomerate to be enlarged so that the pore wall may clog the pore to lower the etching speed. In view of this, after formation of the porous layer, a thin oxidized film is formed on the pore wall so as to suppress the enlargement of the pore wall. On the other hand, since it is necessary to epitaxial-grow the non-porous single-crystal silicon layer on the porous layer, it is necessary to oxidize only the surface of the pore inner wall such that the monocrystalline property remains inside the pore wall of the porous layer. It is preferable that the oxidized film to be formed is in the range of several angstroms to several tens of angstroms. The oxidized film of such a thickness is formed through the heat 2t87269 treatment in the oxygen atmosphere at the temperature of 200C to 700C, and more preferably 250C to 500C.
(2) Hydrogen Baking Process The present inventors have shown in the Publication No. EP553852A2 that, through the heat treatment in the hydrogen atmosphere, small roughness on the silicon surface can be removed to obtain the very smooth silicon surface. Also in the present invention, the baking in the hydrogen atmosphere can be applied. The hydrogen baking can be performed, for example, after formation of the porous silicon layer and before formation of the epitaxial silicon layer.
Apart from this, the hydrogen baking can be performed to the SOI substrate obtained after etching removal of the porous silicon layer. Through the hydrogen baking process performed before formation of the epitaxial silicon layer, a phenomenon that the pore surface is closed due to migration of silicon atoms forming the porous silicon surface. When the epitaxial silicon layer is formed in the state where the pore surface is closed, the epitaxial silicon layer with less crystal defects can be achieved. On the other hand, through the hydrogen baking process performed after etching of the porous silicon layer, the epitaxial silicon surface which was more or less roughened by etching can be smoothened, and boron from the clean room inevitably taken into the bonded interface upon bonding and boron 21 8-726q thermally diffused in the epitaxial Si layer from the porous Si layer can be removed.
[Seventh Embodiment]
The seventh preferred embodiment will be described with reference to Figs. 9A to 9G. Numerals in Figs. 9A
to 9G which are the same as those in Figs. 8A to 8E
represent the same portions in Figs. 8A to 8E. In the embodiment shown in Figs. 8A to 8E, the surfaces of the two substrates to be bonded are the SiO2 layer 103 and the SiO2 layer 104. However, both of these surfaces are not necessarily the SiO2 layers, but at least one of them may be made of SiO2. In this preferred embodiment, the surface of an epitaxial silicon layer 1102 formed on a porous silicon layer is bonded to the surface of an oxidized film 1104 formed on a silicon substrate 1110, and the surface of an oxidized film 1103 formed by thermal oxidation of the surface of the epitaxial silicon layer 1102 is bonded to the surface of the silicon substrate 1110 which is not oxidized. In this preferred embodiment, the other processes can be performed as in the embodiment shown in Figs. 8A to 8E.
[Eighth Embodiment]
The eighth preferred embodiment will be described with reference to Figs. lOA to lOG. Numerals in Figs.
lOA to lOG which are the same as those in Figs. 8A to 8E represent the same portions in Figs. 8A to 8E. In this preferred embodiment, it is characterized in that a substrate bonded to a substrate formed with an epitaxial silicon film is made of a glass material 1210, such as quartz glass or blue glass. In this preferred embodiment, an epitaxial silicon layer 1102 is bonded to the glass substrate 1210, and an oxidized film 1103 formed by thermal oxidation of the surface of the epitaxial silicon layer 1102 is bonded to the glass substrate 1210. In this preferred embodiment, the other processes can be performed as in the embodiment shown in Figs. 8A to 8E.
Hereinbelow, the present invention will be described in detail using concrete examples. However, the present invention is not limited thereto.
[Example 1]
A first p- or n-type (100) single-crystal Si substrate having 625,um in thickness, O.OlQ-cm in resistivity and 6 inches in diameter was anodized in an HF solution.
The anodization condition was as follows:
Current Density: 5 (mA-cm~2) Anodization Solution: HF:H20:C2H50H=1:1:1 Time: 12 (minutes) Thickness of Porous Si: 10 (,um) Porosity: 15 (%) Subsequently, He~ ions of 5xlO16/cm2 were implanted into the porous side of the substrate at acceleration voltage of 30keV. Then, the substrate was subjected to the heat treatment at 850C in the vacuum for 8 hours.
When the light of a mercury lamp was applied to the substrate, luminescence of the red light with wavelength around 750nm was confirmed.
[Example 2]
Two first p-type (100) single-crystal Si substrates each having 625,um in thickness, O.OlS2-cm in resistivity and 6 inches in diameter were prepared, and one of them was anodized in an HF solution.
The anodization condition was as follows:
Current Density: 5 (mA-cm~2) Anodization Solution: HF:H20:C2H50H=1:1:1 Time: 12 (minutes) Thickness of Porous Si: 10 (,um) Porosity: 15 (%) He+ ions of 5xlO16/cm2 were implanted into the porous side of the anodized substrate and the surface side of the other substrate at acceleration voltage of 30keV. Subsequently, phosphorus ions of 5xlO14/cm2 were 20 implanted into the porous side of the anodized substrate and the surface side of the other substrate at acceleration voltage of lOOkeV. Then, these substrates were subjected to the heat treatment at 850C
in the vacuum for 8 hours. Further, IT0 electrodes 25 were deposited on the surfaces.
When the voltage was applied between the Si substrates and the IT0 electrodes, luminescence of 2 1 ~37269 wavelength around 750nm was confirmed at the porous substrate, while ll~m;ne~cence was not confirmed at the other substrate.
[Example 3]
Two first p- or n-type (100) single-crystal Si substrates each having 625~um in thickness, O.OlQ-cm in resistivity and 6 inches in diameter were prepared, and one of them was anodized in an HF solution.
The anodization condition was as follows:
Current Density: 5 (mA-cm~2) Anodization Solution: HF:H20:C2H50H=l:1:1 Time: 12 (minutes) Thickness of Porous Si: 20 (,um) Porosity: 15 (%) The anodized substrate was oxidized at 400C in the oxygen atmosphere for 1 hour. Through the oxidation, the pore inner walls of porous Si were coated with a thermal-oxidized film. Subsequently, hydrogen ions of lxlO17/cm2 were implanted all over the porous side of the porous substrate and all over the other substrate at acceleration voltage of 0.76MeV.
When these substrates were subjected to the heat treatment at l,000C in the vacuum for 1 hour, the porous layer was separated uniformly all over the substrate with a thickness of about l,um corresponding to the ion-implanted region, while a lot of swells like blisters were only formed at the non-porous substrate.

_ - 69 - 218726~

[Example 4]
A first p-type (100) single-crystal Si substrate having 625~um in thickness, O.OlQ-cm in resistivity and 6 inches in diameter was anodized in an HF solution.
The anodization condition was as follows:
Current Density: 5 (mA-cm~2) Anodization Solution: HF:H20:C2H50H=1:1:1 Time: 12 (minutes) Thickness of Porous Si: 10 (,um) Porosity: 15 (~) The substrate was oxidized at 400C in the oxygen atmosphere for 1 hour. Through the oxidation, the pore inner walls of porous Si were coated with a thermal-oxidized film. Using the CVD (chemical vapor deposition) method, single-crystal Si was epitaxial-grown by O.lmm on porous Si. The growing condition was as follows:
Source Gas: SiHzClz/Hz Gas Flow Rate: 0.5/180 l/min Gas Pressure: 80 Torr Temperature: 900 C
Growing Speed: 0.3 ~um/min He4 ions of 5xlO16/cmZ were implanted into the porous side of the anodized substrate and the surface side of the other substrate at acceleration voltage of 30keV. Subsequently, phosphorus ions of 5xlO1~/cm2 were implanted into the porous side of the anodized substrate and the surface side of the other substrate at acceleration voltage of lOOkeV. Then, these substrates were subjected to the heat treatment at 850C
in the argon atmosphere for 8 hours. Further, IT0 electrodes were deposited on the surfaces.
When the voltage was applied between the Si substrate and the IT0 electrode, luminescence of wavelength around 750nm was confirmed at the porous substrate.
[Example 5]
Two first p- or n-type (100) single-crystal Si substrates each having 625,um in thickness, O.Oln-cm in resistivity and 6 inches in diameter were prepared and anodized in an HF solution.
The anodization condition was as follows:
Current Density: 5 (mA-cm~2) Anodization Solution: HF:H20:C2H50H-l:l:l Time: 12 (minutes) Thickness of Porous Si: 3 (,um) Porosity: 15 (%) The substrates were oxidized at 400C in the oxygen atmosphere for 1 hour. Through the oxidation, the pore inner walls of porous Si were coated with thermal-oxidized films. Using the CVD (chemical vapor deposition) method, single-crystal Si was epitaxial-grown by 0.15,um on porous Si. The growing condition was as follows:

Source Gas: SiH2Cl2/H2 Gas Flow Rate: 0.5/180 l/min Gas Pressure: 80 Torr Temperature: 950 C
Growing Speed: 0.3 ~m/min Further, an SiO2 layer of 100nm was formed on the surface of each epitaxial Si layer through thermal oxidation.
Subsequently, Het ions of lxl017/cm2 were implanted into the porous side of only one of the substrates at acceleration voltage of 50keV.
The surface of the SiO2 layer and the surface of a separately prepared support Si substrate formed with an SiO2 layer of 500nm were overlapped and abutted with each other, and subjected to the heat treatment at 1,000C for 2 hours so as to increase the bonding strength. Then, the two substrates were completely separated at a position corresponding to the projection range of the ion implantation. The separated surfaces were observed in detail using an optical microscope, but exposed portions of the initial bonded interface were not found. On the other hand, no change on the outward appearance was caused on the substrate which was not subjected to the helium ion implantation, and the substrates remained bonded to each other. Thus, the porous Si substrate side of the bonded substrates (not subjected to the helium ion implantation) was ~ - 72 - 2187269 ground using a grinder for the normal semiconductor so as to expose the porous Si layer. However, due to insufficient grinding accuracy, the whole porous layer could not be exposed.
Thereafter, the porous Si layer remaining on the support substrate side was agitated in a mixed solution (1:5) of 49% hydrofluoric acid and 30% hydrogen peroxide water for selective etching. Single-crystal Si remained without being etched so that porous Si was selective-etched using single-crystal Si as etching stopper and fully removed.
The etching speed of non-porous single-crystal Si relative to the etching liquid is extremely low so that the ratio of etching selectively relative to the etching speed of the porous layer reaches as much as no less than 105 and the etching amount (about several tens of angstroms) at the non-porous layer can be ignored from a practical point of view.
Specifically, the single-crystal Si layer having O.l~m in thickness was formed on the Si oxidized film.
No change was caused on the single-crystal Si layer even by the selective etching of porous Si.
As the result of section observation by a transmission electron microscope, it was confirmed that no new crystal defects were introduced into the Si layer and the excellent crystalline property was maintained.

- 73 ~ Z187~69 Similar results were obtained even without forming the oxidized film on the surface of the epitaxial Si layer.
[Example 6]
Two first p- or n-type (100) single-crystal Si substrates each having 625,um in thickness, O.OlQ-cm in resistivity and 6 inches in diameter were prepared and anodized in an HF solution.
The anodization condition was as follows:
Current Density: 5 (mA-cm~2) Anodization Solution: HF:HzO:C2H50H=l:l:
Time: 12 (minutes) Thickness of Porous Si: 10 (,um) Porosity: 15 (%) The substrates were oxidized at 400C in the oxygen atmosphere for 1 hour. Through the oxidation, the pore inner walls of porous Si were coated with thermal-oxidized films. Using the CVD (chemical vapor deposition) method, single-crystal Si was epitaxial-grown by 0.15,um on porous Si. The growing condition was as follows. The accuracy of the film thickness was +2~.
Source Gas: SiH2Cl2/H2 Gas Flow Rate: 0.5/180 l/min Gas Pressure: 80 Torr Temperature: 950 C
Growing Speed: 0.3 ~m/min _ - 74 ~ 2l g 7269 Further, an SiO2 layer of lOOnm was formed on the surface of each epitaxial Si layer through thermal oxidation.
Subsequently, hydrogen ions of 5xlO16/cm2 were implanted into the porous side of only one of the substrates at acceleration voltage of 50keV.
The surface of the SiO2 layer and the surface of a separately prepared support Si substrate formed with an SiO2 layer of 500nm were overlapped and abutted with each other, and subjected to the heat treatment at 1,000C for 2 hours so as to increase the bonding strength. Then, the two substrates were completely separated at a position corresponding to the projection range of the ion implantation. The separated surfaces were observed in detail using an optical microscope, but exposed portions of the initial bonded interface were not found. On the other hand, no change on the outward appearance was caused on the substrate which was not subjected to the hydrogen ion implantation, and the substrates remained bonded to each other. The porous substrate side of the bonded substrates (not subjected to the hydrogen ion implantation) was ground using a grinder for the normal semiconductor so as to expose the porous layer. However, due to insufficient grinding accuracy, a thickness of the remaining porous layer was 1 to 9,um.
Thereafter, the porous Si layer r~i n; ng on the ~ 75 ~ 21 8 726q support substrate side was agitated in a mixed solution (1:2) of 49% hydrofluoric acid and 30% hydrogen peroxide water for selective etching. Single-crystal Si remained without being etched so that porous Si was selective-etched using single-crystal Si as etching stopper and fully removed.
The etching speed of non-porous single-crystal Si relative to the etching liquid is extremely low so that the ratio of etching selectively relative to the etching speed of the porous layer reaches as much as no less than 105 and the etching amount (about several tens of angstroms) at the non-porous layer can be ignored from a practical point of view.
Specifically, the single-crystal Si layer having O.l~um in thickness was formed on the Si oxidized film.
Thicknesses of the formed single-crystal Si layer were measured at 100 points thereover. Uniformity of the thicknesses was lOlnm + 3nm with the hydrogen ion implantation, while it was lOlnm + 7nm without the hydrogen ion implantation so that it was confirmed that the thickness distribution was deteriorated due to influence of dispersion of thicknesses of porous silicon.
Thereafter, the heat treatment was performed at 1,100C in the hydrogen atmosphere for 1 hour.
When evaluating the surface roughness using an interatomic force microscope, the mean square roughness at a 50~m square region was about 0.2nm which was equal to the silicon wafer on the market.
As the result of section observation by a transmission electron microscope, it was confirmed that no new crystal defects were introduced into the Si layer and the excellent crystalline property was maintained.
Similar results were obtained even without forming the oxidized film on the surface of the epitaxial Si layer.
At the same time, the porous Si layer remaining on the Si substrate side was also agitated in a mixed solution (1:2) of 49% hydrofluoric acid and 30%
hydrogen peroxide water for selective etching. Single-crystal Si remained without being etched so that porous Si was selective-etched using single-crystal Si as etching stopper and fully removed, and the Si substrate could be again put into the porous-forming process.
[Example 7]
Two first p- or n-type (100) single-crystal Si substrates each having 625~um in thickness, O.OlQ-cm in resistivity and 5 inches in diameter were prepared and anodized in an HF solution.
The anodization condition was as follows:
Current Density: 5 (mA-cm~2) Anodization Solution: HF:H20:C2H50H=1:1:1 Time: 12 (minutes) -- _ 77 ~ 2l 8 7269 Thickness of Porous Si: 10 (~m) Porosity: 15 (%) The substrates were oxidized at 400C in the oxygen atmosphere for 1 hour. Through the oxidation, the pore inner walls of porous Si were coated with thermal-oxidized films. Using the CVD (chemical vapor deposition) method, single-crystal Si was epitaxial-grown by 0.55~m on porous Si. The growing condition was as follows. The accuracy of the film thickness was +2%.
Source Gas: SiH2Cl2/H2 Gas Flow Rate: 0.5/180 l/min Gas Pressure: 80 Torr Temperature: 900 C
Growing Speed: 0.3 ~m/min Further, an SiO2 layer of lOOnm was formed on the surface of each epitaxial Si layer through thermal oxidation.
Subsequently, hydrogen ions of 5xlO17/cm2 were implanted into the porous side of only one of the substrates at acceleration voltage of lOOkeV.
The surface of the SiO2 layer and the surface of a separately prepared support quartz substrate were exposed to oxygen plasma, respectively, then overlapped and abutted with each other, and subjected to the heat treatment at 200C for 2 hours so as to increase the bonding strength. The sufficient pressure is applied _ - 78 - 218 726 9 to the bonded wafers perpendicularly relative to the in-plane and uniformly over the in-plane. Then, the porous Si layer was divided into two at the ion-implanted region.
On the other hand, when the pressure was further applied to the substrate (not subjected to the hydrogen ion implantation), the porous layer was ruptured into two. However, when observing the divided porous layers, cracks were introduced into portions of the single-crystal Si layer so that the substrate could not be put into the subsequent process.
Thereafter, the porous Si layer remaining on the second substrate side was agitated in a mixed solution (1:2) of 49% hydrofluoric acid and 30% hydrogen peroxide water for selective etching. Single-crystal Si remained without being etched so that porous Si was selective-etched using single-crystal Si as etching stopper and fully removed.
The etching speed of non-porous single-crystal Si relative to the etching liquid is extremely low so that the selection ratio relative to the etching speed of the porous layer reaches as much as no less than 105 and the etching amount (about several tens of angstroms) at the non-porous layer can be ignored from a practical point of view.
Specifically, the single-crystal Si layer having 0.5~m in thickness was formed on the Si oxidized film.

Thicknesses of the formed single-crystal Si layer were measured at 100 points thereover. Uniformity of the thicknesses was 501nm + llnm with the hydrogen ion implantation.
Thereafter, the heat treatment was performed at 1,100C in the hydrogen atmosphere for 1 hour.
When evaluating the surface roughness using an interatomic force microscope, the mean square roughness at a 50~m square region was about 0.2nm which was equal to the silicon wafer on the market.
As the result of section observation by a transmission electron microscope, it was confirmed that no new crystal defects were introduced into the Si layer and the excellent crystalline property was maintained.
Similar results were obtained even without forming the oxidized film on the surface of the epitaxial Si layer.
Using the CVD (chemical vapor deposition) method, single-crystal Si was again epitaxial-grown by 0.55,um on porous Si remaining at the first substrate side.
The growing condition was as follows. The accuracy of the film thickness was +2%.
Source Gas: SiH2Cl2/H2 Gas Flow Rate: 0.5/180 l/min Gas Pressure: 80 Torr Temperature: 900 C

2~ 87269 Growing Speed: 0.3 ,um/min When evaluating the crystal defect density of this single-crystal Si layer through the defect revealing etching, the defect density was about lxlO3/cm2 and this substrate could be again put into the processes of ion implantation and bonding.
Similar results were obtained even without forming the oxidized film on the surface of the epitaxial Si layer.
[Example 8]
Two first p- or n-type (100) single-crystal Si substrates each having 625~um in thickness, O.OlQ-cm in resistivity and 6 inches in diameter were prepared and anodized in an HF solution.
The anodization condition was as follows:
Current Density: 5 (mA-cm~2) Anodization Solution: HF:H20:C2H50H=1:1:1 Time: 12 (minutes) Thickness of Porous Si: 10 (,um) Porosity: 15 (~) The substrates were oxidized at 400C in the oxygen atmosphere for 1 hour. Through the oxidation, the pore inner walls of porous Si were coated with thermal-oxidized films. Using the CVD (chemical vapor deposition) method, single-crystal Si was epitaxial-grown by 0.15,um on porous Si. The growing condition was as follows. The accuracy of the film thickness was +2~.
Source Gas: SiH2C12/H2 Gas Flow Rate: 0.5/180 l/min Gas Pressure: 80 Torr Temperature: 950 C
Growing Speed: 0.3 ,um/min Further, an SiO2 layer of lOOnm was formed on the surface of each epitaxial Si layer through thermal oxidation.
Subsequently, helium ions of lxlOl7/cm2 were implanted into the porous side of only one of the substrates at acceleration voltage of lOOkeV.
The surface of the SiO2 layer and the surface of a separately prepared support Si substrate formed with an SiO2 layer of 500nm were overlapped and abutted with each other, and subjected to the heat treatment at 400C
for 2 hours. The sufficient tensile force is applied to the bonded wafers perpendicularly relative to the in-plane and uniformly over the in-plane. Then, the two substrates were completely separated at a position corresponding to the projection range of the helium ion implantation. The separated surfaces were observed in detail using an optical microscope, but exposed portions of the initial bonded interface were not found.
On the other hand, when the pressure was further applied to the substrate (not subjected to the helium ion implantation), the porous layer was ruptured into two. However, when observing the divided porous layers, cracks were introduced into portions of the single-crystal Si layer so that the substrate could not be put into the subsequent process.
Thereafter, the porous Si layer remaining on the support substrate side was agitated in a mixed solution (1:2) of 49% hydrofluoric acid and 30% hydrogen peroxide water for selective etching. Single-crystal Si remained without being etched so that porous Si was selective-etched using single-crystal Si as etching stopper and fully removed.
The etching speed of non-porous single-crystal Si relative to the etching liquid is extremely low so that the selection ratio relative to the etching speed of the porous layer reaches as much as no less than 105 and the etching amount (about several tens of angstroms) at the non-porous layer can be ignored from a practical point of view.
Specifically, the single-crystal Si layer having O.l,um in thickness was formed on the Si oxidized film.
Thicknesses of the formed single-crystal Si layer were measured at 100 points thereover. Uniformity of the thicknesses was lOlnm + 3nm with the hydrogen ion implantation, while it was lOlnm + 7nm without the hydrogen ion implantation so that it was confirmed that the thickness distribution was deteriorated due to _ - 83 ~ 21 872 69 influence of dispersion of thicknesses of porous silicon.
Thereafter, the heat treatment was performed at 1,100C in the hydrogen atmosphere for 1 hour.
When evaluating the surface roughness using an interatomic force microscope, the mean square roughness at a 50~m square region was about 0.2nm which was equal to the silicon wafer on the market.
As the result of section observation by a transmission electron microscope, it was confirmed that no new crystal defects were introduced into the Si layer and the excellent crystalline property was maintained.
Similar results were obtained even without forming the oxidized film on the surface of the epitaxial Si layer.
At the same time, the porous Si layer remaining on the Si substrate side was also agitated in a mixed solution (1:2) of 49% hydrofluoric acid and 30%
hydrogen peroxide water for selective etching. Single-crystal Si remained without being etched so that porous Si was selective-etched using single-crystal Si as etching stopper and fully removed, and the Si substrate could be again put into the porous-forming process.
[Example 9]
Two first p- or n-type (100) single-crystal Si substrates each having 625,um in thickness, O.OlQ-cm in resistivity and 6 inches in diameter were prepared and anodized in an HF solution.
The anodization condition was as follows:
Current Density: 5 (mA-cm~2) Anodization Solution: HF:H20:C2H50H=l:l:l Time: 12 (minutes) Thickness of Porous Si: 10 (,um) Porosity: 15 (%) The substrates were oxidized at 400C in the oxygen atmosphere for 1 hour. Through the oxidation, the pore inner walls of porous Si were coated with thermal-oxidized films. Using the MBE (molecular beam epitaxy) method, single-crystal Si was epitaxial-grown by 0.5,um on porous Si. The growing condition was as follows.
The accuracy of the film thickness was +2%.
Temperature: 700C
Pressure: 1 x 10-9 Torr Growing Speed: 0.1 nm/sec Temperature: 950 C
Growing Speed: 0.3 ,um/min Further, an SiO2 layer of lOOnm was formed on the surface of each epitaxial Si layer through thermal oxidation.
Subsequently, helium ions of lxlOl7/cm2 were implanted into the porous side of only one of the substrates at acceleration voltage of lOOkeV.
The surface of the SiO2 layer and the surface of a 2 1 8726~

separately prepared support Si substrate formed with an SiO2 layer of 500nm were overlapped and abutted with each other, and subjected to the heat treatment at 300C
for 2 hours. The bonded two wafers were fixed by a vacuum chuck and applied with torsion and shearing forces in the horizontal direction relative to the main surface of the wafers. Then, the two substrates were completely separated at a position corresponding to the projection range of the helium ion implantation. The separated surfaces were observed in detail using an optical microscope, but exposed portions of the initial bonded interface were not found.
On the other hand, when the pressure was further applied to the substrate (not subjected to the helium ion implantation), the vacuum chuck was detached and the substrate could not be put into the subsequent process.
Thereafter, the porous Si layer remaining on the support substrate side was agitated in a mixed solution (1:2) of 49% hydrofluoric acid and 30~ hydrogen peroxide water for selective etching. Single-crystal Si remained without being etched so that porous Si was selective-etched using single-crystal Si as etching stopper and fully removed.
The etching speed of non-porous single-crystal Si relative to the etching liquid is extremely low so that the selection ratio relative to the etching speed of the porous layer reaches as much as no less than 105 and the etching amount (about several tens of angstroms) at the non-porous layer can be ignored from a practical point of view.
Specifically, the single-crystal Si layer having O.l,um in thickness was formed on the Si oxidized film.
Thicknesses of the formed single-crystal Si layer were measured at 100 points thereover. Uniformity of the thicknesses was lOlnm + 3nm with the hydrogen ion implantation, while it was lOlnm + 7nm without the hydrogen ion implantation so that it was confirmed that the thickness distribution was deteriorated due to influence of dispersion of thicknesses of porous silicon.
Thereafter, the heat treatment was performed at 1,100C in the hydrogen atmosphere for 1 hour.
When evaluating the surface roughness using an interatomic force microscope, the mean square roughness at a 50~um square region was about 0.2nm which was equal to the silicon wafer on the market.
As the result of section observation by a transmission electron microscope, it was confirmed that no new crystal defects were introduced into the Si layer and the excellent crystalline property was maintained.
Similar results were obtained even without forming the oxidized film on the surface of the epitaxial Si layer.
At the same time, the porous Si layer remaining on the Si substrate side was also agitated in a mixed solution (1:2) of 49% hydrofluoric acid and 30%
hydrogen peroxide water for selective etching. Single-crystal Si remained without being etched so that porous Si was selective-etched using single-crystal Si as etching stopper and fully removed, and the Si substrate could be again put into the porous-forming process.
[Example 10]
Two first p- or n-type (100) single-crystal Si substrates each having 625~um in thickness, O.OlQ-cm in resistivity and 5 inches in diameter were prepared and anodized in an HF solution.
The anodization condition was as follows:
Current Density: 5 (mA-cm~Z) Anodization Solution: HF:H20:C2H50H=1:1:1 Time: 12 (minutes) Thickness of Porous Si: 10 (,um) Porosity: 15 (~) The substrates were oxidized at 400C in the oxygen atmosphere for 1 hour. Through the oxidation, the pore inner walls of porous Si were coated with thermal-oxidized films. Using the CVD (chemical vapor deposition) method, single-crystal Si was epitaxial-grown by 0.55~um on porous Si. The growing condition was as follows. The accuracy of the film thickness was - 88 ~ 2~8 7269 +2%.
Source Gas: SiH2Cl2/H2 Gas Flow Rate: 0.5/180 l/min Gas Pressure: 80 Torr Temperature: 900 C
Growing Speed: 0.3 ,um/min Further, an SiO2 layer of lOOnm was formed on the surface of each epitaxial Si layer through thermal oxidation.
Subsequently, hydrogen ions of lxlO18/cm2 were implanted into the porous side of only one of the substrates at acceleration voltage of lOOkeV.
The surface of the SiO2 layer and the surface of a separately prepared support quartz substrate were exposed to oxygen plasma, respectively, then overlapped and abutted with each other, and subjected to the heat treatment at 200C for 2 hours so as to increase the bonding strength. Then, the porous Si layer was divided into two at the ion-implanted region.
On the other hand, no change was observed at the substrate which was not subjected to the helium ion implantation.
Thereafter, the porous Si layer remaining on the support substrate side was agitated in a mixed solution (1:2) of 49% hydrofluoric acid and 30% hydrogen peroxide water for selective etching. Single-crystal Si remained without being etched so that porous Si was selective-etched using single-crystal Si as etching stopper and fully removed.
The etching speed of non-porous single-crystal Si relative to the etching liquid is extremely low so that the selection ratio relative to the etching speed of the porous layer reaches as much as no less than 105 and the etching amount (about several tens of angstroms) at the non-porous layer can be ignored from a practical point of view.
Specifically, the single-crystal Si layer having 0.5~um in thickness was formed on the quartz substrate.
Thicknesses of the formed single-crystal Si layer were measured at 100 points thereover. Uniformity of the thicknesses was 501nm + llnm with the hydrogen ion implantation. Thereafter, the heat treatment was performed at 1,100C in the hydrogen atmosphere for 1 hour.
When evaluating the surface roughness using an interatomic force microscope, the mean square roughness at a 50~um square region was about 0.2nm which was equal to the silicon wafer on the market.
As the result of section observation by a transmission electron microscope, it was confirmed that no new crystal defects were introduced into the Si layer and the excellent crystalline property was maintained.
Similar results were obtained even without forming - - 9o -2187~69 the oxidized film on the surface of the epitaxial Si layer.
[Example 11]
A first p- or n-type (100) single-crystal Si substrate having 625,um in thickness, O.OlQ-cm in resistivity and 5 inches in diameter was prepared and anodized in an HF solution.
The anodization condition was as follows:
Current Density: 5 (mA-cm~2) Anodization Solution: HF:H20:C2HsOH=1:1:1 Time: 12 (minutes) Thickness of Porous Si: 10 (,um) Porosity: 15 (%) The substrate was oxidized at 400C in the oxygen atmosphere for 1 hour. Through the oxidation, the pore inner walls of porous Si were coated with thermal-oxidized films. Using the MOCVD (metal organic chemical vapor deposition) method, single-crystal GaAs was epitaxial-grown by 1,um on porous Si. The growing condition was as follows.
Source Gas: TMG/AsH3/H2 Gas Pressure: 80 Torr Temperature: 700C
Subsequently, helium ions of lxlO18/cm2 were implanted into the porous side of the substrate at acceleration voltage of lOOkeV.
The surface of the GaAs layer and the surface of a 2l 87269 separately prepared support Si substrate were overlapped and abutted with each other, and subjected to the heat treatment at 200C for 2 hours so as to enhance the bonding strength. Then, the porous Si layer was divided into two at the ion-implanted region.
Thereafter, after removing the oxidized film on the inner walls of the porous Si layer using hydrofluoric acid, the porous Si was etched with a solution of ethylenediamine, pyrocatechol and water (ratio: 17ml:3g:8ml) at 110C. Single-crystal GaAs remained without being etched so that porous Si was selective-etched using single-crystal GaAs as etching stopper and fully removed.
The etching speed of single-crystal GaAs relative to the etching liquid is extremely low so that the thickness reduction can be ignored from a practical point of view.
Specifically, the single-crystal GaAs layer having l~m in thickness was formed on the Si substrate. No change was caused on the single-crystal GaAs layer even by the selective etching of porous Si.
As the result of section observation by a transmission electron microscope, it was confirmed that no new crystal defects were introduced into the GaAs layer and the excellent crystalline property was maintained.
By using the Si substrate with the oxidized film _ 92 - 2 1 87269 as the support substrate, GaAs on the insulating film could also be produced similarly.
[Example 12]
A first p- or n-type (100) single-crystal Si substrate having 625,um in thickness, O.OlQ-cm in resistivity and 5 inches in diameter was prepared and anodized in an HF solution.
The anodization condition was as follows:
Current Density: 10 (mA-cm~2) Anodization Solution: HF:H20:C2HsOH=1:1:1 Time: 24 (minutes) Thickness of Porous Si: 20 (~um) Porosity: 17 (%) The substrate was oxidized at 400C in the oxygen atmosphere for 2 hours. Through the oxidation, the pore inner walls of porous Si were coated with thermal-oxidized films. Using the MBE (molecular beam epitaxy) method, single-crystal AlGaAs was epitaxial-grown by 0.5,um on porous Si.
Subsequently, helium ions of lxlO18/cm2 were implanted into the porous side of the substrate at acceleration voltage of lOOkeV.
The surface of the AlGaAs layer and the surface of a separately prepared support substrate of low melting point glass were overlapped and abutted with each other, and subjected to the heat treatment at 500C for 2 hours. Through this heat treatment, the substrates ~ - 93 -were firmly bonded with each other.
When the sufficient pressure was applied to the bonded wafers perpendicularly relative to the in-plane and uniformly over the in-plane, the porous Si layer was divided into two at the ion-implanted region.
Thereafter, porous Si was etched with a hydrofluoric acid solution. Single-crystal AlGaAs remained without being etched so that porous Si was selective-etched using single-crystal AlGaAs as etching stopper and fully removed.
The etching speed of single-crystal AlGaAs relative to the etching liquid is extremely low so that the thickness reduction can be ignored from a practical point of view.
Specifically, the single-crystal AlGaAs layer having 0.5,um in thickness was formed on the glass substrate. No change was caused on the single-crystal AlGaAs layer even by the selective etching of porous si .
As the result of section observation by a transmission electron microscope, it was confirmed that no new crystal defects were introduced into the AlGaAs layer and the excellent crystalline property was maintained.
[Example 13]
A first p- or n-type (100) single-crystal Si substrate with both sides polished and having 625~m in ~ ~ 94 ~ 2l8 ~26 9 thickness, O.OlQ-cm in resistivity and 6 inches in diameter was prepared and anodized at both sides thereof in an HF solution.
The anodization condition was as follows:
Current Density: 5 (mA-cm~2) Anodization Solution: HF:H20:C2HsOH=1:1:1 Time: 12 x 2 (minutes) Thickness of Porous Si: 10 (~m) for each side Porosity: 15 (%) The substrate was oxidized at 400C in the oxygen atmosphere for 1 hour. Through the oxidation, the pore inner walls of porous Si were coated with thermal-oxidized films. Using the CVD (chemical vapor deposition) method, single-crystal Si was epitaxial-grown by 1,um on porous Si formed at each side. The growing condition was as follows.
Source Gas: SiH2C12/H2 Gas Flow Rate: 0.5/180 l/min Gas Pressure: 80 Torr Temperature: 950 C
Growing Speed: 0.3 ~m/min Further, an SiO2 layer of lOOnm was formed on the surface of each epitaxial Si layer through thermal oxidation.
Subsequently, hydrogen ions of lxlO1~/cmZ were implanted into the porous layers at acceleration voltage of lOOkeV.

~~ ~ 95 ~ 2l8 ~269 The surfaces of the SiO2 layers and the surfaces of separately prepared two support Si substrates each formed with an SiO2 layer of 500nm were overlapped and abutted with each other, and subjected to the heat treatment at 600C for 2 hours so as to achieve bonding.
Then, the porous Si layer was divided into two at the ion-implanted region.
Thereafter, the porous Si layer was agitated in a mixed solution (1:5) of 49% hydrofluoric acid and 30%
hydrogen peroxide water for selective etching. Single-crystal Si remained without being etched so that porous Si was selective-etched using single-crystal Si as etching stopper and fully removed.
The etching speed of non-porous single-crystal Si relative to the etching liquid is extremely low so that the selection ratio relative to the etching speed of the porous layer reaches as much as no less than 105 and the etching amount (about several tens of angstroms) at the non-porous layer can be ignored from a practical point of view.
Specifically, the two single-crystal Si layers each having l~m in thickness were simultaneously formed on the Si oxidized films. No change was caused on the single-crystal Si layers even by the selective etching of porous Si.
As the result of section observation by a transmission electron microscope, it was confirmed that 2 1 872~Y

no new crystal defects were introduced into the Si layer and the excellent crystalline property was maintained.
Similar results were obtained even without forming 5 the oxidized film on the surface of the epitaxial Si layer.
[Example 14]
Two first p- or n-type (100) single-crystal Si substrates each having 625~m in thickness, O.OlQ-cm in 10 resistivity and 5 inches in diameter were prepared and anodized in an HF solution.
The anodization condition was as follows:
Current Density: 5 (mA-cm~2) Anodization Solution: HF:H20:C2H50H=l:l:l Time: 12 (minutes) Thickness of Porous Si: 10 (,um) Porosity: 15 (%) The substrates were oxidized at 400C in the oxygen atmosphere for 1 hour. Through the oxidation, the pore 20 inner walls of porous Si were coated with thermal-oxidized films. Using the CVD (chemical vapor deposition) method, single-crystal Si was epitaxial-grown by 0.55,um on porous Si. The growing condition was as follows. The accuracy of the film thickness was 25 +2%.
Source Gas: SiH2Cl2/H2 Gas Flow Rate: 0.5/180 l/min _ 97 _ 2~8 7269 Gas Pressure: 80 Torr Temperature: 900 C
Growing Speed: 0.3 ,um/min Further, an SiO2 layer of 100nm was formed on the surface of each epitaxial Si layer through thermal oxidation.
Subsequently, hydrogen ions of lxlO18/cm2 were implanted into the porous side of only one of the substrates at acceleration voltage of lOOkeV.
The surface of the SiO2 layer and the surface of a separately prepared support quartz substrate were exposed to oxygen plasma, respectively, then overlapped and abutted with each other, and subjected to the heat treatment at 200C for 2 hours so as to increase the bonding strength. Subsequently, the wave energy such as the ultrasonic wave was applied to the substrates.
Then, the porous Si layer was divided into two at the ion-implanted region.
On the other hand, no change was observed at the substrate which was not subjected to the hydrogen ion implantation.
Thereafter, the porous Si layer remaining on the support substrate side was agitated in a mixed solution (1:2) of 49% hydrofluoric acid and 30% hydrogen peroxide water for selective etching. Single-crystal Si remained without being etched so that porous Si was selective-etched using single-crystal Si as etching - 98 - 2l 8~26 9 stopper and fully removed.
The etching speed of non-porous single-crystal Si relative to the etching liquid is extremely low so that the selection ratio relative to the etching speed of the porous layer reaches as much as no less than 105 and the etching amount (about several tens of angstroms) at the non-porous layer can be ignored from a practical point of view.
Specifically, the single-crystal Si layer having 0.5,um in thickness was formed on the quartz substrate.
Thicknesses of the formed single-crystal Si layer were measured at 100 points thereover. Uniformity of the thicknesses was 501nm + llnm with the hydrogen ion implantation. Thereafter, the heat treatment was performed at 1,100C in the hydrogen atmosphere for 1 hour.
When evaluating the surface roughness using an interatomic force microscope, the mean square roughness at a 50~um square region was about 0.2nm which was equal to the silicon wafer on the market.
As the result of section observation by a transmission electron microscope, it was confirmed that no new crystal defects were introduced into the Si layer and the excellent crystalline property was maintained.
Similar results were obtained even without forming the oxidized film on the surface of the epitaxial Si layer.
The single-crystal Si substrate was reused as a single-crystal Si substrate after removing remaining porous Si and performing surface-polishing to provide a mirror finished surface.

Claims (38)

1. A semiconductor substrate producing method comprising:
a porous-forming step for forming a porous Si layer on at least a surface of an Si substrate; and a large porosity layer forming step for forming large porosity layer at a constant depth from a surface of said porous Si in said porous Si layer.
2. The semiconductor substrate producing method according to claim 1, wherein said large porosity layer forming step has an ion implanting step for implanting ions into said porous Si layer with a given projection range.
3. The semiconductor substrate producing method according to claim 2, further comprising a non-porous layer forming step for forming a non-porous layer on a surface of said porous layer before said ion implanting step.
4. The semiconductor substrate producing method according to claim 2, wherein said ions comprises at least one kind of noble gas, hydrogen and nitrogen.
5. The semiconductor substrate producing method according to claim 3, further comprising a bonding step for bonding said non-porous layer and a support substrate together; and a separating step for separating said Si substrate into two at said large porosity layer.
6. The semiconductor substrate producing method according to claim 5, wherein said separating step is performed by heat-treating said Si substrate.
7. The semiconductor substrate producing method according to claim 5, wherein said separating step is performed by pressurizing said Si substrate in a direction perpendicular to a surface thereof.
8. The semiconductor substrate producing method according to claim 5, wherein said separating step is performed by drawing said Si substrate in a direction perpendicular to a surface thereof.
9. The semiconductor substrate producing method according to claim 5, wherein said separating step is performed by applying a shearing force to said Si substrate.
10. The semiconductor substrate producing method according to claim 3, wherein said non-porous layer is made of single-crystal Si.
11. The semiconductor substrate producing method according to claim 3, wherein said non-porous layer is made of single-crystal Si having an oxidized Si layer on a surface to be bonded.
12. The semiconductor substrate producing method according to claim 3, wherein said non-porous layer is made of a single-crystal compound semiconductor.
13. The semiconductor substrate producing method according to claim 5, wherein said support substrate is an Si substrate.
14. The semiconductor substrate producing method according to claim 5, wherein said support substrate is an Si substrate having an oxidized Si layer on a surface to be bonded.
15. The semiconductor substrate producing method according to claim 5, wherein said support substrate is a light transmittable substrate.
16. The semiconductor substrate producing method according to claim 5, wherein said bonding step is performed by anode bonding, pressurization, heat treatment or a combination thereof.
17. The semiconductor substrate producing method according to claim 5, further comprising a porous Si removing step, after said separating step, for removing the porous Si layer exposed on a surface of said support substrate and exposing said non-porous layer.
18. The semiconductor substrate producing method according to claim 17, wherein said porous Si removing step is performed by an electroless wet etching using at least one of hydrofluoric acid, a mixed liquid obtained by adding at least one of alcohol and hydrogen peroxide water to hydrofluoric acid, buffered hydrofluoric acid, and a mixed liquid obtained by adding at least one of alcohol and hydrogen peroxide water to buffered hydrofluoric acid.
19. The semiconductor substrate producing method according to claim 17, further comprising a flattening step for flattening a surface of said non-porous layer after said porous Si removing step.
20. The semiconductor substrate producing method according to claim 19, wherein said flattening step is performed by heat treatment in the atmosphere including hydrogen.
21. The semiconductor substrate producing method according to claim 5, wherein said porous-forming step forms porous Si layers on both sides of said Si substrate, and said bonding step bonds two support substrates to said porous Si layers formed on both sides of said Si substrate.
22. The semiconductor substrate producing method according to claim 5, further comprising a second non-porous layer forming step, after said separating step, for forming non-porous layer again on the surface of said porous Si layer, and a second ion implanting step, after said second non-porous layer forming step, for implanting ions into said porous Si layer with a given projection range and forming large porosity layer in said porous Si layer.
23. The semiconductor substrate producing method according to claim 1, wherein said porous-forming step is performed by anodization.
24. The semiconductor substrate producing method according to claim 23, wherein said anodization is performed in an HF solution or a mixture of an HF
solution and alcohol.
25. The semiconductor substrate producing method according to claim 1, wherein said large porosity layer forming step is performed by changing a current density of anodization in said porous-forming step.
26. A semiconductor substrate comprising:
a porous Si layer formed at a surface layer of an Si substrate; and a large porosity layer formed in said porous Si layer wherein said large porosity layer exists in a region located at a constant depth from a surface of said porous Si layer.
27. The semiconductor substrate according to claim 26, wherein non-porous Si layer exists on surface of said porous Si layer, and electrodes are formed on surface of said non-porous Si layer and on surface of said Si substrate, in order that said semiconductor substrate becomes an EL element.
28. A semiconductor substrate producing method comprising:
forming on a surface of a Si substrate a first porous Si layer, a second porous Si layer and a third porous Si layer, wherein the second porous Si layer is located under the first porous Si layer and has a porosity higher than the first porous Si layer, and the third porous Si layer is located under the second porous Si layer and has a porosity lower than the second porous Si layer;

forming a non-porous monocrystalline semiconductor layer on the first porous Si layer;
bonding the non-porous monocrystalline semiconductor layer located on the Si substrate to another substrate;
and separating the Si substrate and the other substrate at the second porous Si layer so that the non-porous monocrystalline semiconductor layer remains on the other substrate.
29. The semiconductor substrate producing method according to claim 28, wherein said forming step for forming said first, second and third porous Si layers comprises a step for turning a surface portion of said Si substrate porous.
30. The semiconductor substrate producing method according to claim 29, wherein said second porous Si layer is formed by means of ion implantation.
31. The semiconductor substrate producing method according to claim 28, wherein said non-porous monocrystalline semiconductor layer is formed by epitaxial growth.
32. The semiconductor substrate producing method according to claim 28, wherein said bonding step is conducted after forming an insulating layer on a surface of said non-porous monocrystalline semiconductor layer.
33. The semiconductor substrate producing method according to claim 28, wherein said second porous Si layer is formed by implanting ions after forming said non-porous monocrystalline semiconductor layer through epitaxial growth.
34. A semiconductor substrate producing method comprising:
forming on a surface of a Si substrate a first porous Si layer;
implanting ions into the first porous Si layer to form a second porous Si layer having a porosity higher than the first porous Si layer at a constant depth from a surface of the first porous Si layer;
forming a non-porous monocrystalline semiconductor layer on the first porous Si layer;
bonding the non-porous monocrystalline semiconductor layer located on the Si substrate to another substrate;
and separating the Si substrate and the other substrate at the second porous Si layer so that the non-porous monocrystalline semiconductor layer remains on the other substrate.
35. The semiconductor substrate producing method according the claim 34, wherein said forming step for forming said first porous Si layer comprises a step for turning a surface portion of said Si substrate porous.
36. The semiconductor substrate producing method according to claim 34, wherein said non-porous monocrystalline semiconductor layer is formed by epitaxial growth.
37. The semiconductor substrate producing method according to claim 34, wherein said bonding step is conducted after forming an insulating layer on a surface of said non-porous monocrystalline semiconductor layer.
38. The semiconductor substrate producing method according to claim 34, wherein said second porous Si layer is formed by conducting said ion implantation after forming said non-porous monocrystalline semiconductor layer through epitaxial growth.
CA002187269A 1995-10-06 1996-10-07 Semiconductor substrate and producing method thereof Expired - Fee Related CA2187269C (en)

Applications Claiming Priority (4)

Application Number Priority Date Filing Date Title
JP26010095 1995-10-06
JP7-260100 1995-10-06
JP26438696A JP3352340B2 (en) 1995-10-06 1996-10-04 Semiconductor substrate and method of manufacturing the same
JP8-264386 1996-10-04

Publications (2)

Publication Number Publication Date
CA2187269A1 CA2187269A1 (en) 1997-04-07
CA2187269C true CA2187269C (en) 2001-05-08

Family

ID=26544448

Family Applications (1)

Application Number Title Priority Date Filing Date
CA002187269A Expired - Fee Related CA2187269C (en) 1995-10-06 1996-10-07 Semiconductor substrate and producing method thereof

Country Status (9)

Country Link
US (3) US5854123A (en)
EP (1) EP0767486B1 (en)
JP (1) JP3352340B2 (en)
KR (2) KR100291501B1 (en)
CN (1) CN1132223C (en)
CA (1) CA2187269C (en)
DE (1) DE69631233T2 (en)
SG (1) SG63669A1 (en)
TW (1) TW330307B (en)

Families Citing this family (435)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US20030087503A1 (en) * 1994-03-10 2003-05-08 Canon Kabushiki Kaisha Process for production of semiconductor substrate
US7148119B1 (en) 1994-03-10 2006-12-12 Canon Kabushiki Kaisha Process for production of semiconductor substrate
US6326280B1 (en) 1995-02-02 2001-12-04 Sony Corporation Thin film semiconductor and method for making thin film semiconductor
US6107213A (en) * 1996-02-01 2000-08-22 Sony Corporation Method for making thin film semiconductor
TW374196B (en) 1996-02-23 1999-11-11 Semiconductor Energy Lab Co Ltd Semiconductor thin film and method for manufacturing the same and semiconductor device and method for manufacturing the same
US20050280155A1 (en) * 2004-06-21 2005-12-22 Sang-Yun Lee Semiconductor bonding and layer transfer method
US8018058B2 (en) * 2004-06-21 2011-09-13 Besang Inc. Semiconductor memory device
US8058142B2 (en) * 1996-11-04 2011-11-15 Besang Inc. Bonded semiconductor structure and method of making the same
FR2755537B1 (en) * 1996-11-05 1999-03-05 Commissariat Energie Atomique METHOD FOR MANUFACTURING A THIN FILM ON A SUPPORT AND STRUCTURE THUS OBTAINED
SG65697A1 (en) * 1996-11-15 1999-06-22 Canon Kk Process for producing semiconductor article
CA2225131C (en) 1996-12-18 2002-01-01 Canon Kabushiki Kaisha Process for producing semiconductor article
US6767840B1 (en) * 1997-02-21 2004-07-27 Canon Kabushiki Kaisha Wafer processing apparatus, wafer processing method, and semiconductor substrate fabrication method
SG71094A1 (en) 1997-03-26 2000-03-21 Canon Kk Thin film formation using laser beam heating to separate layers
SG63832A1 (en) * 1997-03-26 1999-03-30 Canon Kk Substrate and production method thereof
JP3754818B2 (en) * 1997-03-27 2006-03-15 キヤノン株式会社 Method for manufacturing semiconductor substrate
US6382292B1 (en) 1997-03-27 2002-05-07 Canon Kabushiki Kaisha Method and apparatus for separating composite member using fluid
CA2233115C (en) * 1997-03-27 2002-03-12 Canon Kabushiki Kaisha Semiconductor substrate and method of manufacturing the same
US6191007B1 (en) 1997-04-28 2001-02-20 Denso Corporation Method for manufacturing a semiconductor substrate
US6251754B1 (en) * 1997-05-09 2001-06-26 Denso Corporation Semiconductor substrate manufacturing method
US6033974A (en) 1997-05-12 2000-03-07 Silicon Genesis Corporation Method for controlled cleaving process
US6291313B1 (en) 1997-05-12 2001-09-18 Silicon Genesis Corporation Method and device for controlled cleaving process
US20070122997A1 (en) 1998-02-19 2007-05-31 Silicon Genesis Corporation Controlled process and resulting device
US6159824A (en) 1997-05-12 2000-12-12 Silicon Genesis Corporation Silicon-on-silicon wafer bonding process using a thin film blister-separation method
US7470600B2 (en) * 1998-02-19 2008-12-30 Silicon Genesis Corporation Method and device for controlled cleaving process
JP2976929B2 (en) * 1997-05-30 1999-11-10 日本電気株式会社 Method for manufacturing semiconductor device
US6215244B1 (en) 1997-06-16 2001-04-10 Canon Kabushiki Kaisha Stacked organic light emitting device with specific electrode arrangement
EP0996967B1 (en) 1997-06-30 2008-11-19 Max-Planck-Gesellschaft zur Förderung der Wissenschaften e.V. Method for producing layered structures on a semiconductor substrate, semiconductor substrate and semiconductor components produced according to said method
DE19730975A1 (en) * 1997-06-30 1999-01-07 Max Planck Gesellschaft Porous material especially single crystal silicon layer production
KR100491272B1 (en) * 1997-07-16 2005-08-01 페어차일드코리아반도체 주식회사 A method of fabricating soi wafer
US6534380B1 (en) * 1997-07-18 2003-03-18 Denso Corporation Semiconductor substrate and method of manufacturing the same
US6548382B1 (en) 1997-07-18 2003-04-15 Silicon Genesis Corporation Gettering technique for wafers made using a controlled cleaving process
JP2001511608A (en) 1997-07-29 2001-08-14 シリコン ジェネシス コーポレイション Cluster tool method and apparatus using plasma penetrating ion implantation
US5882987A (en) * 1997-08-26 1999-03-16 International Business Machines Corporation Smart-cut process for the production of thin semiconductor material films
JP2998724B2 (en) 1997-11-10 2000-01-11 日本電気株式会社 Manufacturing method of bonded SOI substrate
US6686623B2 (en) 1997-11-18 2004-02-03 Semiconductor Energy Laboratory Co., Ltd. Nonvolatile memory and electronic apparatus
JPH11162859A (en) * 1997-11-28 1999-06-18 Canon Inc Liquid phase growth of silicon crystal and manufacture of solar battery using the same
FR2773261B1 (en) * 1997-12-30 2000-01-28 Commissariat Energie Atomique METHOD FOR THE TRANSFER OF A THIN FILM COMPRISING A STEP OF CREATING INCLUSIONS
SG71182A1 (en) 1997-12-26 2000-03-21 Canon Kk Substrate processing apparatus substrate support apparatus substrate processing method and substrate manufacturing method
JPH11195775A (en) * 1997-12-26 1999-07-21 Sony Corp Semiconductor substrate, thin-film semiconductor element, manufacture thereof, and anodizing device
US6306729B1 (en) 1997-12-26 2001-10-23 Canon Kabushiki Kaisha Semiconductor article and method of manufacturing the same
JP4075021B2 (en) * 1997-12-26 2008-04-16 ソニー株式会社 Semiconductor substrate manufacturing method and thin film semiconductor member manufacturing method
JP3847935B2 (en) * 1998-01-09 2006-11-22 キヤノン株式会社 Method for removing porous region and method for manufacturing semiconductor substrate
DE19802131B4 (en) * 1998-01-21 2007-03-15 Robert Bosch Gmbh Process for producing a monocrystalline layer of a conductive or semiconductive material
FR2774214B1 (en) * 1998-01-28 2002-02-08 Commissariat Energie Atomique PROCESS FOR PRODUCING A SEMICONDUCTOR TYPE STRUCTURE ON INSULATOR AND IN PARTICULAR SiCOI
KR100567974B1 (en) * 1998-02-10 2006-04-07 인피니언 테크놀로지스 아게 Optical structure and process for manufacturing the same
US6120660A (en) * 1998-02-11 2000-09-19 Silicon Genesis Corporation Removable liner design for plasma immersion ion implantation
JPH11233769A (en) * 1998-02-12 1999-08-27 Semiconductor Energy Lab Co Ltd Semiconductor device and its manufacturing method
US6274459B1 (en) 1998-02-17 2001-08-14 Silicon Genesis Corporation Method for non mass selected ion implant profile control
TW437078B (en) * 1998-02-18 2001-05-28 Canon Kk Composite member, its separation method, and preparation method of semiconductor substrate by utilization thereof
JP3809733B2 (en) * 1998-02-25 2006-08-16 セイコーエプソン株式会社 Thin film transistor peeling method
US6113735A (en) * 1998-03-02 2000-09-05 Silicon Genesis Corporation Distributed system and code for control and automation of plasma immersion ion implanter
JPH11251207A (en) * 1998-03-03 1999-09-17 Canon Inc Soi substrate and manufacturing method therefor, and manufacturing facilities thereof
US6540861B2 (en) * 1998-04-01 2003-04-01 Canon Kabushiki Kaisha Member separating apparatus and processing apparatus
JPH11307747A (en) * 1998-04-17 1999-11-05 Nec Corp Soi substrate and production thereof
JPH11307472A (en) * 1998-04-23 1999-11-05 Shin Etsu Handotai Co Ltd Soi wafer and manufacture soi by hydrogen ion releasing method
JP3697106B2 (en) * 1998-05-15 2005-09-21 キヤノン株式会社 Method for manufacturing semiconductor substrate and method for manufacturing semiconductor thin film
JP2000012864A (en) 1998-06-22 2000-01-14 Semiconductor Energy Lab Co Ltd Manufacture of semiconductor device
US6291326B1 (en) 1998-06-23 2001-09-18 Silicon Genesis Corporation Pre-semiconductor process implant and post-process film separation
JP3358550B2 (en) * 1998-07-07 2002-12-24 信越半導体株式会社 Method for producing SOI wafer and SOI wafer produced by this method
TW444266B (en) * 1998-07-23 2001-07-01 Canon Kk Semiconductor substrate and method of producing same
US6271101B1 (en) * 1998-07-29 2001-08-07 Semiconductor Energy Laboratory Co., Ltd. Process for production of SOI substrate and process for production of semiconductor device
US6124214A (en) * 1998-08-27 2000-09-26 Micron Technology, Inc. Method and apparatus for ultrasonic wet etching of silicon
JP4476390B2 (en) 1998-09-04 2010-06-09 株式会社半導体エネルギー研究所 Method for manufacturing semiconductor device
US6391743B1 (en) 1998-09-22 2002-05-21 Canon Kabushiki Kaisha Method and apparatus for producing photoelectric conversion device
AU5760199A (en) * 1998-09-25 2000-04-17 Asahi Kasei Kabushiki Kaisha Semiconductor substrate and its production method, semiconductor device comprising the same and its production method
US6555443B1 (en) * 1998-11-11 2003-04-29 Robert Bosch Gmbh Method for production of a thin film and a thin-film solar cell, in particular, on a carrier substrate
JP2000349264A (en) 1998-12-04 2000-12-15 Canon Inc Method for manufacturing, use and utilizing method of semiconductor wafer
US20040229443A1 (en) * 1998-12-31 2004-11-18 Bower Robert W. Structures, materials and methods for fabrication of nanostructures by transposed split of ion cut materials
JP4313874B2 (en) * 1999-02-02 2009-08-12 キヤノン株式会社 Substrate manufacturing method
FR2789518B1 (en) * 1999-02-10 2003-06-20 Commissariat Energie Atomique MULTILAYER STRUCTURE WITH INTERNAL CONTROLLED STRESSES AND METHOD FOR PRODUCING SUCH A STRUCTURE
JP2000277478A (en) * 1999-03-25 2000-10-06 Canon Inc Anodization device and system, substrate processing device and method, and manufcature thereof
US6375738B1 (en) 1999-03-26 2002-04-23 Canon Kabushiki Kaisha Process of producing semiconductor article
US6326279B1 (en) 1999-03-26 2001-12-04 Canon Kabushiki Kaisha Process for producing semiconductor article
US6355541B1 (en) * 1999-04-21 2002-03-12 Lockheed Martin Energy Research Corporation Method for transfer of thin-film of silicon carbide via implantation and wafer bonding
US6171965B1 (en) 1999-04-21 2001-01-09 Silicon Genesis Corporation Treatment method of cleaved film for the manufacture of substrates
US6881644B2 (en) * 1999-04-21 2005-04-19 Silicon Genesis Corporation Smoothing method for cleaved films made using a release layer
US6204151B1 (en) * 1999-04-21 2001-03-20 Silicon Genesis Corporation Smoothing method for cleaved films made using thermal treatment
US6287941B1 (en) 1999-04-21 2001-09-11 Silicon Genesis Corporation Surface finishing of SOI substrates using an EPI process
JP2001015721A (en) * 1999-04-30 2001-01-19 Canon Inc Separation method of composite member and manufacture of thin film
US6248642B1 (en) 1999-06-24 2001-06-19 Ibis Technology Corporation SIMOX using controlled water vapor for oxygen implants
FR2795866B1 (en) * 1999-06-30 2001-08-17 Commissariat Energie Atomique METHOD FOR PRODUCING A THIN MEMBRANE AND MEMBRANE STRUCTURE THUS OBTAINED
JP2003506883A (en) * 1999-08-10 2003-02-18 シリコン ジェネシス コーポレイション Cleavage process for manufacturing multi-layer substrates with low implant dose
US6263941B1 (en) 1999-08-10 2001-07-24 Silicon Genesis Corporation Nozzle for cleaving substrates
US6221740B1 (en) 1999-08-10 2001-04-24 Silicon Genesis Corporation Substrate cleaving tool and method
US6500732B1 (en) 1999-08-10 2002-12-31 Silicon Genesis Corporation Cleaving process to fabricate multilayered substrates using low implantation doses
US6423975B1 (en) 1999-08-18 2002-07-23 Ibis Technology, Inc. Wafer holder for simox processing
US6433342B1 (en) 1999-08-18 2002-08-13 Ibis Technology Corporation Coated wafer holding pin
US6155436A (en) * 1999-08-18 2000-12-05 Ibis Technology Corporation Arc inhibiting wafer holder assembly
US6452195B1 (en) 1999-08-18 2002-09-17 Ibis Technology Corporation Wafer holding pin
US6984571B1 (en) 1999-10-01 2006-01-10 Ziptronix, Inc. Three dimensional device integration method and integrated device
US6653205B2 (en) 1999-12-08 2003-11-25 Canon Kabushiki Kaisha Composite member separating method, thin film manufacturing method, and composite member separating apparatus
US7427526B2 (en) * 1999-12-20 2008-09-23 The Penn State Research Foundation Deposited thin films and their use in separation and sacrificial layer applications
US6544862B1 (en) * 2000-01-14 2003-04-08 Silicon Genesis Corporation Particle distribution method and resulting structure for a layer transfer process
US6602767B2 (en) 2000-01-27 2003-08-05 Canon Kabushiki Kaisha Method for transferring porous layer, method for making semiconductor devices, and method for making solar battery
US6902987B1 (en) 2000-02-16 2005-06-07 Ziptronix, Inc. Method for low temperature bonding and bonded structure
KR100742790B1 (en) * 2000-04-14 2007-07-25 에스. 오. 이. 떼끄 씰리꽁 오 냉쉴라또흐 떼끄놀로지 Method for cutting out at least a thin layer in a substrate or ingot, in particular made of semiconductor materials
JP2002015971A (en) * 2000-06-27 2002-01-18 Matsushita Electric Ind Co Ltd Pattern-forming method and manufacturing apparatus for semiconductor device
FR2811807B1 (en) * 2000-07-12 2003-07-04 Commissariat Energie Atomique METHOD OF CUTTING A BLOCK OF MATERIAL AND FORMING A THIN FILM
US6563133B1 (en) * 2000-08-09 2003-05-13 Ziptronix, Inc. Method of epitaxial-like wafer bonding at low temperature and bonded structure
US6420243B1 (en) * 2000-12-04 2002-07-16 Motorola, Inc. Method for producing SOI wafers by delamination
FR2818010B1 (en) 2000-12-08 2003-09-05 Commissariat Energie Atomique METHOD OF MAKING A THIN LAYER INVOLVING THE INTRODUCTION OF GAS SPECIES
EP1220330B1 (en) * 2000-12-21 2012-03-14 Imec A method of producing a semiconductor layer on a substrate
US6602760B2 (en) 2000-12-21 2003-08-05 Interuniversitair Microelektronica Centrum (Imec) Method of producing a semiconductor layer on a substrate
EP1217663A1 (en) * 2000-12-21 2002-06-26 Interuniversitair Micro-Elektronica Centrum A method of producing a semiconductor layer on a substrate
US7101772B2 (en) * 2000-12-30 2006-09-05 Texas Instruments Incorporated Means for forming SOI
US6774010B2 (en) 2001-01-25 2004-08-10 International Business Machines Corporation Transferable device-containing layer for silicon-on-insulator applications
JP4803884B2 (en) * 2001-01-31 2011-10-26 キヤノン株式会社 Method for manufacturing thin film semiconductor device
JP4993810B2 (en) * 2001-02-16 2012-08-08 株式会社半導体エネルギー研究所 Method for manufacturing semiconductor device
JP5088993B2 (en) * 2001-02-16 2012-12-05 株式会社半導体エネルギー研究所 Method for manufacturing semiconductor device
FR2821697B1 (en) * 2001-03-02 2004-06-25 Commissariat Energie Atomique METHOD OF MANUFACTURING THIN LAYERS ON A SPECIFIC CARRIER AND AN APPLICATION
FR2823596B1 (en) 2001-04-13 2004-08-20 Commissariat Energie Atomique SUBSTRATE OR DISMOUNTABLE STRUCTURE AND METHOD OF MAKING SAME
FR2823599B1 (en) 2001-04-13 2004-12-17 Commissariat Energie Atomique DEMOMTABLE SUBSTRATE WITH CONTROLLED MECHANICAL HOLDING AND METHOD OF MAKING
DE10131249A1 (en) * 2001-06-28 2002-05-23 Wacker Siltronic Halbleitermat Production of a film or a layer of semiconductor material comprises producing structures of repeating recesses on the surface of a semiconductor material
FR2830983B1 (en) * 2001-10-11 2004-05-14 Commissariat Energie Atomique METHOD FOR MANUFACTURING THIN FILMS CONTAINING MICROCOMPONENTS
US8108249B2 (en) * 2001-12-04 2012-01-31 Kimberly-Clark Worldwide, Inc. Business planner
US7309620B2 (en) * 2002-01-11 2007-12-18 The Penn State Research Foundation Use of sacrificial layers in the manufacture of high performance systems on tailored substrates
US20050140283A1 (en) * 2002-02-13 2005-06-30 Lau Silvanus S. Multilayer structure to form an active matrix display having single crystalline drivers over a transmissive substrate
JP4420233B2 (en) * 2002-07-11 2010-02-24 住友電気工業株式会社 Porous semiconductor and method for producing the same
EP1385199A1 (en) 2002-07-24 2004-01-28 IMEC vzw, Interuniversitair Microelectronica Centrum vzw Method for making thin film devices intended for solar cells or SOI application
WO2004019403A2 (en) * 2002-08-26 2004-03-04 S.O.I.Tec Silicon On Insulator Technologies Mechanical recycling of a wafer comprising a buffer layer, after having taken a layer therefrom
US7008857B2 (en) * 2002-08-26 2006-03-07 S.O.I.Tec Silicon On Insulator Technologies S.A. Recycling a wafer comprising a buffer layer, after having separated a thin layer therefrom
TWI242796B (en) * 2002-09-04 2005-11-01 Canon Kk Substrate and manufacturing method therefor
JP2004103600A (en) * 2002-09-04 2004-04-02 Canon Inc Substrate and its manufacturing method
JP2004103855A (en) * 2002-09-10 2004-04-02 Canon Inc Substrate and its manufacturing method
JP2004103946A (en) * 2002-09-11 2004-04-02 Canon Inc Substrate and its manufacturing method
US8187377B2 (en) 2002-10-04 2012-05-29 Silicon Genesis Corporation Non-contact etch annealing of strained layers
US7176108B2 (en) * 2002-11-07 2007-02-13 Soitec Silicon On Insulator Method of detaching a thin film at moderate temperature after co-implantation
FR2847075B1 (en) * 2002-11-07 2005-02-18 Commissariat Energie Atomique PROCESS FOR FORMING A FRAGILE ZONE IN A SUBSTRATE BY CO-IMPLANTATION
FR2848336B1 (en) 2002-12-09 2005-10-28 Commissariat Energie Atomique METHOD FOR PRODUCING A STRESS STRUCTURE FOR DISSOCIATING
FR2849269B1 (en) * 2002-12-20 2005-07-29 Soitec Silicon On Insulator METHOD FOR PRODUCING CAVITIES IN A SILICON PLATE
US20040124088A1 (en) * 2002-12-26 2004-07-01 Canon Kabushiki Kaisha Processing apparatus
US20100133695A1 (en) * 2003-01-12 2010-06-03 Sang-Yun Lee Electronic circuit with embedded memory
US7399681B2 (en) * 2003-02-18 2008-07-15 Corning Incorporated Glass-based SOI structures
US7176528B2 (en) * 2003-02-18 2007-02-13 Corning Incorporated Glass-based SOI structures
CN100472001C (en) * 2003-02-25 2009-03-25 株式会社上睦可 Silicon wafer, process for producing the same and method of growing silicon single crystal
JP4794810B2 (en) * 2003-03-20 2011-10-19 シャープ株式会社 Manufacturing method of semiconductor device
JP2004335662A (en) * 2003-05-06 2004-11-25 Canon Inc Component and method for manufacturing component
EP1620583A4 (en) 2003-05-06 2009-04-22 Canon Kk Semiconductor substrate, semiconductor device, light emitting diode and producing method therefor
US7109092B2 (en) 2003-05-19 2006-09-19 Ziptronix, Inc. Method of room temperature covalent bonding
FR2855910B1 (en) * 2003-06-06 2005-07-15 Commissariat Energie Atomique PROCESS FOR OBTAINING A VERY THIN LAYER BY SELF-CURING BY PROVOQUE SELF-CURING
FR2856192B1 (en) 2003-06-11 2005-07-29 Soitec Silicon On Insulator METHOD FOR PRODUCING HETEROGENEOUS STRUCTURE AND STRUCTURE OBTAINED BY SUCH A METHOD
FR2856844B1 (en) 2003-06-24 2006-02-17 Commissariat Energie Atomique HIGH PERFORMANCE CHIP INTEGRATED CIRCUIT
US8071438B2 (en) * 2003-06-24 2011-12-06 Besang Inc. Semiconductor circuit
US20100190334A1 (en) * 2003-06-24 2010-07-29 Sang-Yun Lee Three-dimensional semiconductor structure and method of manufacturing the same
FR2857953B1 (en) 2003-07-21 2006-01-13 Commissariat Energie Atomique STACKED STRUCTURE, AND METHOD FOR MANUFACTURING THE SAME
US7091108B2 (en) * 2003-09-11 2006-08-15 Intel Corporation Methods and apparatuses for manufacturing ultra thin device layers for integrated circuit devices
US7718231B2 (en) * 2003-09-30 2010-05-18 International Business Machines Corporation Thin buried oxides by low-dose oxygen implantation into modified silicon
US8475693B2 (en) 2003-09-30 2013-07-02 Soitec Methods of making substrate structures having a weakened intermediate layer
US7566482B2 (en) * 2003-09-30 2009-07-28 International Business Machines Corporation SOI by oxidation of porous silicon
FR2860249B1 (en) * 2003-09-30 2005-12-09 Michel Bruel METHOD FOR MANUFACTURING PLATE-LIKE STRUCTURE, ESPECIALLY SILICON, PROCESS APPLICATION, AND PLATE-LIKE STRUCTURE, PARTICULARLY SILICON
FR2861497B1 (en) 2003-10-28 2006-02-10 Soitec Silicon On Insulator METHOD FOR CATASTROPHIC TRANSFER OF A FINE LAYER AFTER CO-IMPLANTATION
US7542197B2 (en) * 2003-11-01 2009-06-02 Silicon Quest Kabushiki-Kaisha Spatial light modulator featured with an anti-reflective structure
AU2003297191A1 (en) * 2003-12-16 2005-07-14 International Business Machines Corporation Contoured insulator layer of silicon-on-onsulator wafers and process of manufacture
US7772087B2 (en) * 2003-12-19 2010-08-10 Commissariat A L'energie Atomique Method of catastrophic transfer of a thin film after co-implantation
US7262466B2 (en) 2004-08-18 2007-08-28 Corning Incorporated Strained semiconductor-on-insulator structures and methods for making strained semiconductor-on-insulator structures
CN101091251B (en) * 2004-08-18 2011-03-16 康宁股份有限公司 Semiconductor-on-insulator structures containing high strain glass/glass-ceramic
EP1667223B1 (en) 2004-11-09 2009-01-07 S.O.I. Tec Silicon on Insulator Technologies S.A. Method for manufacturing compound material wafers
US7402520B2 (en) * 2004-11-26 2008-07-22 Applied Materials, Inc. Edge removal of silicon-on-insulator transfer wafer
US7378331B2 (en) * 2004-12-29 2008-05-27 Intel Corporation Methods of vertically stacking wafers using porous silicon
US20110143506A1 (en) * 2009-12-10 2011-06-16 Sang-Yun Lee Method for fabricating a semiconductor memory device
US8367524B2 (en) * 2005-03-29 2013-02-05 Sang-Yun Lee Three-dimensional integrated circuit structure
US7410883B2 (en) * 2005-04-13 2008-08-12 Corning Incorporated Glass-based semiconductor on insulator structures and methods of making same
US20060240275A1 (en) * 2005-04-25 2006-10-26 Gadkaree Kishor P Flexible display substrates
FR2886051B1 (en) * 2005-05-20 2007-08-10 Commissariat Energie Atomique METHOD FOR DETACHING THIN FILM
FR2889887B1 (en) 2005-08-16 2007-11-09 Commissariat Energie Atomique METHOD FOR DEFERING A THIN LAYER ON A SUPPORT
US7268051B2 (en) * 2005-08-26 2007-09-11 Corning Incorporated Semiconductor on glass insulator with deposited barrier layer
CN100391826C (en) * 2005-09-09 2008-06-04 华东师范大学 Silicon microchannel production method
FR2891281B1 (en) 2005-09-28 2007-12-28 Commissariat Energie Atomique METHOD FOR MANUFACTURING A THIN FILM ELEMENT
US7456080B2 (en) * 2005-12-19 2008-11-25 Corning Incorporated Semiconductor on glass insulator made using improved ion implantation process
EP1981065B1 (en) * 2005-12-27 2014-12-03 Shin-Etsu Chemical Company, Ltd. Process for producing soi wafer
DE102006007293B4 (en) * 2006-01-31 2023-04-06 OSRAM Opto Semiconductors Gesellschaft mit beschränkter Haftung Method for producing a quasi-substrate wafer and a semiconductor body produced using such a quasi-substrate wafer
DE102006013313A1 (en) * 2006-03-21 2007-09-27 Institut Für Solarenergieforschung Gmbh A method of producing a selectively doped region in a semiconductor layer using out-diffusion and corresponding semiconductor device
FR2899378B1 (en) 2006-03-29 2008-06-27 Commissariat Energie Atomique METHOD FOR DETACHING A THIN FILM BY FUSION OF PRECIPITS
DE102006028783B4 (en) * 2006-06-23 2014-09-18 Robert Bosch Gmbh Porous silicon body with layered structure, process for its preparation and use thereof
US7811900B2 (en) 2006-09-08 2010-10-12 Silicon Genesis Corporation Method and structure for fabricating solar cells using a thick layer transfer process
US8293619B2 (en) 2008-08-28 2012-10-23 Silicon Genesis Corporation Layer transfer of films utilizing controlled propagation
US9362439B2 (en) 2008-05-07 2016-06-07 Silicon Genesis Corporation Layer transfer of films utilizing controlled shear region
US8993410B2 (en) 2006-09-08 2015-03-31 Silicon Genesis Corporation Substrate cleaving under controlled stress conditions
TWI450387B (en) * 2006-09-29 2014-08-21 Semiconductor Energy Lab Method for manufacturing semiconductor device
US8137417B2 (en) 2006-09-29 2012-03-20 Semiconductor Energy Laboratory Co., Ltd. Peeling apparatus and manufacturing apparatus of semiconductor device
US7642934B2 (en) * 2006-11-10 2010-01-05 Research In Motion Limited Method of mapping a traditional touchtone keypad on a handheld electronic device and associated apparatus
JP4770706B2 (en) * 2006-11-13 2011-09-14 ソニー株式会社 Thin film semiconductor manufacturing method
FR2910179B1 (en) 2006-12-19 2009-03-13 Commissariat Energie Atomique METHOD FOR MANUFACTURING THIN LAYERS OF GaN BY IMPLANTATION AND RECYCLING OF A STARTING SUBSTRATE
JP2007201502A (en) * 2007-04-20 2007-08-09 Semiconductor Energy Lab Co Ltd Semiconductor device and fabricating method thereof
EP1986230A2 (en) * 2007-04-25 2008-10-29 Semiconductor Energy Laboratory Co., Ltd. Method of manufacturing SOI substrate and method of manufacturing semiconductor device
JP5463017B2 (en) * 2007-09-21 2014-04-09 株式会社半導体エネルギー研究所 Substrate manufacturing method
FR2922681A1 (en) * 2007-10-23 2009-04-24 Soitec Silicon On Insulator METHOD FOR DETACHING A SUBSTRATE
JP5248994B2 (en) * 2007-11-30 2013-07-31 株式会社半導体エネルギー研究所 Method for manufacturing photoelectric conversion device
JP5248995B2 (en) * 2007-11-30 2013-07-31 株式会社半導体エネルギー研究所 Method for manufacturing photoelectric conversion device
FR2925221B1 (en) 2007-12-17 2010-02-19 Commissariat Energie Atomique METHOD FOR TRANSFERRING A THIN LAYER
US8288184B2 (en) * 2007-12-18 2012-10-16 Sharp Kabushiki Kaisha Production method of semiconductor device and semiconductor device
JP5572307B2 (en) * 2007-12-28 2014-08-13 株式会社半導体エネルギー研究所 Method for manufacturing photoelectric conversion device
FR2929444B1 (en) * 2008-03-31 2010-08-20 Commissariat Energie Atomique METHOD FOR MANUFACTURING A MICROELECTRONIC STRUCTURE OF THE SEMICONDUCTOR TYPE ON INSULATION AND WITH DIFFERENTIATED PATTERNS, AND STRUCTURE THUS OBTAINED
US7749884B2 (en) * 2008-05-06 2010-07-06 Astrowatt, Inc. Method of forming an electronic device using a separation-enhancing species
US8623137B1 (en) * 2008-05-07 2014-01-07 Silicon Genesis Corporation Method and device for slicing a shaped silicon ingot using layer transfer
US8076215B2 (en) * 2008-05-17 2011-12-13 Astrowatt, Inc. Method of forming an electronic device using a separation technique
US7951656B2 (en) * 2008-06-06 2011-05-31 Semiconductor Energy Laboratory Co., Ltd. Method for manufacturing semiconductor device
US8338218B2 (en) * 2008-06-26 2012-12-25 Semiconductor Energy Laboratory Co., Ltd. Photoelectric conversion device module and manufacturing method of the photoelectric conversion device module
EP2157602A1 (en) * 2008-08-20 2010-02-24 Max-Planck-Gesellschaft zur Förderung der Wissenschaften e.V. A method of manufacturing a plurality of fabrication wafers
US8330126B2 (en) 2008-08-25 2012-12-11 Silicon Genesis Corporation Race track configuration and method for wafering silicon solar substrates
SG160302A1 (en) * 2008-09-29 2010-04-29 Semiconductor Energy Lab Method for manufacturing semiconductor substrate
US8871610B2 (en) * 2008-10-02 2014-10-28 Semiconductor Energy Laboratory Co., Ltd. Method for manufacturing SOI substrate
JP2010114409A (en) * 2008-10-10 2010-05-20 Sony Corp Soi substrate and method for manufacturing the same, solid-state image pickup device and method for manufacturing the same, and image pickup device
JP4489823B2 (en) * 2008-10-29 2010-06-23 株式会社半導体エネルギー研究所 Method for manufacturing semiconductor device
JP5478199B2 (en) * 2008-11-13 2014-04-23 株式会社半導体エネルギー研究所 Method for manufacturing semiconductor device
JP5586920B2 (en) * 2008-11-20 2014-09-10 株式会社半導体エネルギー研究所 Method for manufacturing flexible semiconductor device
US8427200B2 (en) 2009-04-14 2013-04-23 Monolithic 3D Inc. 3D semiconductor device
US8405420B2 (en) 2009-04-14 2013-03-26 Monolithic 3D Inc. System comprising a semiconductor device and structure
US8373439B2 (en) 2009-04-14 2013-02-12 Monolithic 3D Inc. 3D semiconductor device
US9577642B2 (en) 2009-04-14 2017-02-21 Monolithic 3D Inc. Method to form a 3D semiconductor device
US8058137B1 (en) 2009-04-14 2011-11-15 Monolithic 3D Inc. Method for fabrication of a semiconductor device and structure
US8384426B2 (en) 2009-04-14 2013-02-26 Monolithic 3D Inc. Semiconductor device and structure
US8378715B2 (en) 2009-04-14 2013-02-19 Monolithic 3D Inc. Method to construct systems
US8669778B1 (en) 2009-04-14 2014-03-11 Monolithic 3D Inc. Method for design and manufacturing of a 3D semiconductor device
US9509313B2 (en) 2009-04-14 2016-11-29 Monolithic 3D Inc. 3D semiconductor device
US8754533B2 (en) 2009-04-14 2014-06-17 Monolithic 3D Inc. Monolithic three-dimensional semiconductor device and structure
US8395191B2 (en) 2009-10-12 2013-03-12 Monolithic 3D Inc. Semiconductor device and structure
US8362800B2 (en) 2010-10-13 2013-01-29 Monolithic 3D Inc. 3D semiconductor device including field repairable logics
US7986042B2 (en) 2009-04-14 2011-07-26 Monolithic 3D Inc. Method for fabrication of a semiconductor device and structure
US9711407B2 (en) 2009-04-14 2017-07-18 Monolithic 3D Inc. Method of manufacturing a three dimensional integrated circuit by transfer of a mono-crystalline layer
US8362482B2 (en) 2009-04-14 2013-01-29 Monolithic 3D Inc. Semiconductor device and structure
US8329557B2 (en) 2009-05-13 2012-12-11 Silicon Genesis Corporation Techniques for forming thin films by implantation with reduced channeling
US20100310775A1 (en) * 2009-06-09 2010-12-09 International Business Machines Corporation Spalling for a Semiconductor Substrate
US8633097B2 (en) * 2009-06-09 2014-01-21 International Business Machines Corporation Single-junction photovoltaic cell
US20110048517A1 (en) * 2009-06-09 2011-03-03 International Business Machines Corporation Multijunction Photovoltaic Cell Fabrication
US8703521B2 (en) 2009-06-09 2014-04-22 International Business Machines Corporation Multijunction photovoltaic cell fabrication
US8802477B2 (en) * 2009-06-09 2014-08-12 International Business Machines Corporation Heterojunction III-V photovoltaic cell fabrication
FR2947098A1 (en) 2009-06-18 2010-12-24 Commissariat Energie Atomique METHOD OF TRANSFERRING A THIN LAYER TO A TARGET SUBSTRATE HAVING A THERMAL EXPANSION COEFFICIENT DIFFERENT FROM THAT OF THE THIN LAYER
US9847243B2 (en) 2009-08-27 2017-12-19 Corning Incorporated Debonding a glass substrate from carrier using ultrasonic wave
US10366970B2 (en) 2009-10-12 2019-07-30 Monolithic 3D Inc. 3D semiconductor device and structure
US10388863B2 (en) 2009-10-12 2019-08-20 Monolithic 3D Inc. 3D memory device and structure
US8581349B1 (en) 2011-05-02 2013-11-12 Monolithic 3D Inc. 3D memory semiconductor device and structure
US10043781B2 (en) 2009-10-12 2018-08-07 Monolithic 3D Inc. 3D semiconductor device and structure
US8536023B2 (en) 2010-11-22 2013-09-17 Monolithic 3D Inc. Method of manufacturing a semiconductor device and structure
US8476145B2 (en) 2010-10-13 2013-07-02 Monolithic 3D Inc. Method of fabricating a semiconductor device and structure
US8742476B1 (en) 2012-11-27 2014-06-03 Monolithic 3D Inc. Semiconductor device and structure
US9099424B1 (en) 2012-08-10 2015-08-04 Monolithic 3D Inc. Semiconductor system, device and structure with heat removal
US8450804B2 (en) 2011-03-06 2013-05-28 Monolithic 3D Inc. Semiconductor device and structure for heat removal
US11374118B2 (en) 2009-10-12 2022-06-28 Monolithic 3D Inc. Method to form a 3D integrated circuit
US10157909B2 (en) 2009-10-12 2018-12-18 Monolithic 3D Inc. 3D semiconductor device and structure
US8294159B2 (en) 2009-10-12 2012-10-23 Monolithic 3D Inc. Method for fabrication of a semiconductor device and structure
US10910364B2 (en) 2009-10-12 2021-02-02 Monolitaic 3D Inc. 3D semiconductor device
US11018133B2 (en) 2009-10-12 2021-05-25 Monolithic 3D Inc. 3D integrated circuit
US10354995B2 (en) 2009-10-12 2019-07-16 Monolithic 3D Inc. Semiconductor memory device and structure
JP4642130B2 (en) * 2009-10-30 2011-03-02 株式会社半導体エネルギー研究所 Method for forming single crystal silicon thin film on glass substrate
US7986022B2 (en) * 2009-11-19 2011-07-26 International Business Machines Corporation Semispherical integrated circuit structures
JP5706670B2 (en) 2009-11-24 2015-04-22 株式会社半導体エネルギー研究所 Method for manufacturing SOI substrate
US8461035B1 (en) 2010-09-30 2013-06-11 Monolithic 3D Inc. Method for fabrication of a semiconductor device and structure
US8492886B2 (en) 2010-02-16 2013-07-23 Monolithic 3D Inc 3D integrated circuit with logic
US8373230B1 (en) 2010-10-13 2013-02-12 Monolithic 3D Inc. Method for fabrication of a semiconductor device and structure
US8026521B1 (en) 2010-10-11 2011-09-27 Monolithic 3D Inc. Semiconductor device and structure
US9099526B2 (en) 2010-02-16 2015-08-04 Monolithic 3D Inc. Integrated circuit device and structure
US8541819B1 (en) 2010-12-09 2013-09-24 Monolithic 3D Inc. Semiconductor device and structure
US20110207306A1 (en) * 2010-02-22 2011-08-25 Sarko Cherekdjian Semiconductor structure made using improved ion implantation process
US8343858B2 (en) * 2010-03-02 2013-01-01 Semiconductor Energy Laboratory Co., Ltd. Method for manufacturing microcrystalline semiconductor film and method for manufacturing semiconductor device
KR101134819B1 (en) 2010-07-02 2012-04-13 이상윤 Method for fabricating semiconductor memory
US8901613B2 (en) 2011-03-06 2014-12-02 Monolithic 3D Inc. Semiconductor device and structure for heat removal
US9953925B2 (en) 2011-06-28 2018-04-24 Monolithic 3D Inc. Semiconductor system and device
US9219005B2 (en) 2011-06-28 2015-12-22 Monolithic 3D Inc. Semiconductor system and device
US8642416B2 (en) 2010-07-30 2014-02-04 Monolithic 3D Inc. Method of forming three dimensional integrated circuit devices using layer transfer technique
US10217667B2 (en) 2011-06-28 2019-02-26 Monolithic 3D Inc. 3D semiconductor device, fabrication method and system
DE102011050136A1 (en) 2010-09-03 2012-03-08 Schott Solar Ag Process for the wet-chemical etching of a silicon layer
JP4693938B2 (en) * 2010-09-16 2011-06-01 株式会社半導体エネルギー研究所 Method for manufacturing semiconductor device
US8163581B1 (en) 2010-10-13 2012-04-24 Monolith IC 3D Semiconductor and optoelectronic devices
US8273610B2 (en) 2010-11-18 2012-09-25 Monolithic 3D Inc. Method of constructing a semiconductor device and structure
US10497713B2 (en) 2010-11-18 2019-12-03 Monolithic 3D Inc. 3D semiconductor memory device and structure
US11482440B2 (en) 2010-12-16 2022-10-25 Monolithic 3D Inc. 3D semiconductor device and structure with a built-in test circuit for repairing faulty circuits
US11469271B2 (en) 2010-10-11 2022-10-11 Monolithic 3D Inc. Method to produce 3D semiconductor devices and structures with memory
US11257867B1 (en) 2010-10-11 2022-02-22 Monolithic 3D Inc. 3D semiconductor device and structure with oxide bonds
US10290682B2 (en) 2010-10-11 2019-05-14 Monolithic 3D Inc. 3D IC semiconductor device and structure with stacked memory
US11600667B1 (en) 2010-10-11 2023-03-07 Monolithic 3D Inc. Method to produce 3D semiconductor devices and structures with memory
US11158674B2 (en) 2010-10-11 2021-10-26 Monolithic 3D Inc. Method to produce a 3D semiconductor device and structure
US11024673B1 (en) 2010-10-11 2021-06-01 Monolithic 3D Inc. 3D semiconductor device and structure
US8114757B1 (en) 2010-10-11 2012-02-14 Monolithic 3D Inc. Semiconductor device and structure
US11018191B1 (en) 2010-10-11 2021-05-25 Monolithic 3D Inc. 3D semiconductor device and structure
US11227897B2 (en) 2010-10-11 2022-01-18 Monolithic 3D Inc. Method for producing a 3D semiconductor memory device and structure
US11315980B1 (en) 2010-10-11 2022-04-26 Monolithic 3D Inc. 3D semiconductor device and structure with transistors
US10896931B1 (en) 2010-10-11 2021-01-19 Monolithic 3D Inc. 3D semiconductor device and structure
US11133344B2 (en) 2010-10-13 2021-09-28 Monolithic 3D Inc. Multilevel semiconductor device and structure with image sensors
US11164898B2 (en) 2010-10-13 2021-11-02 Monolithic 3D Inc. Multilevel semiconductor device and structure
US10679977B2 (en) 2010-10-13 2020-06-09 Monolithic 3D Inc. 3D microdisplay device and structure
US8379458B1 (en) 2010-10-13 2013-02-19 Monolithic 3D Inc. Semiconductor device and structure
US11327227B2 (en) 2010-10-13 2022-05-10 Monolithic 3D Inc. Multilevel semiconductor device and structure with electromagnetic modulators
US10833108B2 (en) 2010-10-13 2020-11-10 Monolithic 3D Inc. 3D microdisplay device and structure
US10998374B1 (en) 2010-10-13 2021-05-04 Monolithic 3D Inc. Multilevel semiconductor device and structure
US11855114B2 (en) 2010-10-13 2023-12-26 Monolithic 3D Inc. Multilevel semiconductor device and structure with image sensors and wafer bonding
US11929372B2 (en) 2010-10-13 2024-03-12 Monolithic 3D Inc. Multilevel semiconductor device and structure with image sensors and wafer bonding
US11063071B1 (en) 2010-10-13 2021-07-13 Monolithic 3D Inc. Multilevel semiconductor device and structure with waveguides
US11694922B2 (en) 2010-10-13 2023-07-04 Monolithic 3D Inc. Multilevel semiconductor device and structure with oxide bonding
US11869915B2 (en) 2010-10-13 2024-01-09 Monolithic 3D Inc. Multilevel semiconductor device and structure with image sensors and wafer bonding
US11437368B2 (en) 2010-10-13 2022-09-06 Monolithic 3D Inc. Multilevel semiconductor device and structure with oxide bonding
US9197804B1 (en) 2011-10-14 2015-11-24 Monolithic 3D Inc. Semiconductor and optoelectronic devices
US11043523B1 (en) 2010-10-13 2021-06-22 Monolithic 3D Inc. Multilevel semiconductor device and structure with image sensors
US11404466B2 (en) 2010-10-13 2022-08-02 Monolithic 3D Inc. Multilevel semiconductor device and structure with image sensors
US11163112B2 (en) 2010-10-13 2021-11-02 Monolithic 3D Inc. Multilevel semiconductor device and structure with electromagnetic modulators
US10978501B1 (en) 2010-10-13 2021-04-13 Monolithic 3D Inc. Multilevel semiconductor device and structure with waveguides
US11855100B2 (en) 2010-10-13 2023-12-26 Monolithic 3D Inc. Multilevel semiconductor device and structure with oxide bonding
US10943934B2 (en) 2010-10-13 2021-03-09 Monolithic 3D Inc. Multilevel semiconductor device and structure
US11605663B2 (en) 2010-10-13 2023-03-14 Monolithic 3D Inc. Multilevel semiconductor device and structure with image sensors and wafer bonding
US11508605B2 (en) 2010-11-18 2022-11-22 Monolithic 3D Inc. 3D semiconductor memory device and structure
US11211279B2 (en) 2010-11-18 2021-12-28 Monolithic 3D Inc. Method for processing a 3D integrated circuit and structure
US11804396B2 (en) 2010-11-18 2023-10-31 Monolithic 3D Inc. Methods for producing a 3D semiconductor device and structure with memory cells and multiple metal layers
US11901210B2 (en) 2010-11-18 2024-02-13 Monolithic 3D Inc. 3D semiconductor device and structure with memory
US11923230B1 (en) 2010-11-18 2024-03-05 Monolithic 3D Inc. 3D semiconductor device and structure with bonding
US11784082B2 (en) 2010-11-18 2023-10-10 Monolithic 3D Inc. 3D semiconductor device and structure with bonding
US11031275B2 (en) 2010-11-18 2021-06-08 Monolithic 3D Inc. 3D semiconductor device and structure with memory
US11482439B2 (en) 2010-11-18 2022-10-25 Monolithic 3D Inc. Methods for producing a 3D semiconductor memory device comprising charge trap junction-less transistors
US11355381B2 (en) 2010-11-18 2022-06-07 Monolithic 3D Inc. 3D semiconductor memory device and structure
US11164770B1 (en) 2010-11-18 2021-11-02 Monolithic 3D Inc. Method for producing a 3D semiconductor memory device and structure
US11121021B2 (en) 2010-11-18 2021-09-14 Monolithic 3D Inc. 3D semiconductor device and structure
US11482438B2 (en) 2010-11-18 2022-10-25 Monolithic 3D Inc. Methods for producing a 3D semiconductor memory device and structure
US11854857B1 (en) 2010-11-18 2023-12-26 Monolithic 3D Inc. Methods for producing a 3D semiconductor device and structure with memory cells and multiple metal layers
US11004719B1 (en) 2010-11-18 2021-05-11 Monolithic 3D Inc. Methods for producing a 3D semiconductor memory device and structure
US11018042B1 (en) 2010-11-18 2021-05-25 Monolithic 3D Inc. 3D semiconductor memory device and structure
US11094576B1 (en) 2010-11-18 2021-08-17 Monolithic 3D Inc. Methods for producing a 3D semiconductor memory device and structure
US11735462B2 (en) 2010-11-18 2023-08-22 Monolithic 3D Inc. 3D semiconductor device and structure with single-crystal layers
US11107721B2 (en) 2010-11-18 2021-08-31 Monolithic 3D Inc. 3D semiconductor device and structure with NAND logic
US11495484B2 (en) 2010-11-18 2022-11-08 Monolithic 3D Inc. 3D semiconductor devices and structures with at least two single-crystal layers
US11569117B2 (en) 2010-11-18 2023-01-31 Monolithic 3D Inc. 3D semiconductor device and structure with single-crystal layers
US11521888B2 (en) 2010-11-18 2022-12-06 Monolithic 3D Inc. 3D semiconductor device and structure with high-k metal gate transistors
US11443971B2 (en) 2010-11-18 2022-09-13 Monolithic 3D Inc. 3D semiconductor device and structure with memory
US11862503B2 (en) 2010-11-18 2024-01-02 Monolithic 3D Inc. Method for producing a 3D semiconductor device and structure with memory cells and multiple metal layers
US11355380B2 (en) 2010-11-18 2022-06-07 Monolithic 3D Inc. Methods for producing 3D semiconductor memory device and structure utilizing alignment marks
US11610802B2 (en) 2010-11-18 2023-03-21 Monolithic 3D Inc. Method for producing a 3D semiconductor device and structure with single crystal transistors and metal gate electrodes
US11615977B2 (en) 2010-11-18 2023-03-28 Monolithic 3D Inc. 3D semiconductor memory device and structure
US8558195B2 (en) 2010-11-19 2013-10-15 Corning Incorporated Semiconductor structure made using improved pseudo-simultaneous multiple ion implantation process
US8196546B1 (en) 2010-11-19 2012-06-12 Corning Incorporated Semiconductor structure made using improved multiple ion implantation process
US8008175B1 (en) 2010-11-19 2011-08-30 Coring Incorporated Semiconductor structure made using improved simultaneous multiple ion implantation process
US8992746B2 (en) 2010-12-02 2015-03-31 Dainippon Screen Mfg. Co., Ltd. Anodizing apparatus
US8975670B2 (en) 2011-03-06 2015-03-10 Monolithic 3D Inc. Semiconductor device and structure for heat removal
JP5360127B2 (en) * 2011-05-02 2013-12-04 ソニー株式会社 Thin film semiconductor manufacturing method
US8927318B2 (en) 2011-06-14 2015-01-06 International Business Machines Corporation Spalling methods to form multi-junction photovoltaic structure
US10388568B2 (en) 2011-06-28 2019-08-20 Monolithic 3D Inc. 3D semiconductor device and system
US8883612B2 (en) 2011-09-12 2014-11-11 Infineon Technologies Austria Ag Method for manufacturing a semiconductor device
US8687399B2 (en) 2011-10-02 2014-04-01 Monolithic 3D Inc. Semiconductor device and structure
US9029173B2 (en) 2011-10-18 2015-05-12 Monolithic 3D Inc. Method for fabrication of a semiconductor device and structure
US9000557B2 (en) 2012-03-17 2015-04-07 Zvi Or-Bach Semiconductor device and structure
US11476181B1 (en) 2012-04-09 2022-10-18 Monolithic 3D Inc. 3D semiconductor device and structure with metal layers
US11694944B1 (en) 2012-04-09 2023-07-04 Monolithic 3D Inc. 3D semiconductor device and structure with metal layers and a connective path
US11616004B1 (en) 2012-04-09 2023-03-28 Monolithic 3D Inc. 3D semiconductor device and structure with metal layers and a connective path
US10600888B2 (en) 2012-04-09 2020-03-24 Monolithic 3D Inc. 3D semiconductor device
US11410912B2 (en) 2012-04-09 2022-08-09 Monolithic 3D Inc. 3D semiconductor device with vias and isolation layers
US8557632B1 (en) 2012-04-09 2013-10-15 Monolithic 3D Inc. Method for fabrication of a semiconductor device and structure
US11735501B1 (en) 2012-04-09 2023-08-22 Monolithic 3D Inc. 3D semiconductor device and structure with metal layers and a connective path
US11164811B2 (en) 2012-04-09 2021-11-02 Monolithic 3D Inc. 3D semiconductor device with isolation layers and oxide-to-oxide bonding
US11088050B2 (en) 2012-04-09 2021-08-10 Monolithic 3D Inc. 3D semiconductor device with isolation layers
US11594473B2 (en) 2012-04-09 2023-02-28 Monolithic 3D Inc. 3D semiconductor device and structure with metal layers and a connective path
US11881443B2 (en) 2012-04-09 2024-01-23 Monolithic 3D Inc. 3D semiconductor device and structure with metal layers and a connective path
FR2995444B1 (en) * 2012-09-10 2016-11-25 Soitec Silicon On Insulator METHOD FOR DETACHING A LAYER
US8946052B2 (en) * 2012-09-26 2015-02-03 Sandia Corporation Processes for multi-layer devices utilizing layer transfer
US8574929B1 (en) 2012-11-16 2013-11-05 Monolithic 3D Inc. Method to form a 3D semiconductor device and structure
US8686428B1 (en) 2012-11-16 2014-04-01 Monolithic 3D Inc. Semiconductor device and structure
US11018116B2 (en) 2012-12-22 2021-05-25 Monolithic 3D Inc. Method to form a 3D semiconductor device and structure
US11063024B1 (en) 2012-12-22 2021-07-13 Monlithic 3D Inc. Method to form a 3D semiconductor device and structure
US11916045B2 (en) 2012-12-22 2024-02-27 Monolithic 3D Inc. 3D semiconductor device and structure with metal layers
US11784169B2 (en) 2012-12-22 2023-10-10 Monolithic 3D Inc. 3D semiconductor device and structure with metal layers
US11309292B2 (en) 2012-12-22 2022-04-19 Monolithic 3D Inc. 3D semiconductor device and structure with metal layers
US8674470B1 (en) 2012-12-22 2014-03-18 Monolithic 3D Inc. Semiconductor device and structure
US11217565B2 (en) 2012-12-22 2022-01-04 Monolithic 3D Inc. Method to form a 3D semiconductor device and structure
US11004694B1 (en) 2012-12-29 2021-05-11 Monolithic 3D Inc. 3D semiconductor device and structure
US10651054B2 (en) 2012-12-29 2020-05-12 Monolithic 3D Inc. 3D semiconductor device and structure
US11430668B2 (en) 2012-12-29 2022-08-30 Monolithic 3D Inc. 3D semiconductor device and structure with bonding
US9871034B1 (en) 2012-12-29 2018-01-16 Monolithic 3D Inc. Semiconductor device and structure
US10892169B2 (en) 2012-12-29 2021-01-12 Monolithic 3D Inc. 3D semiconductor device and structure
US10903089B1 (en) 2012-12-29 2021-01-26 Monolithic 3D Inc. 3D semiconductor device and structure
US11430667B2 (en) 2012-12-29 2022-08-30 Monolithic 3D Inc. 3D semiconductor device and structure with bonding
US10115663B2 (en) 2012-12-29 2018-10-30 Monolithic 3D Inc. 3D semiconductor device and structure
US9385058B1 (en) 2012-12-29 2016-07-05 Monolithic 3D Inc. Semiconductor device and structure
US11087995B1 (en) 2012-12-29 2021-08-10 Monolithic 3D Inc. 3D semiconductor device and structure
US11177140B2 (en) 2012-12-29 2021-11-16 Monolithic 3D Inc. 3D semiconductor device and structure
US10600657B2 (en) 2012-12-29 2020-03-24 Monolithic 3D Inc 3D semiconductor device and structure
FR3002684B1 (en) * 2013-02-25 2015-04-10 Centre Nat Rech Scient METHOD FOR FORMING A PATTERN IN A SAMPLE
US10325651B2 (en) 2013-03-11 2019-06-18 Monolithic 3D Inc. 3D semiconductor device with stacked memory
US8902663B1 (en) 2013-03-11 2014-12-02 Monolithic 3D Inc. Method of maintaining a memory state
US11869965B2 (en) 2013-03-11 2024-01-09 Monolithic 3D Inc. 3D semiconductor device and structure with metal layers and memory cells
US10840239B2 (en) 2014-08-26 2020-11-17 Monolithic 3D Inc. 3D semiconductor device and structure
US11398569B2 (en) 2013-03-12 2022-07-26 Monolithic 3D Inc. 3D semiconductor device and structure
US11088130B2 (en) 2014-01-28 2021-08-10 Monolithic 3D Inc. 3D semiconductor device and structure
US11923374B2 (en) 2013-03-12 2024-03-05 Monolithic 3D Inc. 3D semiconductor device and structure with metal layers
US8994404B1 (en) 2013-03-12 2015-03-31 Monolithic 3D Inc. Semiconductor device and structure
US9117749B1 (en) 2013-03-15 2015-08-25 Monolithic 3D Inc. Semiconductor device and structure
US10224279B2 (en) 2013-03-15 2019-03-05 Monolithic 3D Inc. Semiconductor device and structure
US9021414B1 (en) 2013-04-15 2015-04-28 Monolithic 3D Inc. Automation for monolithic 3D devices
US11270055B1 (en) 2013-04-15 2022-03-08 Monolithic 3D Inc. Automation for monolithic 3D devices
US11720736B2 (en) 2013-04-15 2023-08-08 Monolithic 3D Inc. Automation methods for 3D integrated circuits and devices
US11030371B2 (en) 2013-04-15 2021-06-08 Monolithic 3D Inc. Automation for monolithic 3D devices
US11341309B1 (en) 2013-04-15 2022-05-24 Monolithic 3D Inc. Automation for monolithic 3D devices
US11574109B1 (en) 2013-04-15 2023-02-07 Monolithic 3D Inc Automation methods for 3D integrated circuits and devices
US11487928B2 (en) 2013-04-15 2022-11-01 Monolithic 3D Inc. Automation for monolithic 3D devices
WO2015019971A1 (en) 2013-08-06 2015-02-12 Semiconductor Energy Laboratory Co., Ltd. Peeling method
TWI777433B (en) 2013-09-06 2022-09-11 日商半導體能源研究所股份有限公司 Light-emitting device and method for manufacturing light-emitting device
US9217206B2 (en) * 2013-09-27 2015-12-22 Sunpower Corporation Enhanced porosification
US9937698B2 (en) 2013-11-06 2018-04-10 Semiconductor Energy Laboratory Co., Ltd. Peeling method and light-emitting device
US10297586B2 (en) 2015-03-09 2019-05-21 Monolithic 3D Inc. Methods for processing a 3D semiconductor device
US11031394B1 (en) 2014-01-28 2021-06-08 Monolithic 3D Inc. 3D semiconductor device and structure
US11107808B1 (en) 2014-01-28 2021-08-31 Monolithic 3D Inc. 3D semiconductor device and structure
US9230991B2 (en) * 2014-04-16 2016-01-05 Stmicroelectronics, Inc. Method to co-integrate oppositely strained semiconductor devices on a same substrate
US9799829B2 (en) 2014-07-25 2017-10-24 Semiconductor Energy Laboratory Co., Ltd. Separation method, light-emitting device, module, and electronic device
US10381328B2 (en) 2015-04-19 2019-08-13 Monolithic 3D Inc. Semiconductor device and structure
US10825779B2 (en) 2015-04-19 2020-11-03 Monolithic 3D Inc. 3D semiconductor device and structure
US11011507B1 (en) 2015-04-19 2021-05-18 Monolithic 3D Inc. 3D semiconductor device and structure
US11056468B1 (en) 2015-04-19 2021-07-06 Monolithic 3D Inc. 3D semiconductor device and structure
US9892910B2 (en) 2015-05-15 2018-02-13 International Business Machines Corporation Method and structure for forming a dense array of single crystalline semiconductor nanocrystals
FR3041364B1 (en) 2015-09-18 2017-10-06 Soitec Silicon On Insulator PROCESS FOR TRANSFERRING SINGLE CRYSTAL PAVES
US10515981B2 (en) 2015-09-21 2019-12-24 Monolithic 3D Inc. Multilevel semiconductor device and structure with memory
US10522225B1 (en) 2015-10-02 2019-12-31 Monolithic 3D Inc. Semiconductor device with non-volatile memory
US10418369B2 (en) 2015-10-24 2019-09-17 Monolithic 3D Inc. Multi-level semiconductor memory device and structure
US11114464B2 (en) 2015-10-24 2021-09-07 Monolithic 3D Inc. 3D semiconductor device and structure
US11296115B1 (en) 2015-10-24 2022-04-05 Monolithic 3D Inc. 3D semiconductor device and structure
US10847540B2 (en) 2015-10-24 2020-11-24 Monolithic 3D Inc. 3D semiconductor memory device and structure
US11114427B2 (en) 2015-11-07 2021-09-07 Monolithic 3D Inc. 3D semiconductor processor and memory device and structure
CN105226187B (en) * 2015-11-15 2018-01-30 河北工业大学 Film crystal silicon perovskite heterojunction solar battery and preparation method thereof
US10259207B2 (en) 2016-01-26 2019-04-16 Semiconductor Energy Laboratory Co., Ltd. Method for forming separation starting point and separation method
DE102016112976A1 (en) * 2016-07-14 2018-01-18 Infineon Technologies Ag Method for processing a wafer and layer stack
US11329059B1 (en) 2016-10-10 2022-05-10 Monolithic 3D Inc. 3D memory devices and structures with thinned single crystal substrates
US11812620B2 (en) 2016-10-10 2023-11-07 Monolithic 3D Inc. 3D DRAM memory devices and structures with control circuits
US11711928B2 (en) 2016-10-10 2023-07-25 Monolithic 3D Inc. 3D memory devices and structures with control circuits
US11930648B1 (en) 2016-10-10 2024-03-12 Monolithic 3D Inc. 3D memory devices and structures with metal layers
US11869591B2 (en) 2016-10-10 2024-01-09 Monolithic 3D Inc. 3D memory devices and structures with control circuits
US11251149B2 (en) 2016-10-10 2022-02-15 Monolithic 3D Inc. 3D memory device and structure
FR3077923B1 (en) 2018-02-12 2021-07-16 Soitec Silicon On Insulator METHOD OF MANUFACTURING A SEMICONDUCTOR TYPE STRUCTURE ON INSULATION BY LAYER TRANSFER
CN109786306A (en) * 2018-03-22 2019-05-21 苏州捷芯威半导体有限公司 Method, semi-conductor device manufacturing method and substrate support structure
FR3079532B1 (en) * 2018-03-28 2022-03-25 Soitec Silicon On Insulator METHOD FOR MANUFACTURING A MONOCRYSTALLINE LAYER OF AIN MATERIAL AND SUBSTRATE FOR GROWTH BY EPITAXIS OF A MONOCRYSTALLINE LAYER OF AIN MATERIAL
JP6911812B2 (en) * 2018-06-06 2021-07-28 信越半導体株式会社 Anodizing equipment, anodizing method and cathode manufacturing method for anodizing equipment
CN109406555B (en) * 2018-10-15 2021-12-07 上海华力微电子有限公司 Sample layering removing method
US10624213B1 (en) 2018-12-20 2020-04-14 Intel Corporation Asymmetric electronic substrate and method of manufacture
US10892016B1 (en) 2019-04-08 2021-01-12 Monolithic 3D Inc. 3D memory semiconductor devices and structures
US11296106B2 (en) 2019-04-08 2022-04-05 Monolithic 3D Inc. 3D memory semiconductor devices and structures
US11158652B1 (en) 2019-04-08 2021-10-26 Monolithic 3D Inc. 3D memory semiconductor devices and structures
US11763864B2 (en) 2019-04-08 2023-09-19 Monolithic 3D Inc. 3D memory semiconductor devices and structures with bit-line pillars
US11018156B2 (en) 2019-04-08 2021-05-25 Monolithic 3D Inc. 3D memory semiconductor devices and structures
FR3098643B1 (en) * 2019-07-09 2023-01-13 Commissariat Energie Atomique Manufacture of a photosensitive semiconductor device
CN112670170B (en) * 2020-12-30 2024-02-02 长春长光圆辰微电子技术有限公司 Method for improving bonding force of silicon wafer
WO2023067386A1 (en) * 2021-10-22 2023-04-27 Infineon Technologies Ag Manufacturing and reuse of semiconductor substrates
CN115867107B (en) * 2023-02-27 2023-12-08 青禾晶元(天津)半导体材料有限公司 Method for synchronously preparing two composite piezoelectric substrates by using bonding technology

Family Cites Families (26)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPS62108539A (en) * 1985-11-07 1987-05-19 Oki Electric Ind Co Ltd Manufacture of soi-structure semiconductor device
GB8725497D0 (en) * 1987-10-30 1987-12-02 Atomic Energy Authority Uk Isolation of silicon
DE68913254T2 (en) * 1988-10-02 1994-07-07 Canon Kk Crystal article and process for its manufacture.
US5290712A (en) * 1989-03-31 1994-03-01 Canon Kabushiki Kaisha Process for forming crystalline semiconductor film
US5278092A (en) * 1989-08-07 1994-01-11 Canon Kabushiki Kaisha Method of forming crystal semiconductor film
JPH0370156A (en) * 1989-08-10 1991-03-26 Oki Electric Ind Co Ltd Manufacture of semiconductor device
US5278093A (en) * 1989-09-23 1994-01-11 Canon Kabushiki Kaisha Method for forming semiconductor thin film
JP2695488B2 (en) * 1989-10-09 1997-12-24 キヤノン株式会社 Crystal growth method
US5363793A (en) * 1990-04-06 1994-11-15 Canon Kabushiki Kaisha Method for forming crystals
CA2048339C (en) * 1990-08-03 1997-11-25 Takao Yonehara Semiconductor member and process for preparing semiconductor member
GB9025236D0 (en) * 1990-11-20 1991-01-02 Secr Defence Silicon-on porous-silicon;method of production
US5403771A (en) * 1990-12-26 1995-04-04 Canon Kabushiki Kaisha Process for producing a solar cell by means of epitaxial growth process
FR2681472B1 (en) * 1991-09-18 1993-10-29 Commissariat Energie Atomique PROCESS FOR PRODUCING THIN FILMS OF SEMICONDUCTOR MATERIAL.
JP3112106B2 (en) * 1991-10-11 2000-11-27 キヤノン株式会社 Manufacturing method of semiconductor substrate
US5285078A (en) * 1992-01-24 1994-02-08 Nippon Steel Corporation Light emitting element with employment of porous silicon and optical device utilizing light emitting element
DE69333152T2 (en) * 1992-01-30 2004-05-27 Canon K.K. Method of manufacturing a semiconductor substrate
JP3214631B2 (en) * 1992-01-31 2001-10-02 キヤノン株式会社 Semiconductor substrate and method of manufacturing the same
US5331180A (en) * 1992-04-30 1994-07-19 Fujitsu Limited Porous semiconductor light emitting device
JP3352118B2 (en) 1992-08-25 2002-12-03 キヤノン株式会社 Semiconductor device and manufacturing method thereof
JPH06338631A (en) * 1993-03-29 1994-12-06 Canon Inc Light-emitting element and manufacture thereof
JP2972066B2 (en) * 1993-09-09 1999-11-08 シャープ株式会社 Method for manufacturing porous silicon film
JPH07211602A (en) * 1994-01-13 1995-08-11 Canon Inc Production of semiconductor substrate
JP3257580B2 (en) * 1994-03-10 2002-02-18 キヤノン株式会社 Manufacturing method of semiconductor substrate
JPH08148280A (en) * 1994-04-14 1996-06-07 Toshiba Corp Semiconductor device and manufacture therefor
JPH07326719A (en) * 1994-05-31 1995-12-12 Canon Inc Forming method of bonded semiconductor substrate
JP7211602B1 (en) 2021-10-19 2023-01-24 ジャラ テック プライベートリミテッド Aquaculture support system

Also Published As

Publication number Publication date
CA2187269A1 (en) 1997-04-07
JP3352340B2 (en) 2002-12-03
DE69631233T2 (en) 2004-11-11
JPH09162090A (en) 1997-06-20
SG63669A1 (en) 1999-03-30
US20010019153A1 (en) 2001-09-06
US6246068B1 (en) 2001-06-12
DE69631233D1 (en) 2004-02-05
US5854123A (en) 1998-12-29
KR100348514B1 (en) 2002-08-13
CN1159071A (en) 1997-09-10
EP0767486A3 (en) 1997-12-29
EP0767486B1 (en) 2004-01-02
TW330307B (en) 1998-04-21
KR100291501B1 (en) 2001-10-24
EP0767486A2 (en) 1997-04-09
CN1132223C (en) 2003-12-24

Similar Documents

Publication Publication Date Title
CA2187269C (en) Semiconductor substrate and producing method thereof
US20030087503A1 (en) Process for production of semiconductor substrate
AU728331B2 (en) Semiconductor substrate and method of manufacturing the same
KR100282111B1 (en) Method of manufacturing a semiconductor article
AU744654B2 (en) Substrate and production method thereof
US6294478B1 (en) Fabrication process for a semiconductor substrate
US6054363A (en) Method of manufacturing semiconductor article
KR100348513B1 (en) Process for producing semiconductor substrate
EP0843344A1 (en) Process for transferring a semiconductor layer using silicon on insulator (SOI) technology
AU745315B2 (en) Method for manufacturing semiconductor article
JP3697052B2 (en) Substrate manufacturing method and semiconductor film manufacturing method
JP3293767B2 (en) Semiconductor member manufacturing method
JP3013932B2 (en) Semiconductor member manufacturing method and semiconductor member
JP3293766B2 (en) Semiconductor member manufacturing method

Legal Events

Date Code Title Description
EEER Examination request
MKLA Lapsed