CA2007601A1

CA2007601A1 - Process for preparing self-supporting bodies and products made thereby

Info

Publication number: CA2007601A1
Application number: CA002007601A
Authority: CA
Inventors: Danny R. White; Terry D. Claar
Original assignee: Danny R. White; Terry D. Claar; Lanxide Technology Company, Lp
Current assignee: Lanxide Technology Co LP
Priority date: 1989-01-13
Filing date: 1990-01-11
Publication date: 1990-07-13
Also published as: IL92394A; PH26245A; CN1022102C; KR0134960B1; AU628462B2; EP0378502A1; PT92854A; NO900145D0; FI900200A0; DE69004813T2; DE69004813D1; ATE97892T1; NO900145L; JPH02275764A; EP0378502B1; KR900011682A; US5296419A; ZA90215B; AU4779490A; BR9000088A

Abstract

ABSTRACT
Self-supporting bodies are produced by reactive infiltration of a parent metal into a boron nitride material typically resulting in a body comprising a boron-containing compound, a nitrogen-containing compound and metal. The mass to be infiltrated may contain one or more inert fillers admixed with the boron nitride, to produce a composite by reactive infiltration, which composite comprises a matrix which embeds the filler material. The matrix, in a composite body containing filler material, comprises one or more of metal, a boron-containing compound and a nitrogen-containing compound. The relative amounts of reactants and process conditions may be altered or controlled to yield a body containing varying volume percents of ceramic, metal and/or porosity. The mass to be infiltrated can be contained within a refractory vessel having a venting means included therein.

Description

fi~)l.
PROCESS FOR PREPARING SELF-SUPPORTING
BODIES AND PRODUCTS MADE THEREBY
~ield of the Invention This invention relates generally to a novel method of preparing self-supporting bodies, and to novel products made thereby. In its more specific aspects, this invention relates to a method of producing self-supporting bodies comprising one or more boron-containing compounds, e.g.
a boride or a boride and a nitride, by reactive infiltration of a molten parent ~etal into a bed or mass tontaining boron nitride and, optionally, one or more inert fillers, to form the body.

Backqround of the Present Invention In recent years, there has been an increasing interest in the use of ceramics for structural applications historically served by metals. The impetus for this interest has been the superiority of ceramics with respect to certain properties, such as corrosion resistance, hardness, wear resistance, modulus of elasticity, and refractory capabilities when compared with metals.
However, a ma~or limitation on the use of ceramics for such purposes is the feasibility and cost of producing the desired ceramic structures.
For example, the production of ceramic boride bodies by the methods of hot pressing, reaction sintering and reaction hot pressing is well known. In the case of hot pressing, fine powder particles of the desired boride are compacted at high temperatures and pressures. Reaction hot pressing involves, for example, compacting at elevated temperatures and pressures boron or a metal boride with a suitable metal-containing powder. U.S.
Patent No. ~ o Clougherty describes the preparation of a boride body by hot pressing a mixture of powdered metal with a powdered diboride, 30 ~ and U.S. Patent No.~ S~Lto Brun describes hot pressing ceramic 7~ powder with boron and a metal hydride to form a boride composite. 5 However, these hot pressing methods require special handling and expensive special equipment, they are limited as to the size and shape of the ceramic part produced, and they typically involve low process productivities and high manufacturing cost.
A second ma~or limitation on the use of ceramics for structural applications is their general lack of toughness (i.e. damage tolerance or resistance to fracture). ~his characteristic tends to result in sudden.

0~6 0 easily ~nduced, catastrophic failure of ceramics in applications invol~ing even rather moderate tensile stresses. This lack of toughness tends to be particularly common in monolithic ceramic boride bodies.
One approach to overcome this problem has been to attempt to use ceramics tn comblnation with metals, for example, as cermets or metal matrix composites. The ob~ective of this approach is to obtain a combinatton of the best properties of the ceramic (e.g. hardness and/or stiffness) and the metal (e.g. ductility). U.S. Patent 4,585,618 to Fresnel, et al., discloses a method of producing a cermet whereby a bulk reaction ~ixture of particulate reactants, which react to produce a sintered self-sustaining ceramic body, is reacted while in contact with a molten metal. ~he molten metal infiltrates at least a portion of the resulting ceramic body. Exemplary of such a reaction mixture is one containing titanium, aluminum and boron oxide (all in particulate form), which is heated while in contact with a pool of molten aluminum. The reaction mixture reacts to form titanium diboride and alumina as the ceramic phase, which is infiltrated by the molten aluminum. ~hus, this method uses the aluminum in the reaction mixture principally as a reducing agent. Further, the external pool of molten aluminum is not being used as a source of precursor metal for a boride forming reaction, but rather it is being utilized as a means to fill the pores in the resulting ceramic structure. This creates cermets which are wettable and resistant to ~olten àluminum. These cermets are particularly useful in aluminum production cells as components which contact the molten aluminum produced but preferably remain out of contact with the molten cryolite.
European Application 0,113,249 to Reeve, et al. discloses a method for making a cermet by first forming in situ dispersed particles of a ceramic phase ~n a molten metal phase, and then maintaining this molten condition for a time sufficient to effect formation of an intergrown ceramic network. Formation of the ceramic phase ts illustrated by reacting a titanium salt with a boron salt tn a molten metal such as aluminum. A ceramic boride ts developed in situ and becomes an intergrown network. ~here ts, however, no infiltration, and further the boride is formed as a precipitate in the molten metal. Both examples in the application expressly state that no grains were formed of ~iA13, AlB2, or AlB12, but rather ~iB2 is formed demonstrating the fact that the aluminum is not the metal precursor to the boride.

~0~7 6 U.S. Patent No. 3,864,l54 to Gazza, et al. discl~ses a ceramic-metal system produced by infiltration. An AlBl2 compact was impregnated with molten aluminum under vacuum to yield a system of these components. Other materlals prepared included SiB6-Al, B-Al; B4C-Al/Si; and AlBl2-B^Al.
There ls no suggestion whatsoever of a reaction, and no suggestion of making composltes 1nvolv~ng a reaction with the infiltrating metal nor of any reaction product embedding an inert filler or being part of a composite.
U.S. Patent ~,605,440 to Halverson, et al., discloses that in order to obtain B4C-Al compos~tes, a B4C-Al compact (formed by cold pressing a homogeneous mixture of B4C and Al powders) is subjected to sintering in either a vacuum or an argon atmosphere. There is no infiltration of molten metal from a pool or body of molten precursor metal into a preform.
Further, there is no mention of a reaction product embedding an inert filler in order to obtain composites utilizing the favorable properties of the filler.
~hile these concepts for producing cermet materials have in some cases produced promising results, there is a general need for more effective and economical methods to prepare boride-containing materials.
Discussion of Related Patent ADDlications Many of the above-discussed problems associated with the production of boride-containing materials have been addressed in co-pending U.S.
Patent Application Serial No. 073,533, filed in the names of Danny R.
~hite, Michael K. Aghajanian and T. Dennis Claar, on ~uly l5, 1987, and entitled ~Process for Preparing Self-Supporting Bodies and Products Made Thereby~.
Briefly summarizing the disclosure of Application '533, self-supporting ceramic bodies are produced by utili~ing a parent metal 3~ infiltration and reaction process (i.e., reactive infiltration) in the presence of a boron carbide. Particularly, a bed or mass of boron carbide ~s infiltrated by molten parent metal, and the bed may be comprised entirely of boron carbide, thus resulting in a self-supporting body comprising one or more parent metal boron-containing compounds, which compounds include a parent metal boride or a parent metal boro carbide, or both, and typically also may include a parent metal carbide. lt is also disclosed that the mass of boron carbide which is to be infiltrated may also contain one or more inert fillers mixed with the boron carbide.

Accordingly, by combining an inert filler, the result will be a composite body having a matrix produced by the reactive infiltration of the parent metal, said matrix comprising at least one boron-containing compound, and the matrix may also include a parent metal carbide, the matr;x embedding S the 1nert filler. It is further noted that the final composite body product tn either of the above-discussed embodiments (i.e., filler or no filler) may include a residual metal as at least one metallic constituent of the original parent metal.
Broadly, in the disclosed method of Application '533, a mass comprising boron carbide is placed adjacent to or in contact with a body of molten metal or metal alloy, which ~s melted in a substantially inert environment within a particular temperature envelope. The molten metal infiltrates the boron carbide mass and reacts with the boron carbide to form at least one reaction product. The boron carbide is reducible, at least in part, by the molten parent metal, thereby forming the parent metal boron-containing compound (e.g., a parent metal boride and/or boro compound under the temperature conditions of the process). Typically, a parent metal carbide is also produced, and in certain cases, a parent metal boro carbide is produced. At least a portion of the reaction product is maintained in contact with the metal, and molten metal is drawn or transported toward the unreacted boron carbide by a wicking or a capillary action. This transported metal forms additional parent metal, boride, carbide, and/or boro carbide and the formation or development of a ceramic body ~s continued until either the parent metal or boron carbide has been consumed, or until the reaction temperature is altered to be outside of the reaction temperature envelope. The resulting structure comprises one or more of a parent metal boride, a parent metal boro compound, a parent metal carbide, a metal (which, as discussed in Application '533, ~s ~ntended to include alloys and intermetallics), or voids, or any combination thereof. Moreover, these several phases may or may not be interconnected in one or more dimensions throughout the body.
~he final volume fractions of the boron-containing compounds (i.e., boride and boron compounds), carbon-containing compounds, and metallic phases, and the degree of interconnectivity, can be controlled by changing one or more conditions, such ~s the initial density of the boron carbide body, the relative amounts of boron carbide and parent metal, alloys of the parent metal, dilution of the boron carbide with a filler, temperature, ~63n ~fiol.

~nd time. Preferably, conversion of the boron carbide to the parent metal boride, parent metal boro compound(s) and parent metal carbide is at least about 50%, and most preferably at least about 90%.
The typical environment or atmosphere which was utilized in Appltcatlon '533 ~as one ~hich is relatively inert or unreactive under the process conditions. Particularly, lt was disclosed that an argon gas, or a vacuum, for example, would be suitable process atmospheres. Still further, 1t ~as dlsclosed that when zirconium was used s the parent metal, the resulting composite comprised zirconium diboride, zirconium carbide, nd residual zirconlum metal. It was also disclosed that when ~lum;num parent metal was used w;th the process, the result was an aluminum boro carbide such as Al3B48C2, AlB~2C2 and/or AlB24C4~
aluminum parent metal and other unreacted unoxidized constituents of the parent metal remaining. Other parent metals which were disclosed as being suitable for use with the processing conditions included silicon, titan;um, hafnium, lanthanum, iron, calcium, vanadium, niobium, magnesium, and beryllium.
Copending U.S. Patent Application Serial No. 137,044 (hereinafter referred to as ~Appllcatlon '044~), f;led in the names of Terry Dennis Claar, Steven Mlchael Mason, Kev;n Peter Pochopien and Danny Ray ~hite, on December 23, l987, and entitled ~Process for ~reparing Self-Supporting Bodies and Products Made ~hereby~, is a Continuation-in-Part Application of Application '533. Application '044 discloses that in some cases it may be desirable to add a carbon donor material (i.e., a carbon-containing compound) to the bed or mass of boron carbide which is to be infiltrated by molten parent metal. Specifically, it was disclosed that the carbon donor material could be capable of reacting with the parent metal to form a parent metal-carbide phase which could modify resultant mechanical properties of the composite body, relative to a composite body wh;ch was produced without the use of a carbon donor material. Accordingly, it was disclosed that reactant concentrations and process conditions could be ~ltered or controlled to yield a body containing varying volume percents of ceramic compounds, metal and/or porosity. For example, by adding a carbon donor materlal (e.g., graphite powder or carbon black) to the mass of boron carbide, the ratio of parent metal-boride/parent metal-carbide could be adjusted. In part;cular, if z;rcon;um was used as the parent metal, the ratio of ZrB2/ZrC could be reduced (i.e., more ZrC could be fi~)l.

produced due to the addition of a carbon donor material in the mass ofboron carbide).
Application '044 also dlscloses the use of a graphite ~old which contains an appropriate number of through-holes having a particular size, shape and location which function as a venting means to permit the removal of, for example, any gas which may be trapped in the prefonm or f~ller ~aterial as the parent metal reactive ~nfiltration front infiltrates the preform.
In another related application, specifically, Copending U.S. Patent Application Serial No. 137,382 (hereinafter referred to as ~Application '382~), filed in the names of ~erry Dennis Claar and Gerhard Hans Schiroky, on December 23, 1987, and entitled ~A Method of Modifying Ceramic Composite Bodies By a Carburization Process and Articles Made Thereby~, additional modification techniques are disclosed. Specifically, Application '382 discloses that a ceramic composite body made in accordance with the teachings of Application '533 can be modified by exposing the composite to a gaseous carburizing species. Such a gaseous carburizing spec~es can be produced by, for example, embedding the composite body in a graphitic bedding and reacting at least a portion of the graphitic bedding with moisture or oxygen in a controlled atmosphere furnace. However, the furnace atmosphere should comprise typically, primarily, a non-reactive gas such as argon. It is not clear whether impurities present in the argon gas supply the necessary 2 for forming a carburizing species, or whether the argon gas merely serves as a vehicle which contains impurities generated by some type of volatilization of components in the graphitic bedding or in the composite body. ln addition, a gaseous carburizing species could be introduced directly into controlled atmosphere furnace during heating of the composite body.
Once the gaseous carburizing species has been introduced into the controlled atmosphere furnace, the setup should be designed in such a manner to permlt the carburizing species to be able to contact at least a portion of the surface of the composite body buried )n the loosely packed graphitic powder. lt ~s believed that carbon in the carburizing species, or carbon from the graphitic bedding, will dissolve into the interconnected zirconium carbide phase, which can then transport the dissolved carbon throughout substantially all of the tomposite body, if desired, by a vacancy diffusion process. Moreover, Application '382 ~V~)'7~01 discloses that by controlling the time, the exposure of the composite body to the carburizing species and/or the temperature at which the carbur~zation process occurs, a carburized zone or layer can be formed on the surface of the composite body. Such process could result in a hard, ~ear-resistant surface surrounding a core of composite material having a higher metal content and higher fracture toughness.
~ hus, ~f a composite body ~as formed having a residual parent metal phase in the amount of between about 5-30 volume percent, such composite body could be modified by a post-carbur~ation treatment to result in from about O to about 2 volume percent, typ1cally ~bout l/2 to about 2 volume percent, of parent metal remaining in the composite body.
The disclosures of each of the above-discussed Commonly Owned U.S.
Applications are herein expressly incorporated by reference.
I5 SummarY of the Invention In accordance with the present invention, self- supporting ceramic bodies are produced utilizing a parent metal infiltration and reaction process (i.e. reactive infiltration) in the presence of boron nitride. A
bed or mass of boron nitride is infiltrated by molten parent metal, and the bed may be comprised entirely of boron nitride, resulting in a self-supporting body comprising one or more parent metal boron-containing compounds, which compounds include a parent metal boride or a parent metal nitride, or both. Al~ernatively, the mass to be infiltrated may contain one or more inert fillers admixed with the boron nitride to produce a composite by reactive infiltration, which composite comprises a matrix of one or more boron- containing compounds and also may include a parent metal nitride and residual unreacted or unoxidized constituents of the parent metal. ln certain embodiments of the present invention, the filler ~aterial may be embedded by a matrix cDmprising parent metal boron-containing compounds, parent metal nitrogen-containing compounds and unreacted or unoxidized parent metal. In both embodiments, the final product may include a metal as one or more metallic constituents of the parent metal. Still further, in some cases 1t may be desirable to add a carbon donor mater1al (i.e., a carbon-containing compound) to the boron nitride, the carbon donor material being capable of reacting with the parent metal to form a parent metal-carbide phase, thereby modifying resultant mechanical properties of the composite body. ~he reactant concentrations and process conditions may be altered or controlled to yield 7fiQl.

a body containing varying volume percents of ceramic compounds, metal and/or porosity.
8roadly, in the method of this invention, a mass comprising boron n1tride is placed ad~acent to or contacted with a body of molten metal or metal alloy, which is melted in a substantially lnert environment within a partlcular temperature envelope. The molten metal infiltrates the mass and reatts with the boron nitride to form one or more reaction products.
The boron nitrlde ls reducible, at least in part, by the molten parent metal to form the parent metal boron-containing compound, e.g. a parent metal boride and/or boro compound, under the temperature conditions of the process. Typically a parent metal nitride is also produced. At least a portion of the reaction product is maintained in contact with the metal, and molten metal is drawn or transported toward the unreacted boron nitride by wicking or capillary action. ~his transported metal forms additional parent metal boride and nitride, and the formation or development of a ceramic body is continued until the parent metal or boron nitride has been consumed, or until the reaction temperature is altered to be outside the reaction temperature envelope. ~he resulting structure comprises one or more of a parent metal boride, a parent metal boro compound, a parent metal nitride, a metal (which as used herein is intended to include alloys and intermetallics), or voids, or a combination thereof, and these several phases may or may not be interconnected in one or more dimensions. The final volume fractions of the boron- containing compounds (i.e. boride and boro compounds), nitrogen-containing compounds, and metallic phases, and the degree of interconnectivity, can be controlled by changing one or more conditions, such as the initial density of the boron nitride body, the relative amounts of boron nitride and parent metal, alloying the parent metal, dilution of the boron nitride with a f~ller, temperature and time.
Moreover, by adding a carbon donor material (e.g., graphite powder or carbon black) to the mass of boron nitrlde, a parent metal carbide phase may be formed wh~ch may modify or enhance one or more properties of the final body.
Typically, the mass of boron nitride will be at least somewhat porous so as to allow for wicking the parent metal through the reaction product.
Wicking occurs apparently either because any volume change on reaction does not fully close off pores through which parent metal can continue to ~C~()'7fi~

wick, or because the reaction product remains permeable to the molten metal due to such factors as surface energy considerations which render at least some of its grain boundaries permeable to the parent metal.
In another embodiment, a compos~te is produced by the transport of molten parent ~etal ~nto a bedding of boron n~tride admixed with one or more inert filler materials. In this embodiment, boron nitride is ~ncorporated 1nto a suitable f~ller material, ~hich then ~s placed ad~acent to or in contact with the molten parent metal. This setup may be supported on or 1n a separate bed that is substantially non-wettable by and non-reactive with the molten metal under the process conditions.
The molten parent metal infiltrates the boron nitride-filler mixture and reacts with the boron nitride to form one or more boron-containing compounds. ~he resulting self-supporting ceramic-metal composite typically is a dense microstructure which comprises a filler embedded by a matrix comprising boron-containing compound(s), and also may include a substantial quantity of a nitride and metal. Only a small amount of boron nitride is required to promote the reactive infiltration process.
~hus, the resulting matrix can vary in content fro~ one composed pr~marily of metallic constituents thereby exhibiting certain properties characteristic of the parent metal; to cases where a high concentration of the boron nitride is used in the process, thereby producing either a significant boron-containing compound(s) phase or a significant nitrogen-containing compound(s) phase, or both, which dominate the properties of the matrix. The filler may serve to enhance the properties of the composite, lower the raw materials cost of the composite, or moderate the kinetics of the boron-containing compound(s) - and/or nitrogen-containing compound(s) formation reactions and the associated rate of heat evolution.
In a further embodiment, the material to be infiltrated is shaped into a preform corresponding to the geometry of the deslred final composite. Subsequent reactive infiltration of the preform by the molten parent metal results in a composite having the net shape or near net shape of the preform, thereby mini0izing expenslve final machining and finishing operations. Moreover, to assist ~n reducing the amount of final machining and finishing operations, a barrier material can surround the preform. The use of a graphite mold is particularly useful as a barrier for such parent metals as zirconium, titanium, or hafnium, ;~Vn'~

- ~o -when used in combination with preforms made of, for example, boron carbide, boron nitride, boron and carbon. Still further, by placing an appropriate number of through-holes having a particular size and shape 1n the aforementioned graphite mold, the amount of porosity which typically occurs within a compos~te body manufactured according to the present ~nvention, ~s reduced. Typically, a plurality of holes is placed in a bottom portion of the mold, or that portion of the mold toward ~hich reactive infiltration occurs. The holes function as a venting means which permit the removal of, for example, argon gas which has been trapped in the preform as the parent metal reactive infiltration front lnfiltrates the preform.
Still further, the procedures discussed above herein in the Section ~Discussion of Related patent Applications~ may be applicable in this invention.
Definitions As used in this specification and the appended claims, the terms below are defined as follows:
~Parent metal~ refers to that metal, e.g. zirconium, which is the precursor for the polycrystalline oxidation reaction product, that is, the parent metal boride, parent metal nitride, or other parent metal compound, and includes that metal as a pure or relatively pure metal, a commercially available metal having impurities and/or alloying constituents therein, and an alloy in which that metal precursor is the major constituent; and when a specific metal is mentioned as the parent metal, e.g. zirconium, the metal identified should be read with this definition in mind unless indicated otherwise, by the context.
~Parent metal boride~ and ~parent metal boro compounds~ mean a reaction product containing boron formed upon reaction between boron nitride and the parent metal and includes a binary compound of boron ~ith the parent metal as well as ternary or higher order compounds.
~Parent metal nitride~ means a reaction product containing nitrogen formed upon reaction of boron nitride and parent metal.
~Parent metal carbide~ means a reaction product containing carbon formed upon reaction of a carbon source and parent metal.

~C~0'7fi~

Brief DescriDtion of the Drawinqs Figure 1 ~s a schematic cross-section of an assembly utilized to form a body according to the present invention;
F~gure 2 is a schematic cross-section of an assembly utilized to fonm a body according to the present invention;
Figures 3 and 4 show a novel graphite mold for use with the ilnvention;
Figure S is a photomicrograph taken at 50X of a cross-section of a body produced ln accordance ~ith Example l;
Figure 6 ls a photomicrograph taken at 400X of a cross-section of a body produced according to Example l;
Figure 7 is a photomicrograph taken at 400X of a cross-section of a sample produced according to Example 2;
Figure 8 shows a sample produced in accordance with Example 4; and Figure 9 shows a sample produced in accordance with Example 6.

Detailed DescriDtion of the Invention and Preferred Embodiments In accordance with the lnvention, a self-supporting body is produced by the reactive infiltration of a molten parent metal into a mass comprising boron nitride to form a polycrystalline ceramic-containing body comprising the reaction product(s) of the parent metal with boron nitride, and also may include one or more constituents of the parent metal. ~he boron nitride, typically a solid at the process conditions, is preferably in fine particulate or powdered form. The environment or atmosphere for the process is chosen to be relatively inert or nonreactive under the process conditions. Argon or vacuum, for example, would be suitable process atmDspheres. The resulting product comprises one or more of (a) a parent metal boride, (b) a boro compound, (c) a parent metal nitride, and (d) metal. The constituents and proportions in the product depend largely on the choice and composition of parent metal and the reaction conditions. Also, the self-supporting body produced may exhibit porosity or voids.
In the preferred embodiments of the present invention, the parent metal and a mass or bedding of boron nitride are positioned adjacent each other so that reactive infiltration will be in the direction towards and into the bedding. ~he bedding, which may be preshaped, may include a ;~0 n 7 6 0 - l2 -filler material, such as a reinforcing filler, which is substantially ~nert under the process conditions. This filler material is usually embedded by a matrix comprising the reaction products formed from the reaction between the parent metal and the boron nitride, and the matrix may also contain unoxidized or unreacted const1tuents of the parent metal.
~he reaction product can grow into the bedding without substantially disturbing or displacing it. Thus, no external forces are required which might damage or disturb the arrangement of the bedding and no awkward or costly high temperature, high pressure processes and facilities are required to create the reaction product. Reactive infiltration of the parent metal into and w~th a mass of filler material containing boron nitride, which preferably is in particulate or powdered form, forms a composite typically compr;sing filler material and parent metal borides and parent metal nitrides. ~ith aluminum as the parent metal, in lS addition to the filler material, the product may comprise borides or nitrides of aluminum, and also may include unreacted parent metal, e.g.
aluminum, and possibly other unreacted or unoxidized constituents of the parent metal. If zirconium is the parent metal, the resulting composite may compr~se, in addition to the filler material, borides or carbides of zirconium, and also may include unreacted or unoxidized parent metal or constituents of the parent metal.
Although the present invention is hereinafter described with particular reference to certain preferred embodiments in which the parent metal is zirconium or aluminum, this is for illustrative purposes only. Other parent metals also may be used such as silicon, titanium, hafnium, lanthanum, iron, calcium, vanadium, niobium, magnesium, tantalum, chromium, molybdenum, tungsten and beryllium, and examples for several such parent metals are given below.
Referring to Figure 1, the parent metal lO as the precursor, e.g.
zirconium, is formed into an ingot, billet, rod, plate, or the like. The metal 1s ~t least partially embedded in particulate boron nitride 12. This setup or assembly ~s surrounded by an inert material l4, typically in particulate form, which ~s not-wettable by and non- reactive with the molten metal under the process conditions, and contained within a crucible 16 or other refractory vessel. The top surface 18 of the parent metal may be exposed, or the parent metal may be completely embedded or surrounded by the boron nitride, and also the inert bed 14 may be omitted. This assembly ~)0 7 6 0 i ~s placed in a furnace and heated, preferably in an inert atmosphere such as argon, above the melting point of the parent metal but preferably below the melting point of the desired reaction product so as to form a body or pool of molten metal. It should be understood that the operable temperature range or preferred temperature may not extend over this entire ~nterval. The temperature range will depend largely upon such fa~tors as the composition of the parent metal and the desired phases in the resulting composite. Molten metal contacts the boron n~tride, and a parent metal boride (e.g. zirconium diboride) and/or ~ parent metal n~tride (e.g., zirconium nitride) are formed ~s the reaction product. Upon continued exposure to the boron nitride, the remaining molten metal 1s progressively drawn through the reaction product in the direction of and into the mass containing the boron nitride, to provide continued formation of reaction product at the interface between the molten metal and boron nitride. The product produced by this method comprises the reaction product(s) of the parent metal with the boron nitride, sr may comprise a cera~ic-metal composite to include further one or more unreacted or non-oxidized constituents of the parent metal. A substant~al amount of the boron nitride is reacted to form the reaction product~s), preferably this am~unt being at least about 25%. The ceramic crystallites formed as the reaction product by the process may or may not be interconnected, but preferably are interconnected in three dimensions, and the metallic phases and any voids in the product are normally at least partially interconnected. Any porosity tends to result from a partial or nearly complete depletlon of the parent metallic phase in favor of the formation of additional reaction product (as in the case where boron nitride is present in at least a stoichiometric amount), but the volume percent of voids will depend on such factors as temperature, time, type of parent metal, and the porosity of the mass of boron nitride.
It has been observed that products made in accordance with this invention using zirconium, titanium and hafnium as the parent metal form a parent metal boride characterized by a platelet-like structure. ~hese platelets typically are unaligned or randomly oriented and may increase the fracture toughness of the body because of crack deflection and/or pull-out mechanisms.
In another aspect of the invention, there is provided a self-supporting body, including composite bodies, comprising a matrix of ~0~

reaction product, and, optionally metallic constituents, embedding a substantially inert filler. ~he matrix is formed by the react;ve ~nfiltration of a parent metal into a bed or mass of the filler 1nt~ately mixed with boron nitride. The filler material may be of any size or shape, and may be orlented ~ith respect to the parent metal in any wanner as long as the direction of development of the reaction product wSll be towards and will engulf at least a portion of the filler material without substantially disturbing or displacing it.The filler may be composed of or comprise any suitable material, such as ceramic ~0 and~or metal fibers, whiskers, particulates, powders, rods, wires, wire cloth, refractory cloth, plates, platelets, reticulated foam structure, solid or hollow spheres, etc. A particularly useful filler is alumina, but other oxides and ceramic fillers may be used depending on the starting materials and the end properties desired. ~he volume of filler material may be a loose or bonded array or arrangement, which array has interstices, openings, intervening spaces, or the like, to render the filler material permeable to the infiltration of molten parent metal.
Further the filler material may be homogeneous or heterogeneous. If desired, these materials may be bonded with any suitable binding agent (e.g. Avicil PH I05, from FMC Co.) whith does not interfere with the reactions of this invention or leave any undesirable residual by-products within the final composite product. A filler which would tend to react excessively with the boron nitride or with the molten metal during processing may be coated so as to render the filler inert to the process environment. For example, carbon fiber, if used as a filler in conjunction with aluminum as the parent metal will tend to react with molten aluminum, but this reaction can be avoided if the fiber is first coated, e.g. with alumina.
A suitable refractory container holding the parent metal and a bed or volume of filler with admixed boron nitride properly oriented to permit reactive ~nfiltration of the parent metal into the filler bed and proper development of the compos~te, ~s placed in a furnace, and this lay-up ~s heated to a temperature above the melting point of the parent metal. At these elevated temperatures, the molten parent metal ~nfiltrates the permeable filler by a wicking process and reacts with the boron nitride, thereby producing the desired ceramic or ceramic-metal composite body. Moreover, to assist in reducing the amount of ~6~0'7 6C) - ~5 -final machining and finishing operations, a barrier material can surround the preform. The use of a graphite mold ~s particularly useful as a barrier for such parent metals as zirconium, titanium, or hafnium, when used in combination with preforms made of, for example, boron carbide, boron nitride, boron and carbon. Still further, by placing an appropriate number of through-holes having a particular size and shape in the aforementioned graphite mold, the amount of porosity which typically occurs within a composite body manufactured according to the prcsent ~nventlon, ~s reduced. Typically, a plurality of holes is placed in a bottom portion of the mold, or that portion of the mold toward ~hich reactive infiltration occursO The holes funçtion as a venting means which permit the removal of, for example, argon gas which has been trapped in the preform as the parent metal reactive infiltration front infiltrates the preform. Figure 3 and Figure 4 show a preform 42 in contact with a parent metal ingot 43, both of which are contained in a graphite refractory vessel 41. The graphite refractory vessel 41 has a bottom portion 44 having therein a plurality of through-holes 45 which function as a ventlng means. ~he through-holes 45 permit any gas trapped ln the preform (e.g., argon) to escape as the parent metal reactive infiltration front infiltrates the preform (i.e., the reactive infiltration front penetrates the preform in the direction of the arrow ~A~ in Figure 3). Thus, porosity in the formed composite body can be reduced.
A setup which can be utilized to produce the bodies of this invention is illustrated in Figure 2. ~he boron nitride, together with any desired inert filler materials, is fabricated into a preform with a shape corresponding to the desired geometry of the final composite. The preform 20 is superimposed with the parent metal precursor 10 and the assembly is surrounded by the inert material 14 contained within the crucible 16. ~he top surface 18 of the parent metal may or may not be exposed. The preform 20 may be prepared by any of a ~ide range of conventional ceramic body formation methods tSUch as uniax;al pressing, ~sostatic pressing, slip casting, sedimentation casting, tape casting, injection molding, filament winding for fibrous materials, etc.) depending on the characteristics of the filler. Initial bonding of the filler particles, whiskers, fibers, or the like, prior to reactive infiltration may be sbtained through light sintering or by use of various organic or inorganic binder materials which ~00'7fiO~.
- ~6 -do not interfere with the process or contribute undesirable by- products to the finished material. The preform 20 is manufactured to have sufficient shape integrity and green strength, and should be permeable to the transport of molten metal, preferably having a porosity of between about 5 S and 90~ by volume and more preferably between about 25 and 15% by volume.
In the case of an aluminum parent metal, suitable filler materials include, for example, sil~con carb~de, titanium diboride, alumina and aluminum dodecaboride (among others), and as particulates typically having a mesh size of from about 14 to 1000, but any admixture of filler ~aterials and ~esh sizes ~ay be used. The preform 20 is then contacted with molten parent metal on one or more of its surfaces for a time sufficient to complete infiltration of the matrix to the surface boundaries of the preform. The result of this preform method is a ceram;c-metal composite body of a shape closely or exactly representing that desired in the final product, thus minimizing or eliminating expensive final machining or grind;ng operations.
A wide variation of boron nitride concentrations can be provided ~n the filler, but the lower the concentration of boron nitride, the higher the volume percent of metal in the matrix. ~hen very low amounts of the boron nitride are used, the resulting matrix is interconnected metal and a limited amount of parent metal boride and parent metal nitride dispersed in the metal. In the absence of boron nitride, reactive infiltration of the filler may not occur, and infiltration may not be possible without special procedures, such as the application of external pressure to force the metal into the filler.
Because a wide range of boron nitride concentrations in the filler can be used in the process of this invention, it is possible to control or to modify the properties of the completed product by varying the concentration of boron nitride and/or the composition of the bed. ~hen only a small amount of boron nltride is present relative to the amount of parent metal, such that the mass comprises a low density of boron nitride, the composite body or matrix properties are dominated by the properties of the parent ~etal, most typically ductility and toughness, because the matrix is predominately metal. Such a product may be advantageous for low or mid-range temperature applications. ~hen a large amount of boron nitride is used, as for example when compound(s) having boron nitride particles are densely packed around a filler ~0(~'7~0 ~

material or occupy a high percentage of space between constituents of the filler, the resulting body or matrix properties tend to be dominated by the parent metal boride and parent metal n~tride, 1n that the body or matrix would be harder or less ductile or less tough. If the stoichlometry 1s closely controlled so as to achieve substantially eomplete convers10n of the parent metal, the resulting product will conta1n 11ttle or no metal, which may be advantageous for high temperature applications of the product. Also, the substantially complete conversion of the parent metal could be significant especially ~n some high temperature applications, because the boride reaction product 1s more stable than boron nitride in that boron nitride will tend to react ~ith residual or unoxidized metal, e.g. aluminum, present ~n the product.
In one embodiment of the present invention, TiB2 is added to the boron nitride to obtain a final body having a higher boride content.
~his technique can be utilized with other compounds which might affect or enhance the properties of the final body. For example, AlB12 could be added to the boron nitride in order to create more parent metal boride in the final product and, in addition, the aluminum metal released from the reaction between the AlB12 and parent metal could alloy, or form intermetallics, with the parent metal, thus affecting or enhancing the properties of the final body.
In another embodiment of the present invention, a solid oxidant could be added to the boron nitride bed to permit enhanced infiltration.
Also, elemental boron may be admixed with the boron nitride bed (1ncluding a bed with filler) to facilitate reactive infiltration, particularly when using aluminum as the parent metal.
Additional variations in the characteristics and properties of the composite can be created by controlling the 1nfiltration conditions.
Var1ables which can be manipulated include the nature and size of the part1cles of boron nitride material, nd the temperature and time of ~nf11trat10n. For example, react1ve 1nfiltration involving large boron nitride particles and minimum exposure times at low temperatures will result in a partial conversion of the boron nitride to parent metal boron and parent metal nitrogen containin~ compound(s). As a consequence, unreacted boron nitr~de material remains in the microstructure, which may impart desirable properties to the finished '~C~0'7~i ~aterial for some purposes. lnfiltration involving the boron nitride particles, high temperatures and prolonged exposure times (perhaps even to hold at temperature after infiltration is complete) will tend to favor substantially complete conversion of the parent metal to the parent ~etal boride and nitride compound(s). Preferably, conversion of the boron nitride to the parent metal boride, and parent metal nitride is at least about 25%. Infiltration at high temperatures (or a subsequent high temperature treatment) also may result in densification of some of the composite constituents by a sintering process. In addition, as noted previously, the reduction of the amount of available parent metal below that necessary to form the parent metal boride and nitride compound(s) and fill the resulting interstices in the material may result in a porous body which also could have useful applications.
In such a composite, porosity may vary from about 1 to 25 volume percent, and sometimes higher, depending upon the several factors or conditions enumerated above.
The following Examples illustrate the novel reaction products of this invention and the method by which they are prepared; however, these Examples are illustrative only and they are not intended to limit the invention claimed.

ExamDlel The following example demonstrates the reactive infiltration of a titanium parent metal into a boron nitride bedding.
A cylindrical ingot of commercially pure titanium having approximate dimensions of 1 inch in diameter and 1-1/2 inches tall was embedded within a mass of particulate boron nitride ( approximate particle si~e 150 micron) contained within an alumina crucible.
The assembly, consisting of the alumina crucible and its contents, was ptaced in an induction furnace supplied with argon gas ftowing at 300 cc/minute. The assembly was heated from room temperature to about 1700-C
and maintained at about 1700-C for approximately 30 minutes. After the 30 minute heating period, the furnace was turned off and the assembly was allowed to cool within the furnace for about 1 hour prior to removal from the furnace.
A visual examination of the assembly indicated that the titanium parent metal had reactively infiltrated the boron nitride bedding to form ~ 0'7 6~3~

a self-supporting body. A powdered sample of an interior section of th2 self-supporting body was subjected to X-ray diffraction analysis and this analysis showed the presence of compounds of titanium with nitrogen and boron (such as Ti2N, TiB and possibly TiN), thus confirming that the titanium parent metal had reacted w~th the boron nitride bedding material.
Figure 5 is a photom;crograph at SOX magnification of ~ cross-section of the self-supporting body produced in this example. Figure 6 is a photomicrograph at ~OOX magnification of a cross-section of the self-supporting body produced in this example.
ExamDle 2 The following example demonstrates the reactive infiltration of a titanium parent metal into a bedding of boron nitride mixed with aluminum powder.
lS A cylindrical ingot of commercially pure titanium having approximate dimensions of 1 inch diameter by 1.5 inches tall was embedded within a particulate bedding material comprising about 89.5 grams of 150 micron boron nltride powder and about 22.4 grams of aluminum powder. The bedding mater~al was contained w~th~n an alum~na crucible.
The assembly, consisting of the alumina crucible and its contents, was placed within an induction furnace supplied with argon gas flowing at approximately S00 cc/minute. The assembly was heated from room temperature to about 1700-C and maintained at 1700 C for approximately 30 minutes. After the 30 minute heating period, the furnace was turned off and the assembly was allowed to cool within the furnace for approximately 1 hour.
A visual examination of the assembly indicated that the titanium parent ~etal had reactively infiltrated the boron nitride/aluminum mixture to form a self-supporting body. A powdered sample of an interior section of this body was subjected to X-ray diffraction analysis. ~his analysis showed the presence of compounds of titanium with nitrogen and boron (such as TiN, TiB2 and ~iB), thus confirming that the titanium parent ~etal had reacted with the boron nitride bedding material. This analys~s also showed at least trace amounts of AlBlo, which indicates that the aluminum in the beddin~ materlal reacted with either the boron nitride or with dissociated boron.

~0 7~0~L

Figure 7 ~s a photomicrograph at 4~0X ~agnification of a cross-sect1On of the self-supporting body prDduceJ ~n this example.

ExamDle 3 The follo~ng exampl~ demonstr~tes the reactive infiltration of a zirconium parent ~e~al lnto a bed of particulate Doron nitride.
A cylindr~cal ingot of c~mnercially pure z~rconium parent metal having ~pproximate dimens~ons l ~nch diameter by ~.5 inches tall was embedded within a mass of particulate boron nitride (approximate particle size 150 micron) contained ~ithin an alumina crucible.
The assembly tonsist~ng of the alumina crucible and its contents was placed in an induct~on furnace supplied ~ith argon gas flowing at approximately 500 cc~minute. The ~ssembly was heated from room temperature to a~out l900 C and maintained at l9D0-C for approximately one lS hour. After the one hour heating period the furnace was turned off and the assembly was allowed to cool within the furnace for approximately 1 hour.
A visual examination of the assembly inJicated that the zirconium metal had reactively infiltrated the boron nitride bed to form a self-supporting body.
ExamDle 4 The following example demonstrates the reactive infiltration of a zirconium parent ~etal into a bed of particulate boron nitride.
A cylindri~al ingot of Grade 702 zirconium from Teledyne-Wah-Chang-Albany (Albany OR) having approximate dimensiDns of 5/8 inch in diameter by 3/4 inch tall was embedded in a porous mass of UCAR HCM partitulate boron nitride (partlcle si~e smaller than ~8 mesh and larger than 200 mesh) contained within a gr-ph~te cru~ible. The upper surface of the ingot was left ~x~Dsed t~ the atmDsphere.
The assembly, consisting of the grap~1te er~cible and its contents was placed ~n ~n electrical resistance heated furnace supplied with argon gas flowing at approximately 5D0 ccJminute. The assembly was heated to a t`emperature of about 1900 C Dver a periDd of apprDx;mately four hours and then maintained ~t abDut l900-C for about Dn~ hour. 8efore being removed from the furnace the assembly was ~llowed to c~ol for approximately l2 hours.

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A visual examination of the assembly indicated that the zirconium parent metal had reactively infiltrated the boron nitride bed to form a self-supporting body having an interior cavity which replicated the shape of the cylindrical zirconium ingot, as shown in Figure 8. A powdered sample of an 1nterior section of the body was sub~ected to X-ray diffraction analysis. ~his analysis showed the presence of at least one compound of zirconium with boron (ZrB2), thus confirming that the zirconium parent metal had reacted with the boron nitride bedding ~aterial.
~O
xamDle 5 The following example demonstrates the reactive infiltration of titanium into a bed of particulate boron nitride.
A cylindrical ingot of 6rade 2 titanium having approximate dimensions of 1 inch diameter by 3/8 inch height was placed on top of an approximately l/2 inch thick by 1 inch diameter cylindrical preform of HTP-40 boron nitride (particle size smaller than 40 mesh and larger than l50 mesh), contained within a graphite crucible having a l inch inner diameter. ~he preform was formed by placing a layer of the boron nitride partlculate within the graphite crucible and subjecting the boron nitride layer to vibratory packing for about 2 minutes. A small metal weight was placed on top of the boron nitride layer before the packing procedure was initiated in order to facilitate the densification of the boron nitride layer. No binder was utilized to produce the preform. The assembly, consisting of the graphite crucible and its contents, was placed within an electrical resistance heated furnace supplied with argon gas flowing at ~00 cc/minute. The assembly was heated from room temperature to about 1750-C over a period of approximately 3 hours. ~he assembly was maintained at about 1750-C for approximately 2 hours. After this two hour heating period, the assembly was allowed to cool within the furnace for about 12 hours prior to removal from the furnace.
A visual examination of the ssembly indicated that the titanium parent ~etal had reactively infiltrated the boron nitride preform to form a self-supporting body. A powdered sample of an interior section of the body was subJected to X-ray diffraction analysis. ~his analysis sho~ed the presence of compounds of titanium with nitrogen and boron (such as ~ O'~ 6 O ~

Ti2N and TiB), thus confirming that the titanium parent metal had reacted with the boron nitride bedding material.

Exam~le 6 The follow1ng example demonstrates the reactive infiltration of a titanium parent Detal into a bed of particulate boron nitride.
A cylindrical ingot of Grade 2 titanium having approximate di~ensions of 5/8 inch in diameter by 3/4 inch tall was embedded within a ~ass of particulate boron nitride (UCAR HCM BN from Union Carbide, particle size smaller than ~8 mesh and larger than 200 mesh) contained within an alumina crucible. The upper surface of the titanium ingot was exposed to the atmosphere. The assembly, consisting of the alumina crucible and its contents, was placed within an electrical resistance heated furnace supplied with argon gas flowing at about l liter/minute.
I5 The assembly was heated to about 1750-C in approximately 4.5 hours, at which time the argon gas was replaced with forming gas (approximately 96x by volume N2 gas and 4% by volume H2 gas) flowing at about one liter/minute. The assembly was then maintained in the flowing forming gas at about 1750-C for about four hours.
The assembly was removed from the furnace after cooling for about 12 hours and visually examined. The examination indicated that the titanium parent metal had reactive~y infiltrated the boron nitride bed to form a self-supporting body having an interior cavity which, as shown in Figure 9, closely replicated the exterior surface of the cylindrical ingot of titanium.
A powdered sample of an interior section of the body was subjected to X-ray diffraction analysis. This analysis showed the presence of compounds of titanium with boron and nitrogen (such as TiB2 and TiN), thus confirming that the titanium parent metal had reacted with the boron nitride bedding material.

Claims

1. A method for producing a self-supporting body, comprising:
selecting a parent metal;
heating said parent metal in a substantially inert atmosphere to a temperature above its melting point to form a body of molten parent metal;
contacting said body of molten parent metal with a permeable mass comprising boron nitride;
maintaining said temperature for a time sufficient to permit infiltration of molten parent metal into said permeable mass and to permit reaction of said molten parent metal with said boron nitride to form at least one boron-containing compound; and continuing said infiltration and reaction for a time sufficient to produce said self-supporting body comprising at least one parent metal boron-containing compound.

2. A method for producing a self-supporting body, comprising:
selecting a parent metal;
heating said parent metal in a substantially inert atmosphere to a temperature above its melting point to form a body of molten parent metal;
contacting said body of molten parent metal with a permeable mass comprising boron nitride;
maintaining said temperature for a time sufficient to permit infiltration of molten parent metal into said permeable mass and to permit reaction of said molten parent metal with said boron nitride to form at least one nitrogen-containing compound; and continuing said infiltration and reaction for a time sufficient to produce said self-supporting body comprising at least one parent metal nitrogen-containing compound.

3. A method for producing a self-supporting body, comprising:
selecting a parent metal;
heating said parent metal in a substantially inert atmosphere to a temperature above its melting point to form a body of molten parent metal;

contacting said body of molten parent metal with a permeable mass comprising boron nitride;
maintaining said temperature for a time sufficient to permit infiltration of molten parent metal into said permeable mass and to permit reaction of said molten parent metal with said boron nitride to form at least one boron-containing compound and at least one nitrogen-containing compound; and continuing said infiltration and reaction for a time sufficient to produce said self-supporting body comprising at least one parent metal boron-containing compound and at least one parent metal nitrogen-containing compound.

4. The method according to claim l, wherein said parent metal comprises a metal selected from the group of metals consisting of aluminum, titanium, zirconium, hafnium, vanadium, chromium, niobium, tantalum, molybdenum and tungsten.

5. The method according to claim 2, wherein said parent metal comprises a metal selected from the group of metals consisting of aluminum, titanium, zirconium, hafnium, vanadium, chromium, niobium, tantalum, molybdenum and tungsten.

6 The method according to claim 3, wherein said parent metal comprises a metal selected from the group of metals consisting of aluminum, titanium, zirconium, hafnium, vanadium, chromium, niobium, tantalum, molybdenum and tungsten.