US20060189474A1

US20060189474A1 - Alumina-boron carbide ceramics and methods of making and using the same

Info

Publication number: US20060189474A1
Application number: US11/063,480
Authority: US
Inventors: Russell Yeckley; Shanghua Wu
Original assignee: Kennametal Inc
Current assignee: Kennametal Inc
Priority date: 2005-02-23
Filing date: 2005-02-23
Publication date: 2006-08-24
Also published as: US7217674B2; US20060188348A1; CN101166700A; JP2008537703A

Abstract

A ceramic body that contains between about 15 volume percent and about 35 volume percent of a boron carbide irregular-shaped phase and at least about 50 volume percent of alumina. The substrate has a fracture toughness (K_IC, 18.5 Kg Load E&C) greater than or equal to about 4.5 MPa·m^0.5.

Description

BACKGROUND OF THE INVENTION

The disclosure of the present patent application pertains to a ceramic body that contains alumina and boron carbide, as well as a method of making the same and a method of using the same. More specifically, the disclosure of the present patent application pertains to a ceramic body (for use as a ceramic cutting insert or a substrate for a coated ceramic cutting insert or a ceramic wear part) that contains alumina and a boron carbide phase, as well as a method (e.g., hot pressing) of making the same and a method of using the same.
Ceramic materials have been used as cutting inserts and as wear members for a number of years. These ceramic materials include silicon nitride or silicon nitride-based ceramics, SiAlON or SiAlON-based ceramics, and alumina or alumina-based ceramics. One of the first ceramic cutting inserts was an alumina cutting insert. See Dörre et al., “Alumina, Processing, Properties, and Applications”, Springer-Verlag (1984), pages 254-265. The alumina cutting insert was essentially over 99.7 percent alumina. Later on, the alumina ceramic was modified by the addition of titanium carbide. See Whitney, “Modern Ceramic Cutting Tool Materials”, Presentation at October, 1982 ASM Metals Congress in St. Louis, Mo.
Over the passage of time, there have been a number of other additives used in conjunction with alumina to form an alumina-based ceramic cutting insert. Examples of the additives include the use of silicon carbide whiskers such as the ceramics that appear to be disclosed in the U.S. Pat. No. 4,789,277 to Rhodes et al. and U.S. Pat. No. 4,961,757 to Rhodes et al. In an alumina-SiC whisker ceramic, the Rhodes et al. patents appears to show that the (K_IC) fracture toughness increased (4.15 to 8.9 MPa·m^0.5) as the SiC whisker content increased from 0 to 24 volume percent. The Rhodes et al. patents then appear to show that the fracture toughness decreased (8.9 to 7.6 MPa·m^0.5) as the SiC whisker content increased from 24 to 35 volume percent. European Patent No. 0 335 602 B1 to Lauder appears to disclose the use of silicon carbide whiskers in alumina along with the addition of additives like zirconia, yttria, hafnia, magnesia, lanthana or other rare earth oxides, silicon nitride, titanium carbide, titanium nitride or mixtures thereof. The use of silicon carbide whiskers along with alumina is described in Billman et al., “Machining with Al₂O₃—SiC Whisker Cutting Tools”, Ceramic Bulletin, Vol. 67, No. 6 (1988) pages 1016-1019. U.S. Pat. No. 4,343,909 to Adams et al. appears to disclose the use of zirconia and titanium diboride along with alumina (and a sintering aid). U.S. Pat. No. 4,543,343 to Iyori et al. discloses the use of titanium boride and zirconia along with alumina.
In the article written by Liu and Ownby (Liu et al. entitled “Physical Properties of Alumina-Boron Carbide Whisker/Particle Composites” Ceramic Eng. Sci. Proc. 12 (7-8) pp. 1245-1253 (1991) there is a disclosure of a ceramic comprising alumina and boron carbide particles. In this regard, the Liu et al. composites appear to disclose alumina (A16SG from Alcoa)-boron carbide particle (0.2 to 7 μm particles size) composites along with boron carbide that is present in amounts of 5.0, 10.0, 15.0 and 20.0 volume percent (the balance equals alumina). The examples were either sintered at 1500° C. or 1600° C. for 3 hours or hot-pressed under the hot pressing parameters that comprised a temperature equal to 1520° C. for a duration equal to 20 minutes. The sintered composites had a density less than 80 percent of the theoretical density. The hot pressed ceramics had a density of greater than 98 percent of the theoretical density. The hot pressing pressure seems to be absent from the disclosures of this Liu et al. article.
This Liu et al. article appears to show that the fracture toughness (measured by the Chevron Notched Short Rod (CNSR) technique) improves from 0 volume percent boron carbide particles to 5.0 volume percent boron carbide particles wherein the fracture toughness of the 5.0 volume percent boron carbide particle-alumina ceramic equals about 5.2 MPa·m^0.5. However, the fracture toughness drops off at boron carbide particle contents greater than 5.0 volume percent. More specifically, the fracture toughness diminishes at boron carbide particle contents of 10.0, 15.0 and 20.0 volume percent. The fracture toughness of the 20.0 volume percent boron carbide particle-alumina ceramic appears to equal about 4.5 MPa·m^0.5. Liu et al also shows that the flexural strength improves from 0 volume percent boron carbide particles to 5.0 volume percent boron carbide particles. The 5.0 volume percent boron carbide particle-alumina material has a flexural strength equal to about 575 MPa. The flexural strength levels off (i.e., remains essentially the same) at boron carbide particle contents greater than 5.0 volume percent (i.e., boron carbide particle contents of 10.0, 15.0 and 20.0 volume percent). The 20.0 volume percent boron carbide particle-alumina material has a flexural strength equal to about 590 MPa.
In the article (1991—American Institute of Physics) written by Liu et al. entitled “Boron Containing Ceramic Particulate and Whisker Enhancement of the Fracture Toughness of Ceramic Matrix Composites” there is a disclosure of a ceramic comprising alumina and boron carbide particles. These Liu et al composites appear to disclose α-alumina-boron carbide particle composites wherein the boron carbide is present in amounts of 5.0, 10.0, 15.0 and 20.0 volume percent (the balance equals alumina). The examples were hot-pressed under the hot pressing parameters that comprised a temperature equal to 1480° C. so that the ceramic had a density of greater than 98 percent of the theoretical density. The hot pressing duration and the hot pressing pressure appear to be absent from the disclosure of this Liu et al. article.
The Liu et al. articles show that the fracture toughness (CNSR technique) improves from 0 volume percent boron carbide particles to 5.0 volume percent boron carbide particles wherein the fracture toughness of the 5.0 volume percent boron carbide particle-alumina ceramic equals about 5.5 MPa·m^0.5. However, the fracture toughness drops off at boron carbide particle contents greater than 5.0 volume percent. More specifically, the fracture toughness diminishes at boron carbide particle contents of 10.0, 15.0 and 20.0 volume percent. The fracture toughness of the 20.0 volume percent boron carbide particle-alumina ceramic appears to equal about 4.6 MPa·m^0.5.
In the article written by Liu et al. entitled “Boron Carbide Reinforced Alumina Composites” Journal American Ceramic Society 74 (3) pp. 674-677 (1991)) there is a disclosure of a ceramic comprising alumina and boron carbide particles. The Liu et al. composites appear to disclose fine α-alumina (A16SG from Alcoa)-boron carbide “shard like” particle (0.2 to 7 μm particles size) composites along with boron carbide that is present in amounts of 5.0, 10.0, 15.0 and 20.0 volume percent (the balance equals alumina). The examples were hot-pressed under the hot pressing parameters that comprised a temperature equal to 1520° C. for duration equal to 20 minutes so that the ceramic had a density of greater than 98 percent of the theoretical density. The hot pressing pressure seems to be absent from the disclosures of the Liu et al. articles.
This Liu et al. article appears to show that the fracture toughness (CNSR technique) improves from 0 volume percent boron carbide particles to 5.0 volume percent boron carbide particles wherein the fracture toughness of the 5.0 volume percent boron carbide particle-alumina ceramic equals about 5.3 MPa·m^0.5. However, the fracture toughness drops off at boron carbide particle contents greater than 5.0 volume percent. More specifically, the fracture toughness diminishes at boron carbide particle contents of 10.0, 15.0 and 20.0 volume percent. The fracture toughness of the 20.0 volume percent boron carbide particle-alumina ceramic appears to equal about 4.6 MPa·m^0.5. Liu et al also shows that the flexural strength improves from 0 volume percent boron carbide particles to 5.0 volume percent boron carbide particles. The 5.0 volume percent boron carbide particle-alumina material has a flexural strength equal to about 580 MPa. The flexural strength levels off (i.e., remains essentially the same) at boron carbide particle contents greater than 5.0 volume percent (i.e., boron carbide particle contents of 10.0, 15.0 and 20.0 volume percent). The 20.0 volume percent boron carbide particle-alumina material has a flexural strength equal to about 600 MPa.
The Jung and Kim article entitled “Sintering and Characterization of Al₂O₃—B₄C composites”, Journal of Material Science 26 (1991) pp. 5037-5040 concerns the sintering of alumina-boron carbide composites. According to the article, for composites sintered at 1850° for 60 minutes the density was about 97 percent for a boron carbide content that ranged between 5 to 20 volume percent boron carbide. According to the Jung et al. article, the flexural strength had a maximum value of 550 MPa for an alumina-20 volume percent boron carbide composite that had been sintered at 1850° for 60 minutes. According to the Jung et al. article, for a composite sintered at 1850° for 60 minutes. The Vickers micro-hardness increased with increasing boron carbide content to 30 volume percent. For this same composite, the fracture toughness slightly increases with increasing boron carbide contents up to 20 volume percent. The maximum fracture toughness is 4 MPa·m_1/2.
Air Force Report AFML-TR-69-50 by E. Dow Whitney entitled “New and Improved Cutting Tool Materials” (1969) discloses an alumina-boron carbide composite. At page 119, the Report reads:

- The metal carbides, WC, TaC, TiC, B₄C and SiC were selected as additives for improving the general properties of hot presses alumina. Mixtures of Al₂O₃containing 1.25 wt. % of each additive were hot pressed at 1600° C., 2600 psi, for 30 minutes in a nitrogen atmosphere. In FIGS. 147 to 149 are shown the heating densification curves of these systems. Density increased rapidly from about 1200° C. and reached almost 100% relative density at temperatures below 1600° C.
  Table 52 of the Air Force Report appears to show that the addition of 1.25 weight percent boron carbide to alumina increased the MOR from 30,700 psi (for alumina) to 42,500 psi (alumina+1.25 weight percent boron carbide), but the hardness decreased from 94.2 (R_N15) to 93.7 (R_N15).

U.S. Pat. No. 5,271,758 to Buljan et al. pertains to an alumina-based composite that can include boron carbide and a Ni—Al metallic phase. Example 20 comprises” 8 v/o (Ni,Al), 27.6 v/o B₄C and 64.4 v/o Al₂O₃. U.S. Pat. No. '758 does not appear to specifically recite a hot pressing process for Example 20. PCT Patent Publication WO 92/07102 to Buljan et al. published Apr. 30, 1992) appears to be related to U.S. Pat. No. '758. U.S. Pat. No. 5,279,191 to Buljan appears to disclose an alumina-based ceramic that may include boron carbide. U.S. Pat. No. '191 requires the use of SiC reinforcement and a Ni—Al metal phase.
U.S. Pat. No. 5,162,270 to Ownby et al. pertains to an alumina ceramic that has boron carbide whisker reinforcement. FIG. 1 appears to show specific compositions in which the boron carbide whiskers appear to comprise 0, 5.0, 10.0, 15.0, 20.0 and 30.0 volume percent of the composite (the balance alumina). These samples were hot pressed at 1520° C. under a pressure equal to 7500 psi to achieve a density equal to greater than abut 98 percent of theoretical density. The maximum fracture toughness (about 7.1 MPa·m^0.5) occurs at 15.0 volume percent boron carbide whiskers. There is a slight decrease in the fracture toughness (about 7.1 MPa·m^0.5to about 7.0 MPa·m^0.5) when boron carbide whisker content exceeds 15 volume percent. U.S. Pat. No. 5,398,858 to Dugan et al. mentions the use of boron carbide whiskers to reinforce alumina. The specific application for the ceramic is in a roller guide.
The article by Liu and Ownby entitled “Densification of B₄C Whisker Reinforced Al₂O₃Matrix Composites”, Proceedings of the First China International Conference on High-Performance Ceramics (October, 1998, Beijing) pp. 415-419 pertains to the sintering of boron carbide whisker-alumina composites. The boron carbide whisker contents were (in volume percent): 0, 5, 10, 15, 20, 25, 30, 35 and 40.
The article by Liu et al. entitled “Enhanced Mechanical Properties of Alumina by Dispersed Titanium Diboride Particulate Inclusions”, Journal American Ceramic Society 74(1) pp. 241-243 (1991) discloses the use of titanium diboride particles to improve mechanical properties of alumina. FIG. 2 shows the impact of the boron carbide particle content in an alumina-based ceramic on the flexural strength wherein the boron carbide content ranges from 0 to 20.0 volume percent. Like in the other articles to Liu et al., the flexural strength appears to level off (or remain steady) for boron carbide contents that exceed 5.0 volume percent.
U.S. Pat. No. 4,745,091 to Landingham discloses an alumina-based ceramic that has a nitride modifier (e.g. AlN or Si₃N₄) and dispersion particles. A listing of the dispersion particles mentions boron carbide. According to the '091 patent, the nitride modifier can range from 0.1 to 15.0 weight percent, and the dispersion particles can range between 0.1 and 40.0 weight percent. There do not appear to be any actual examples that use boron carbide as dispersion particles.
U.S. Pat. No. 6,417,126 B1 to Yang discloses an alumina-based composite with a boride (e.g., boron carbide) and metal carbide (e.g., silicon carbide). The examples appear to disclose compositions comprising alumina, silicon carbide, and boron carbide wherein the boron carbide ranges between 0.5 and 5.4 weight percent. U.S. Pat. No. '126 appears to disclose that the principal use of the ceramic is an industrial blast nozzle. U.S. Patent Application Publication U.S. 2002/0195752 A2 to Yang appears to be related to U.S. Pat. No. '126. European Patent 0 208 910 to Suzuki et al. appears to disclose the use of boron carbide along with SiC whiskers in an alumina composite.
U.S. Pat. No. 5,164,345 to Rice et al. relates to an alumina-boron carbide-silicon carbide composite. The end product is the result of heating silicon dioxide, boron oxide, aluminum and carbon.
The article by Sato et al., “Sintering and Fracture Behavior of Composites Based on Alumina-Zirconia (Yttria)-Nonoxides”, Journal de Physique, Colloque C1, Supplement No. 2, Tome 47, February 1986 pp. C1-733 through C1-737 pertains to the sintering of alumina-containing composites including an alumina-zirconia-boron carbide composite. Table 1 of Sato et al. shows various properties of a 50 volume percent Al₂O₃-40 volume percent ZrO₂(no yttria)-10 volume B₄C composite, and an 80 volume percent Al₂O₃-10 volume percent ZrO₂(no yttria)-10 volume percent B₄C composite. Each composite was hot pressed at 1500° C. and 2 GPa for a duration of 30 minutes.
The article by Becher entitled “Microstructural Design of Toughened Ceramics” Journal American Ceramic Society 74(2) pp. 255-269 (1991) discusses toughening mechanisms. The principal toughening mechanism is crack-bridging. Additives include silicon carbide whiskers, tetragonal zirconia and monoclinic zirconia.
U.S. Pat. No. 4,474,728 to Radford and U.S. Pat. No. 4,826,630 to Radford each discloses pellets that comprise alumina and boron carbide. These pellets appear to be useful as neutron absorbers.
While there have been ceramic bodies that comprise alumina and boron carbide, there remains a need to provide an improved ceramic body that contains alumina and boron carbide, and especially alumina and a boron carbide irregular-shaped phase. There also remains the need to provide such a ceramic body of alumina and boron carbide that exhibits properties that are especially useful for metalcutting. Exemplary of these properties are the ability of the ceramic body to maintain its hardness even at higher operating temperatures, especially those temperatures associated with higher cutting speeds. Another exemplary property is the ability of the ceramic body to exhibit good chemical resistance with respect to the workpiece material even at high operating temperatures, especially those associated with higher cutting speeds. Each one of these properties by itself, and especially when combined together, provide for a ceramic body that is particularly useful as a ceramic cutting insert for applications at higher cutting speeds wherein there are generated higher operating temperatures. For example, a higher cutting speed contemplated by applicants for ductile cast iron could be a speed equal to or greater than about 1500 surface feet per minute (about 457 surface meters per minute), and more preferably, a higher cutting speed equal to or greater than about 2000 surface feet per minute (610 surface meters per minute).

SUMMARY OF THE INVENTION

In one form, the invention is a ceramic metalcutting insert for chip forming machining made from a starting powder mixture. The ceramic insert body comprises a substrate that has a rake surface and a flank surface wherein the rake surface and the flank surface intersect to form a cutting edge. The substrate comprises between about 15 volume percent and about 35 volume percent of a boron carbide irregular-shaped phase and at least about 50 volume percent of alumina. The substrate has a fracture toughness (K_IC) (18.5 Kg Load E&C) equal to or greater than about 4.5 MPa·m^0.5.
In still another form the invention is a process for making a ceramic (wherein the ceramic has a preferred application for cutting tool applications) comprising the steps of: providing a starting powder mixture that comprises between about 15 volume percent and about 35 volume percent of a boron carbide powder, and at least about 50 volume percent of alumina powder and no more than about 5 volume percent of a sintering aid; consolidating the powder mixture at a temperature equal to between about 1400 degrees Centigrade and about 1850 degrees Centigrade to achieve a ceramic with a density equal to or greater than 99 percent of the theoretical density.
In yet another form thereof, the invention is a ceramic body that comprises between about 15 volume percent and about 35 volume percent of a boron carbide irregular-shaped phase, and at least about 50 volume percent of alumina. The substrate has a fracture toughness (K_IC) (18.5 Kg Load E&C) equal to or greater than about 4.5 MPa·m^0.5.
In still another form thereof, the invention is a method of machining a workpiece comprising the steps of: providing a workpiece; providing a ceramic cutting insert having a rake surface and a flank surface wherein the rake surface and the flank surface intersect to form a cutting edge and the ceramic cutting insert having a substrate that comprises between about 15 volume percent and about 35 volume percent of a boron carbide phase and at least about 50 volume percent alumina and has a fracture toughness (K_IC, 18.5 Kg Load E&C) greater than or equal to about 4.5 MPa·m^0.5; causing relative rotational movement between the workpiece and the ceramic cutting insert wherein the surface speed of the relative rotational movement is equal to or greater than about 457 surface meters per minute; and bringing the ceramic cutting insert and the workpiece into contact with each other so as to remove material from the workpiece.

BRIEF DESCRIPTION OF THE DRAWINGS

The following is a brief description of the drawings wherein these drawings form a part of this patent application:
FIG. 1 is an isometric view of a ceramic cutting insert that embodies the invention;
FIG. 2 is a colorized photomicrograph (50 micrometer scale) that shows the microstructure of the ceramic body of Sample CA340-58 that has a starting composition of about 24.9 volume percent boron carbide powder, about 74.6 volume percent alumina powder, and sintering aid residue from 0.5 volume percent of ytterbia (i.e., ytterbium oxide) as a sintering aid in the starting powder mixture, and in the photomicrograph the light phase is boron carbide;
FIG. 3. is a photomicrograph (30 micrometer scale) that was made via scanning electromicroscopy (SEM) techniques that shows the microstructure the ceramic body of Sample CA340-59 that has a composition of about 25 volume percent boron carbide powder, about 74 volume percent alumina powder and sintering aid residue from 1.0 volume percent ytterbia (ytterbium oxide) as a sintering aid in the starting powder mixture, and in the photomicrograph the dark phase is the boron carbide and the light phase is a ytterbium-containing compound;
FIG. 4A is a colorized photograph (at a magnification equal to 30×) of the flank surface of a prior art ceramic cutting insert designated herein as Comparative Insert #1 [KYON 3400] showing the nature of the flank wear on the cutting insert after completion (duration of 6 minutes) of the testing set out in Table 5;
FIG. 4B is a colorized photograph (at a magnification equal to 30×) of the rake surface of a prior art ceramic cutting insert designated herein as Comparative Insert #1 [KYON 3400] showing the nature of the crater wear on the cutting insert after completion (duration of 6 minutes) of the testing set out in Table 5;
FIG. 5A is a colorized photograph (at a magnification equal to 30×) of the flank surface of Sample CA340-58 showing the nature of the flank wear on the cutting insert after completion (duration of 6 minutes) of the testing set out in Table 5; and
FIG. 5B is a colorized photograph (at a magnification equal to 30×) of the rake surface of Sample CA340-58 showing the nature of the crater wear on the cutting insert after completion (duration of 6 minutes) of the testing set out in Table 5.

DETAILED DESCRIPTION OF SPECIFIC EMBODIMENTS

Referring to the drawings, FIG. 1 shows an indexable ceramic cutting insert, i.e., a ceramic body, generally designated as 20. Ceramic cutting insert 20 comprises a substrate 21 that has a rake surface 22 and flank surfaces 24 wherein a cutting edge 26 is at the intersection of the rake surface 22 and the flank surfaces 24. Throughout this description, selected physical properties of the ceramic body (or ceramic substrate) are set forth. In regard to the method to determine these properties, the fracture toughness (K_IC) is determined by the method set forth in Evans & Charles, “Fracture Toughness Determination by Indentation”, J. American Ceramic Society, Vol. 59, Nos. 7-8, pages 371-372 using an 18.5 kilogram load. The Young's Modulus is determined by ASTM Standard E111-97 Standard Test Method for Young's Modulus, Tangent Modulus and Chord Modulus. The Vicker's micro-hardness is determined by ASTM Standard E384-99e1 Standard Test Method for Microindentation Hardness of Materials using an 18.5 kilogram load.
The ceramic substrate (or ceramic body) 21 of the ceramic cutting insert 20 has a composition that comprises primarily alumina and a boron carbide irregular-shaped phase along with optionally lesser amounts of additives such as, for example, sintering aid residue from an addition of sintering aid to the starting powder mixture. The sintering aid typically comprises in its broader range between about 0.05 volume percent and about 5 volume percent of the starting powder mixture. A preferable range for the sintering aid is between about 0.1 volume percent and about 1.5 volume percent of the starting powder mixture. A more preferable amount of sintering aid in the starting powder mixture is about 0.5 volume percent of the starting powder mixture. For the ceramic substrate, the content (in volume percent) of the alumina in the ceramic is greater than the content (in volume percent) volume percent of the boron carbide irregular-shaped phase in the ceramic. The content (in volume percent) of the boron carbide irregular-shaped phase in the ceramic is greater than any other component, except for the alumina in the ceramic.
Applicants contemplate that other additives may be added in amounts effective to improve the metalcutting performance characteristics (of the inventive ceramic cutting inserts) without undergoing a significant reaction with the boron carbide in the ceramic during the densification of the ceramic body. In this regard, these additives include one or more of the oxides of zirconium and/or hafnium and silicon carbide whiskers.
In one compositional range, the substrate 21 comprises between about 15 volume percent and about 35 volume percent of a boron carbide irregular-shaped phase and at least about 50 volume percent alumina and sintering aid residue. In another compositional range for the ceramic substrate, the substrate of the ceramic cutting insert comprises between about 15 volume percent and about 35 volume percent of a boron carbide irregular-shaped phase and between about 65 volume percent and about 85 volume percent alumina and sintering aid residue. In yet another compositional range for the ceramic substrate, the substrate of the ceramic cutting insert comprises between about 20 volume percent and about 30 volume percent of a boron carbide irregular-shaped phase and between about 70 volume percent and about 80 volume percent alumina and sintering aid residue. In still another composition of the ceramic substrate, the substrate comprises about 25 volume percent of a boron carbide irregular-shaped phase and about 75 volume percent alumina and sintering aid residue.
The ceramic substrate (or ceramic body) of the ceramic cutting insert exhibits certain physical properties. These physical properties include Young's Modulus (E), fracture toughness (K_IC) and Vicker's microhardness. Values for these properties are set forth hereinafter.
In one embodiment of the ceramic body, the fracture toughness (K_IC, 18.5 kg load Evans & Charles) is greater than or equal to about 4.5 MPa·m^1/2. In another embodiment of the ceramic body, the fracture toughness (K_IC, 18.5 kg load Evans & Charles) is greater than or equal to about 5.0 MPa·m^1/2. In another embodiment of the ceramic body, the fracture toughness (K_IC, 18.5 kg load Evans & Charles) is greater than or equal to about 5.5 MPa·m^1/2. In still another embodiment of the ceramic body, the fracture toughness (K_IC, 18.5 kg load Evans & Charles) is greater than or equal to about 6.0 MPa·m^1/2.
In one embodiment of the ceramic body, the Young's Modulus (ASTM Standard E111-97, Standard Test Method for Young's Modulus, Tangent Modulus and Chord Modulus) is greater than or equal to about 300 GPa. In another embodiment of the ceramic body, the Young's Modulus is greater than or equal to about 350 GPa. In yet another embodiment of the ceramic body, the Young's Modulus is greater than or equal to about 400 GPa.
In one embodiment of the ceramic body, the Vickers microhardness (ASTM Standard E384-99e1, Standard Test Method for Microindentation Hardness of Materials, 18.5 kg load) is greater than or equal to about 17 GPa. In another embodiment of the ceramic body, the Vickers microhardness is greater than or equal to about 18 GPa. In yet another embodiment of the ceramic body, the Vickers microhardness that is greater than or equal to about 19 GPa.
The ceramic body (after hot pressing) has a density that is greater than or equal to about 3.6 grams per cubic centimeter. This equates to a density that is greater than about 99.7 percent of the theoretical density for a composition that comprises about 25 volume percent of a boron carbide irregular-shaped phase and about 75 volume percent alumina and sintering aid residue.
Although the specific embodiment of FIG. 1 is a ceramic body that takes on the form of a substrate for an uncoated indexable ceramic cutting insert, applicants contemplate that the ceramic body has uses other than as a substrate for a ceramic cutting insert. In this regard, the ceramic body may have use as a substrate for a coated ceramic cutting insert including an indexable ceramic cutting insert. In addition, the ceramic body may have use as a wear member. Exemplary wear members include nozzles for shot blasting and abrasive water jet applications.
One useful technique to produce the ceramic body is hot pressing. However, applicants contemplate that any consolidation process that applies heat and (optionally) pressure for a sufficient duration of time to achieve the desired density can be an acceptable process. Sintering is another possible process to produce the ceramic body.
In general, the hot pressing process comprises the following steps that are described hereinafter. The first step comprises providing a starting powder mixture wherein the starting powder mixture has a composition that falls within one of the compositional ranges contemplated by the invention as set forth in this patent application. The basic components of the starting powder mixture are a majority content of alumina powder, a minority content of boron carbide powder, and a minor content (e.g., about 0.5 volume percent) of a sintering aid or in some cases, another additive as mentioned above (e.g., the oxides of zirconium and/or hafnium and/or silicon carbide whiskers). The sintering aid can comprise one or more materials that are suitable for use as a sintering aid for ceramics. Exemplary sintering aids include oxides such as, for example, yttrium oxide, yttrium aluminum garnet (YAG), ytterbium oxide, lanthanum oxide and chromium oxide.
The second step in the hot pressing process comprises hot pressing the starting powder mixture under pressure and heat to form the ceramic body. The hot pressing conditions are generally defined by the hot pressing temperature, hot pressing pressure and the duration of the hot pressing process. In regard to the hot pressing parameters, the hot pressing temperature has one range that is between about 1400 degrees Centigrade and about 1850 degrees Centigrade, as well as a narrower range that is between about 1400 degrees Centigrade and about 1700 degrees Centigrade. The hot pressing pressure has a range that is between about 20 MPa and about 50 MPa. The hot pressing duration has a range that is between about 20 minutes and about 90 minutes. The hot pressing process may occur under a vacuum (i.e., a pressure equal to or less than about 100 micrometers of mercury) or an inert gas atmosphere.
The hot pressing process produces a ceramic body that exhibits physical properties that include the fracture toughness (K_IC, 18.5 Kg Load E&C), the Young's Modulus and the Vickers hardness. The typical values of these properties have been set forth in this patent application.
Tests to determine selected physical properties (e.g., Young's Modulus, Vickers microhardness and fracture toughness (K_IC)), as well as metalcutting performance, were conducted on specific examples (or samples) of the ceramic body to compare the performance of specific examples of the alumina-boron carbide irregular-shaped phase ceramic cutting inserts against the performance of standard cutting inserts. The steps of the process employed to make the alumina-boron carbide irregular-shaped phase ceramic cutting inserts that were the subjects of the tests to determine the physical properties and the metalcutting performance are set forth below.
In regard to the specific powders used in the samples, for most of the examples, the boron carbide powder (which has a blocky-angular shape) was sold by Electro Abrasives (having a place of business at 701 Willet Road, Buffalo N.Y. 14218) under the designation F800 wherein the powder has the following properties: median particle size equal to about 15 micrometers, a surfaces area (as measured by BET) equal to 1.5 m²/gram, an oxygen content equal to 0.64 weight percent, the total boron content=77.5 weight %, the total carbon content=21.5 weight %, iron=0.2 weight %, and the total B+C content=98 weight %. Additional information about the boron carbide powders sold by Electro-Abrasives is available through the website: http:/www.electroabrasives.com/b4C.html.
The other kind of boron carbide powder, which is designated as “HP” in Table 1, was sold under the designation Grade HP by H.C. Starck, Inc. 45 Industrial Place, Newton, Mass. 02461. The Grade HP boron carbide powder has the following chemical characteristics: a B:C ratio=3.8-3.9, minimum of 21.8 weight % carbon, maximum of 0.7 weight nitrogen, maximum of 1.0 weight % oxygen, maximum of 0.05 weight % iron, maximum of 0.15 weight % of silicon, maximum of 0.05 weight percent aluminum, and a maximum of 0.5 weight % of other components. The Grade HP boron carbide powder has the following physical characteristics: specific surface area (TRISTAR 3000 by BET per ASTM D 3663)=6 to 9 m²/gram; green density (10³kg/cm²)=1.5 to 1.7 g/cm²; particle size distribution with typical values (MASTERSIZER by Laser Light Diffraction per ASTM B 822, deglomeration with high energy ultrasonic before analysis)=D90=6.5 micrometers, D50=2.5 micrometers, D10=0.4 micrometers. The above chemical characteristics and physical characteristics are available from the website http:/www.hcstarck.com and are set forth in the H.C. Starck Data Sheet Number PD-4012.
The alumina powder was sold by Baikowski International (having a place of business at 352 Westinghouse Blvd., Charlotte, N.C. 28273) under the designation SM8 wherein the powder has the following properties: BET specific surface area equal to 10 m²/gram, an alpha crystal structure, an alpha crystallite size/XRD=50 nanometers (nm), an ultimate particle size/TEM=400 nanometers (nm), and a purity greater than 99.99 percent. The agglomerate size distribution/sedigraph is: D20=0.2 micrometers; D50=0.3 micrometers; D90=0.7 micrometers. This information about the SM8 alumina powder is available at the website: http:/www.baikowski.com.
Another kind of alumina powder was used for at least one other example, and that was alumina powder sold under the designation “HPA-0.5” by Sasol North America, Inc., Ceralox Division, having a place of business at 7800 South Kolb Road, Tucson, Ariz. 85706. The HPA-0.5 alumina powder has the following properties: a purity equal to 99.99 weight percent; a surface area=9.0 m²/gram; a green density equal to 2.19 grams/cubic centimeter; and a particle size distribution of D90=1.2 micrometers, D50=0.4 micrometers and D10=0.2 micrometers. Additional information about the properties and the HPA-0.5 alumina powder can be found at the website: http:/www.ceralox.com/Documents/PDF files/TDS-ceramicpowders.pdf.
For the sintering aids, the yttrium oxide powder was sold by Molycorp Inc. (having a place of business at 67750 Bailey Road, Mountain Pass, Calif. 97366) wherein the powder had the following properties: surface area equal to 1.8 m²/gram, a particle size (Microtrac d50) equal to 3-6 micrometers (μm), and a purity equal to greater than 99.0 percent. The ytterbium oxide powder was sold by MolyCorp Inc. under the designation Yb₂O₃99% and has the following properties: particle size (FAPS) 3 μm max. and a purity greater than 99 percent. The lanthanum oxide powder was sold by MolyCorp Inc. under the designation La₂O₃99.99% and has the following properties: particle size (FAPS) 5-10 μm maximum and a purity greater than 99.9 percent. The YAG powder was sold by Cerac Inc. (having a place of business at P.O. Box 1178, Milwaukee, Wis. 53201-1178) under the designation Y-2000 and has the following properties: formula is Y₃Al₅O₁₂, average particle size −325 mesh and a purity greater than 99.9 percent.
To produce the starting powder mixture, the mixture of the starting powders of alumina and boron carbide and the sintering aid was subjected to ball-milling using high purity alumina cycloids for a duration equal to about 36 hours in alcohol. After completion of the ball-milling, the powder mixture was dried.
For all of the examples, each one of the starting powder mixture was hot pressed to form a ceramic body. For all of the examples, unless indicated to the contrary, the hot pressing was done using a graphite die and graphite rams, and the hot pressing parameters were a temperature equal to about 1650 degrees Centigrade for a duration of about 1 hour under a pressure of about 35 MPa. The ceramic body was then finished ground to form the geometries of the alumina-boron carbide irregular-shaped phase ceramic cutting inserts used in the metalcutting tests set forth below. The geometries of the ceramic cutting inserts are set forth in each of the tables.

Table 1 below sets forth the starting powder compositions for a number of the compositions that are contained in the Tables set forth hereinafter.

TABLE 1


Compositions of the Starting Powder Mixtures for the Samples
of the Ceramic Cutting Inserts as Reported in the Tables

		Boron Carbide
	Alumina (volume	Particles (volume	Additive (volume
Sample	percent)	percent)	percent)

CA340-30	74.6	(SM8)	24.9	(F800)	0.5 yttria
CA340-62	74.6	(SM8)	24.9	(HP)	0.5 yttria
CA340-57	74.6	(SM8)	24.9	(F800)	0.5 YAG
CA340-58	74.6	(SM8)	24.9	(F800)	0.5 ytterbia
CA340-63	74.6	(SM8)	24.9	(F800)	0.5 lanthanum oxide
CA340-67	74.6	(SM8)	24.9	(F800)	0.5 ytterbia
AA301-013	74.5	(HPA-0.5)	25	(F800)	0.5 yttria
CA340-59	74.25	(SM8)	24.75	(F800)	1.0 ytterbia

Table 1 sets forth herein above presents the compositions of the samples of the ceramic cutting inserts that were subjected to metalcutting tests, and testing for physical properties, wherein the test results are set forth in the Tables in this patent application. The compositions are reported in volume percent of the starting powder mixture. Except for Sample AA301-013, which used the Ceralox HPA-0.5 alumina powder, all of these samples used the SM8 alumina powder described earlier herein. The designation “F800” for the boron carbide powder means that the boron carbide powder was the F800 boron carbide powder from Electro-Abrasives described earlier herein. The designation “HP” for the boron carbide powder means the boron carbide powder was the HP boron carbide powder from H.C. Starck described earlier.

Table 2 set forth herein presents the results of measuring the Young's Modulus according to ASTM Standard E111-97 wherein the results are reported in gigapascals (GPa), the Vicker's Microhardness (18.5 kg load) according to ASTM Standard E384-99e1 wherein the results are reported in gigapascals (GPa), and the fracture toughness (K_IC) as measured according to Evans & Charles using an 18.5 kg load and reported in MPa·m^1/2.

TABLE 2


Room Temperature Properties for Selected Compositions

		Vickers
	Young's Modulus -	Microharadness	Fracture Toughness
Composition	E (GPa)	(VHN (GPa)	(K_IC) (MPa · m^1/2)

AA301-013	392	18.9	—
CA340-30	395	18.7	5.46
CA340-57	414	18.3	5.00
CA340-58	400	18.1	4.94
CA340-62	395	18.7	4.82
CA340-63	399	18.1	5.09

FIG. 2 is a colorized photomicrograph that shows the microstructure of the ceramic body of Sample CA340-58 that has a starting composition set forth in Table 1 and the Room Temperature properties set forth in Table 2. The light phase in the photomicrograph is the boron carbide phase. One can see that the boron carbide phase does present an irregular shape and the distribution of the boron carbide phase is relatively uniform throughout the microstructure. The darker goldish phase is the alumina.
FIG. 3. is a photomicrograph that was made via scanning electromicroscopy (SEM) techniques that shows the microstructure of the ceramic body of Sample CA340-59 that has a composition as set forth in Table 1. In this photomicrograph, the dark phase is the boron carbide phase. One can see that the boron carbide phase presents an irregular shape. It can be seen that the boron carbide phase appears to be about 6 micrometers or less, and more typically about 3 micrometers or less, in its major dimension. The light phase is a ytterbium-containing compound which is sintering aid residue. The gray phase is the alumina.
Table 3 set out below reports the results from turning a round clean bar of ductile cast iron (80-55-06) wherein these results show a comparison between a ceramic cutting insert of the invention (designated as Sample AA 301-013 wherein the starting powder composition is set forth in Table 1) and a number of comparative cutting inserts. The inventive ceramic cutting insert (Sample AA 301-013) has a composition of about 25 volume percent of a boron carbide irregular-shaped phase, about 74.5 volume percent alumina, and sintering aid residue from about 0.5 volume percent of yttria sintering aid in the starting powder mixture. Comparative Cutting Insert K090 has a composition that comprises about 30 volume percent titanium carbide and the balance (70 volume percent) alumina. Comparative Insert Kyon1615 has a composition that comprises 75 volume percent alumina-25 volume percent titanium carbonitride. The cutting insert that carries the designation LA 17/02 in the tables has a composition of 75 volume percent alumina-25 volume percent titanium carbonitride. The cutting insert that carries the designation CB347-216 has a composition of 42 volume percent alumina-43 volume percent titanium carbonitride-15 volume percent silicon carbide whiskers. The cutting insert that has the designation alumina-SiC whisker is a cutting insert that has a composition of about 15 volume percent silicon carbide whiskers and the balance (about 85 volume percent) alumina. Comparative Cutting Insert KYON 3400 is a chemical vapor deposition (CVD) coated silicon nitride substrate.

This metalcutting test comprised the turning of a round clean bar of ductile Cast Iron 80-55-06. The turning parameters were: a speed of 1500 surface feet per minute (457 surface meters per minute), a feed of 0.015 inches (0.38 millimeters) per revolution, and a depth of cut of 0.100 inches (2.54 millimeters) d.o.c. The metalcutting was dry, i.e., no coolant. The geometries of the cutting inserts are set forth in Table 3 below wherein the lead angle for all of the cutting inserts was 15 degrees. The geometries are identified according to the American National Standard for Cutting Tools-Indexable Inserts-Identification System, ANSI B212.4-1986. The failure criteria for this test is as follows: Flank Wear (UNIF)=0.020 inches (0.508 mm); Flank Wear (MAX)=0.020 inches (0.508 mm); Nose Wear=0.020 inches (0.508 mm); and Trailing edge wear=0.020 inches (0.508 mm).

TABLE 3


Metalcutting Test (TR9722A) Results for Turning at a Speed of 1500
Surface Feet Per Minute of Ductile Cast Iron 80-55-06 Using Different
Cutting Inserts

		Rep. 1	Rep. 2	Rep. 3
Tool		Tool	Tool	Tool	Mean T.L.
Material	Geometry	Life	Life	Life	(minutes)

AA301-013	SNG433T0425	6.6	3.4	5.1	5.0
KO90	SNG453T0820	0.8	0.3	—	0.4
KYON 1615	SNG453T0820	0.3	0.7	—	0.3
LA 17/02	SNG454T0825	1.3	3.0	—	1.4
CB347-216	SNG453T0425	2.0	3.3	3.0	2.8
Alumina-	SNG453T0820	4.7	4.1	2.0	3.6
SiC
Whisker
KYON 3400	SNG453T0820	—	3.1	3.1	3.1

As can be seen from the insert designations set forth in the second column from the left side in Table 3, the sizes, geometries and edge preparations for some of the cutting inserts were different. Based upon applicants' experience, and later verified by additional tests, these differences in sizes, geometries and edge preparations between the cutting inserts that were tested did not have a significant impact upon the test results. Hence, applicants believe that the test results reported in Table 3 comprise a fair comparison between cutting inserts of the invention and the other cutting inserts.
These test results show that the ceramic cutting insert of the invention (Sample AA301-013) exhibited superior tool life when cutting at a speed equal to 1500 sfm (457 smm) as compared to a number of other prior art ceramic cutting inserts. More specifically, the invention showed excellent crater wear and nose wear resistance, as compared with the comparative cutting inserts. The crater wear and nose wear resistance are the key factors for controlling the tool life when cutting (e.g., turning) at a high speed (e.g., a speed equal to 1500 sfm (457 smm)). In other words, better crater wear and nose wear properties result in a longer tool life for a ceramic cutting insert when cutting (e.g., turning) at a high speed (e.g., a speed equal to 1500 sfm (457 smm)).
Table 4 set out below reports the results from turning a round clean bar of ductile cast iron (80-55-06) wherein the results show a comparison between a ceramic cutting insert of the invention (designated as Sample CA340-67) and a comparative cutting insert (Kyon3400). Sample CA340-67 has a composition of about 24.9 volume percent of the boron carbide irregular-shaped phase, about 74.6 volume percent alumina, and sintering aid (ytterbia) residue that is from a starting powder content of sintering aid equal to about 0.5 volume percent. The turning parameters were: a speed of 2000 surface feet per minute (609.6 surface meters per minute), a feed of 0.015 inches (0.38 millimeters) per revolution, and a depth of cut of 0.100 inches (2.54 millimeters) d.o.c. The metalcutting was dry, i.e., no coolant. The geometries of the cutting inserts are set forth in Table 4 below wherein the lead angle for all of the cutting inserts was 15 degrees. The failure criteria for this test is as follows: Flank Wear (UNIF)=0.020 inches (0.508 mm); Flank Wear (MAX)=0.020 inches (0.508 mm); Nose Wear=0.020 inches (0.508 mm); and Trailing Edge Wear=0.020 inches (0.508 mm).

TABLE 4

Metalcutting Test (T11338) Results (tool life in minutes) for Turning at

a Speed of 2000 Surface Feet Per Minute of Ductile Cast Iron 80-55-06

Tool Life Mean Tool

Tool Material Geometry Rep 1 Rep 2 Life (minutes)

Kyon 3400 SNGN433T0820 2.5 3.9 3.2

CA340-67 SNGN433T0820 8.0 7.7 7.8

The inventive ceramic cutting insert (Sample CA340-67) significantly outperformed the cutting insert of the comparative grade (KYON 3400). Applicants believe that this improvement in performance was due to the superior chemical wear resistance provided by the inventive ceramic cutting inserts at higher cutting speeds (e.g., 2000 sfm (610 smm)) wherein at such higher cutting speeds, the chemical wear exerts great influence over (i.e., dominates) the tool life.
Additional metalcutting test results demonstrate the performance of specific samples of the ceramic cutting insert of the invention. These test results are set forth below.

Except for the speed, each one of the tests referred to in Tables 5 and 6 was conducted at the following parameters: the feed equal to 0.015 inches (0.381 millimeters); the Depth of cut (DOC) equal to 0.100 inches (2.54 mm); and the coolant: dry. The speed for the tests reported in Table 5 was 1500 feet per minute (457 meters per minute) and the speed for the tests reported in Table 6 was 2000 feet per minute (610 meters per minute). For each of the tests, the geometry of the cutting insert was a SNG433T0820 style of cutting insert that had a negative 5 degree lead angle. The workpiece material was a round clean bar of ductile cast iron (80-55-06). The failure criteria for these tests set forth in Tables 5 and 6 were as follows: Flank Wear (UNIF)=0.020 inches (0.508 mm); Flank Wear (MAX)=0.020 inches (0.508 mm); Nose Wear=0.020 inches (0.508 mm); and Trailing Edge Wear=0.020 inches (0.508 mm).

TABLE 5


T10828_Turning DCI 80-55-06
SNG-433T0820/1500 sfm/.015 ipr/.1″ doc/dry

Average Insert Wear After 6 min. Turning

Mean Tool

Insert #	FW	MW	NW	TW	Life (min)

1. KYON 3400	0.0124	0.0170	0.0190	0.0146	5.6
2. CA340-30	0.0143	0.0173	0.0165	0.0153	6.8
3. CA340-62	0.0139	0.0205	0.0154	0.0138	5.0
4. CA340-57	0.0130	0.0161	0.0148	0.0152	7.2
5. CA340-58	0.0129	0.0150	0.0152	0.0154	7.0
6. CA340-63	0.0125	0.0153	0.0153	0.0153	7.4

In Table 5 above, the designations “FW” means average flank wear reported in inches, “MW” means average maximum flank wear reported in inches, “NW” means average nose wear reported in inches, and “TW” means average trailing edge wear reported in inches. The mean tool life is reported in minutes.

Referring to the test results presented in Table 5 above, it is apparent that, for the most part, the ceramic cutting inserts of the invention outperformed the KYON 3400 ceramic cutting insert. The KYON 3400 cutting insert is a commercial cutting insert that is well-accepted for the use in the turning of ductile cast iron. More specifically, except for Insert No. 3 (Sample CA340-62) which had a mean tool life equal to about 89.2 percent of the mean tool life of the KYON 3400 cutting insert, all of the ceramic cutting inserts demonstrated an improved mean tool life. In this regard, Insert No. 2 (Sample CA340-30) had a mean tool life equal to about 121.4 percent of the mean tool life of the KYON 3400 cutting insert, Insert No. 4 (Sample CA340-57) had a mean tool life equal to about 128.6 percent of the mean tool life of the KYON 3400 cutting insert, Insert No. 5 (Sample CA340-58) had a mean tool life equal to 125 percent of the mean tool life of the KYON 3400 cutting insert, and Insert No. 6 (Sample CA340-63), which used the lanthanum oxide sintering aid, had a mean tool life equal to about 132.1 percent of the mean tool life of the KYON 3400 cutting insert.
Based upon a comparison of the test results for Insert No. 2 and Insert No. 3, it appears that the ceramic cutting insert that used the F800 boron carbide (from Electro-Abrasives) had better results (i.e., a longer mean tool life) than the ceramic cutting insert that used the HP boron carbide (from H.C. Starck).
A comparison of the test results for an alumina-boron carbide irregular-shaped phase ceramic cutting insert using yttria as the sintering aid (i.e., Insert No. 2) against the alumina-boron carbide irregular-shaped phase ceramic cutting inserts using other sintering aids shows that these other sintering aids (i.e., YAG, ytterbium and La₂O₃) provided for improved results in the form of a longer mean tool life.
FIGS. 4A and 5A illustrate the comparison of the flank wear properties between a Comparative Insert #1 and a cutting insert of the invention (Sample CA340-58). More specifically, FIG. 4A is a colorized photograph (at a magnification equal to 30×) of the flank surface of the Comparative Insert #1 [KYON 3400] showing the nature of the flank wear on the cutting insert after completion (duration of 6 minutes) of the testing set out in Table 5. FIG. 5A is a colorized photograph (at a magnification equal to 30×) of the flank surface of Sample CA340-58 showing the nature of the flank wear on the cutting insert after completion (duration of 6 minutes) of the testing set out in Table 5. It is apparent from an examination of the cutting inserts shown in FIGS. 4A and 5A, that the inventive cutting insert experienced less flank wear and a more uniform flank wear than did the prior art comparative cutting insert (Comparative Insert #1).
FIGS. 4B and 5B show a comparison of the crater wear properties between a Comparative Insert #1 and a cutting insert of the invention (Sample CA340-58). More specifically, FIG. 4B is a colorized photograph (at a magnification equal to 30×) of the rake surface of the Comparative Insert #1 [KYON 3400] showing the nature of the crater wear on the cutting insert after completion (duration of 6 minutes) of the testing set out in Table 5. FIG. 5B is a colorized photograph (at a magnification equal to 30×) of the rake surface of Sample CA340-58 showing the nature of the crater wear on the cutting insert after completion (duration of 6 minutes) of the testing set out in Table 5. It is apparent from an examination of FIGS. 4B and 5B that the inventive cutting insert (Sample CA340-58) experienced less crater wear than did the prior art cutting insert (Comparative Insert #1).
Metalcutting tests also show that the inventive ceramic cutting inserts exhibit better performance (i.e., tool life) at even higher cutting speeds, e.g., on the order of 2000 sfm (610 smm). In this regard, Table 6 below sets forth the results for the turning of ductile cast iron at the parameters (including a speed equal to 2000 sfm (610 smm)) set forth by cutting inserts of the geometry (SNG-433T0820) presented in Table 6. As seen by the results presented in Table 6, the inventive cutting inserts exhibit a much greater mean tool life than the KYON 3400 cutting insert. More specifically, the Insert No. 2 (Sample CA340-30), which is an alumina-boron carbide irregular-shaped phase ceramic cutting insert that used the F800 boron carbide, had a mean tool life equal to 244 percent of the mean tool life of the KYON 3400 ceramic cutting insert. Insert No. 5 (Sample CA340-58), which is an alumina-boron carbide irregular-shaped phase ceramic cutting insert that used ytterbia as the sintering aid, had a mean tool life that was 292 percent of the mean tool life of the KYON 3400 ceramic cutting insert.

TABLE 6

Mean Tool Life Reported in Minutes

T10919_Turning DCI 80-55-06

SNG-433T0820/2000 sfm/.015 ipr/.1″ doc/dry

Insert # Test No. 1 Test No. 2 Mean Tool Life (min)

1. KYON 3400 3.0 1.9 2.5

2. CA340-30 7.4 4.7 6.1

5. CA340-58 7.5 7.0 7.3

6. CA340-63 4.5 6.6 5.5
When increasing the turning speeds from 1500 sfm (457 m/min) to 2000 sfm (610 m/min), as shown in metal cutting test T10919 (Table 6 below), the performance of KY3400 degraded considerably while the influence of speeds on the performance of alumina-boron carbide composites was not so significant. The cutting insert (Sample CA340-63) that used lanthanum oxide as the sintering aid had a mean tool life that was over twice as long (i.e., 5.5 minutes vs. 2.5 minutes) as the mean tool life for the KYON 3400 cutting insert.
Overall, it is apparent that applicants have invented a new and useful ceramic body that comprises alumina and a boron carbide irregular-shaped phase, and optionally, the sintering aid residue from a sintering aid contained in the starting powder mixture. The ceramic body can be used as a wear member, as well as an uncoated ceramic cutting insert or a coated ceramic cutting insert.
When used as a ceramic cutting insert, the ceramic substrate has maintained its wear resistance even at higher operating temperatures, especially those temperatures associated with higher cutting speeds (e.g., a speed equal to or greater than about 1500 sfm (457 smm), or at even higher cutting speeds equal to or greater than about 2000 sfm (610 smm)). The ceramic substrate has also been able to exhibit good chemical resistance with respect to the workpiece material.
These improved properties demonstrate that overall the alumina-boron carbide irregular-shaped phase ceramic cutting inserts of the invention outperform (as measured by mean tool life in the turning of ductile cast iron) the conventional commercial ceramic cutting insert (a CVD coated silicon nitride cutting insert). This is especially true at higher cutting speeds in the order of 2000 sfm (610 smm). This is also markedly apparent when the sintering aid comprises a material like YAG or Yb₂O₃or La₂O₃or Y₂O₃.
All patents, patent applications, articles and other documents identified herein are hereby incorporated by reference herein. Other embodiments of the invention may be apparent to those skilled in the art from a consideration of the specification or the practice of the invention disclosed herein. It is intended that the specification and any examples set forth herein be considered as illustrative only, with the true spirit and scope of the invention being indicated by the following claims.

Claims

1. A ceramic metalcutting insert for chip forming machining made from a starting powder mixture, the ceramic insert body comprising:

a substrate having a rake surface and a flank surface wherein the rake surface and the flank surface intersect to form a cutting edge;

the substrate comprising between about 15 volume percent and about 35 volume percent of a boron carbide irregular-shaped phase and at least about 50 volume percent alumina; and

the substrate having a fracture toughness (K_IC, 18.5 Kg Load E&C) greater than or equal to about 4.5 MPa·m^0.5.

2. The ceramic metalcutting insert according to claim 1 wherein the substrate has a fracture toughness (K_IC, 18.5 Kg Load E&C) greater than or equal to about 5.5 MPa·m^0.5.

3. The ceramic metalcutting insert according to claim 1 wherein the substrate has a Young's Modulus equal to or greater than about 300 GPa.

4. The ceramic metalcutting insert according to claim 1 wherein the substrate has a Vicker's micro-hardness equal to or greater than about 17 GPa.

5. The ceramic metalcutting insert according to claim 1 wherein the substrate comprises between about 15 volume percent and about 35 volume percent of the boron carbide irregular-shaped phase and between about 65 volume percent and about 85 volume percent alumina.

6. The ceramic metalcutting insert according to claim 1 wherein the substrate comprises between about 20 volume percent and about 30 volume percent of the boron carbide irregular-shaped phase and between about 70 volume percent and about 80 volume percent alumina.

7. The ceramic metalcutting insert according to claim 1 wherein the substrate comprises about 25 volume percent of the boron carbide irregular-shaped phase and about 75 volume percent alumina.

8. The ceramic metalcutting insert according to claim 1 wherein the substrate further comprises residue from a sintering aid in the starting powder mixture and the sintering aid is selected from the group comprising yttrium oxide, ytterbium oxide, yttrium aluminum garnet, lanthanum oxide, and chromium oxide.

9. The ceramic metalcutting insert according to claim 1 wherein the substrate further includes the constituents from one or more of the following additives in the starting powder mixture: the oxides of hafnium and/or zirconium, and silicon carbide whiskers.

10. The ceramic metalcutting insert according to claim 1 further including a refractory coating on the substrate.

11. A process for making a ceramic body comprising the steps of:

providing a starting powder mixture,

the starting powder mixture comprises between about 15 volume percent and about 35 volume percent boron carbide powder and at least about 50 volume percent alumina powder and no more than about 5 volume percent of a sintering aid; and

consolidating the powder mixture at a temperature equal to between about 1400 degrees Centigrade and 1850 degrees Centigrade to achieve a ceramic with a density equal to greater than 99 percent of theoretical density.

12. The process according to claim 11 wherein the consolidating conditions further comprise a hot pressing pressure equal to between about 30 MPa and about 40 MPa.

13. The process according to claim 11 wherein the consolidating conditions further comprise a hot pressing duration equal to between about 30 minutes and about 90 minutes.

14. The process according to claim 11 wherein the ceramic body has a fracture toughness (K_IC, 18.5 Kg Load E&C) greater than or equal to about 4.5 MPa·m^0.5.

15. The process according to claim 11 wherein the ceramic body has a Young's Modulus greater than or equal to about 300 GPa.

16. The process according to claim 11 wherein:

the starting powder mixture comprises between about 20 volume percent and about 30 volume percent of the boron carbide powder and between about 70 volume percent and about 80 volume percent of the alumina powder.

17. The process according to claim 11 further including the step of applying a coating to the ceramic body.

18. A ceramic body comprising:

between about 15 volume percent and about 35 volume percent of a boron carbide irregular-shaped phase, and at least about 50 volume percent alumina, and

the ceramic body has a fracture toughness (K_IC, 18.5 Kg Load E&C) greater than or equal to about 4.5 MPa·m^0.5.

19. The ceramic body according to claim 18 wherein the body further includes the residue from a sintering aid.

20. A method of machining a workpiece comprising the steps of:

providing a workpiece;

providing a ceramic cutting insert having a rake surface and a flank surface wherein the rake surface and the flank surface intersect to form a cutting edge and the ceramic cutting insert having a substrate that comprises between about 15 volume percent and about 35 volume percent of a boron carbide phase and at least about 50 volume percent alumina and has a fracture toughness (K_IC, 18.5 Kg Load E&C) greater than or equal to about 4.5 MPa·m^0.5;

causing relative rotational movement between the workpiece and the ceramic cutting insert wherein the surface speed of the relative rotational movement is equal to or greater than about 457 surface meters per minute; and

bringing the ceramic cutting insert and the workpiece into contact with each other so as to remove material from the workpiece.

21. The method of claim 20 wherein the surface speed of the relative rotational movement is equal to or greater than about 610 surface meters per minute.

22. The method of claim 20 wherein the workpiece material is cast iron.

23. The method of claim 20 wherein the workpiece material is ductile cast iron.