GB2263704A - Heat-resistant sintered hard alloy - Google Patents
Heat-resistant sintered hard alloy Download PDFInfo
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- GB2263704A GB2263704A GB9201927A GB9201927A GB2263704A GB 2263704 A GB2263704 A GB 2263704A GB 9201927 A GB9201927 A GB 9201927A GB 9201927 A GB9201927 A GB 9201927A GB 2263704 A GB2263704 A GB 2263704A
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- weight
- cobalt
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
- C22C32/0047—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents
- C22C32/0073—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents only borides
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C29/00—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides
- C22C29/14—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on borides
Abstract
A heat-resistant sintered hard alloy comprises 35% to 95% by weight of a WCoB type complex boride in a cobalt base alloy. The alloy may contain 1.5% to 4.1% boron, 19.1% to 69.7% tungsten, optionally 1 to 25% chromium, the balance being cobalt and a maximum of 1% impurities. Nickel (0.2 - 30%), iron (0.2 - 15%) and/or copper (0.1 - 7.5%) may be substituted for portions of the cobalt content.
Description
HEAT-RESISTANT SINTERED HARD ALLOY
The present invention relates to a heat-resistant sintered hard alloy, composed of a hard phase consisting mainly of a WCoB type complex boride, and a cobalt base alloy matrix phase binding the hard phase which hard alloy exhibits excellent room temperature characteristics as well as excellent high temperature characteristics such as high temperature strength and oxidation resistance, and as a hot extruding die for a copper rod.
Requirements for wear-resistant sintered hard materials have become increasingly severe, and the industry has sought improved materials having wear-resistance as well as heat-resistance and corrosion resistance or the like.
As sintered hard materials, carbides, nitrides and carbonitrides such as WC base hard alloys and TiCN type cermets are well known. As substitute materials for the aforementioned hard materials, hard alloys and cermets including metallic borides such as WB and TiB2, and metallic complex borides such as Mo2FeB2 and Mo2NiB2 have been recently proposed, noting excellent properties of borides such as extreme hardness, high melting point and high electric conductivity. Further, stellites are utilized as cobalt base wear-resistant materials.
A hard alloy formed by binding WB with a nickel base alloy such as disclosed in Japanese Patent Publications No. Sho 56-45985, No. Sho 56-45986 and No. Sho 56-45987 is a paramagnetic wear-resistant material to be used especially in watch cases and ornaments, and is not intended for structural materials to be used at high temperature.
Ceramics comprising metallic borides such as TiB2 as disclosed in Japanese Patent Publications No. Sho 61-50909 and No. Sho 63-5353 exhibit extreme hardness and pronounced heat resistance, but impart poor thermal shock resistance due to there being no metallic binding matrix phase.
Generally, hard materials formed by adding metals to metallic borides suffer from the disadvantage in that they tend to form a brittle third phase, and it is difficult to obtain high strength or toughness.
Hard alloys comprising metallic complex borides such as
Mo2FeB2 and Mo2NiB2 formed by reaction during sintering have been developed to eliminate the above disadvantage.
A Mo2FeB2 type hard alloy disclosed in Japanese Patent
Publication No. Sho 60-57499 has excellent mechanical properties, wear-resistance and corrosion resistance at room temperature but unsatisfactory high temperature strength and oxidation resistance due to its iron base binding matrix phase.
A Mo2NiB2 type hard alloy disclosed in Laid Open Japanese
Patent application No. Sho 62-196353 has excellent high temperature properties and corrosion resistance, but poor wear-resistance and anti adhesion property, since the complex boride Mo2NiB2 is about 15 GPa at micro-Vickers hardness and is not so hard, and its binding phase consists of nickel base alloy. Stellites exhibit excellent high temperature properties, but their hardness is too low to be used for wear-resistant materials.
It is an object of the present invention to provide a sintered hard alloy having excellent room temperature properties as well as pronounced high temperature properties such as high temperature strength and oxidation resistance.
According to the present invention, there is provided a heatresistant sintered hard alloy comprising 35 to 95% by weight of a
WCoB type complex boride and a cobalt base alloy matrix phase. The hard alloy may consist of boron of 1.5 to 4.1% by weight, tungsten of 19.1 to 69.7% by weight with the balance being cobalt and unavoidable impurities. In addition to the above elements, the hard alloy may contain chromium of 1 to 25% by weight for the improvement of mechanical properties and corrosion resistance.
Further, the hard alloy may comprise boron of 1.5 to 4.1% by weight, ungsten of 19.1 to 69.7% by weight, chromium of 1 to 25% by weight, and at lest one of nickel, iron and copper. Nickel, when present, substitutes for cobalt in the range of 0.2 to 30% by weight of cobalt content. Iron, when present, substitutes for cobalt in the range of 0.2 to 15% by weight of cobalt content.
Copper, when present, substitutes for cobalt in the range of 0.1 to 7.5% by weight of cobalt content. The balance of this alloy consists of cobalt and unavoidable impurities.
In this description, WCoB and a complex boride identified as
WCoB by means of x-ray diffraction comprising tungsten and cobalt, in which part of tungsten may be replaced by chromium and part of the cobalt may be replaced by chromium, nickel, iron or copper2 will be referred to as a WCoB type complex boride.
The WCoB type complex boride offers the following advantages.
The formation of a brittle third phase, which tends to be formed in a boride base hard alloy, can be suppressed by forming the WCoB type complex boride by reaction during sintering. The micro
Vickers hardness of the WCoB type boride is larger than 30 GPa, and higher than those of other metallic complex borides such as Mo2FeB2 and Mo2NiB2, and the same as or higher than those of carbides and nitrides which are currently used for hard materials. Further, the
WCoB type complex boride has excellent oxidation resistance.
In the case where the content of the WCoB type complex boride is less than 35% by weight, the wear resistance of the hard alloy is reduced due to the insufficient amount of the complex boride, and is liable to marked deformation at high temperature due to insufficient development of complex boride networks in the cobalt base alloy matrix phase. On the other hand, in the case where the content of the WCoB type complex boride is more than 95% by weight, the strength of the hard alloy is remarkably decreased, though its hardness is increased. For the above reason, it is preferable that the content of the WCoB type complex boride be 35 to 95% by weight.
Boron is an essential element for forming the WCoB type complex boride in the heat-resistant sintered hard alloy. With boron less than 1.5% by weight, the complex boride is less than 35% by weight, and with boron more than 4.1% by weight, the complex boride is over 95% by weight, leading to a pronounced decrease in the strength of the hard alloy. For the above reason, it is preferable that the amount of boron in the hard alloy be from 1.5 to 4.1% by weight.
Tungsten is also an essential element for forming the WCoB type complex boride. The stoichiometric ratio in the WCoB type complex boride is generally such that W:Co:B = 1:1:1. The WCoB type complex boride which is practically applicable, however, need not be a perfectly stoichiometric compound, but may have a composition variance of a few percent. Accordingly, the molecular ratio of W/B (hereafter will be referred to as W/B ratio) need not be 1, but it is important that the W/B ratio be within a specific range including 1 as the approximate centre.
Test results indicate that in the case where the W/B ratio is far smaller than 1, cobalt borides such as Co2B are formed, and in the case where the W/B ratio is far larger than 1, intermetallic compounds of tungsten and cobalt such as W6Co7 are formed, leading to a decrease in the strength of the hard alloy in both cases.
When the W/B ratio is within the range of 0.75 to 0.135 x (11.5-X), where X indicates the content of boron by weight percent, even if the above third phase is formed, the third phase will little affect the strength of the hard alloy; i.e., there would be an allowable decrease in the strength.
In the case where the W/B ratio is larger than 1, part of excess tungsten will be solid solute into the cobalt base alloy matrix phase, which will strengthen the matrix phase, thus improving the mechanical properties of the heat-resistant sintered hard alloy. However, since the amount of the cobalt base alloy matrix phase decreases with the increase of the amount of the WCoB type complex boride; it is necessary to decrease the amount of said excess tungsten in the matrix phase accompanied by the above increase, so as to maintain the strength of the hard alloy.
For the above reason, it is preferable that the upper limit of the amount of tungsten be 1.35 in terms of the W/B ratio in the case where the amount of boron is lowest (1.5t by weight), and 1 in terms of the W/B ratio in the case where the amount of boron is highest (4.1% by weight). This range is represented by the formula 0.135 x (11.5-X), in which X is the weight percent of boron.
Accordingly, it is desirable that the amount of tungsten in the hard alloy be in the range of from 0.75 to 0.135 x (11.5-X), preferably in the range of 0.8 to 0.135 x (ll.5-X) in terms of the
W/B ratio; that is, from 19.1 to 69.7% by weight, preferably from 20.4 to 69.7% by weight, in said hard alloy.
In the case of a sintered hard alloy containing chromium, it is presumed that chromium will be solid solute into the WCoB type complex boride, and form a (WxCoyCr B multiple boride of the WCoB type complex boride, in which cobalt rather than tungsten is replaced partially by chromium and x + y + z is equal to 2, and further chromium will be solid solute into the cobalt base alloy matrix also, so that the resistances to corrosion, heat and oxidation of the sintered hard alloy will be improved.
Furthermore, chromium refines the (WxCoyCrz)B multiple boride phase and improves the mechanical properties of the sintered hard alloy. With a content of chromium below 1% by weight, the abovementioned improvement can not be attained, and with the content of chromium above 25% by weight, the mechanical properties of the sintered~hard alloy are remarkably decreased due to the generation of a brittle phase such as a CoCr sigma (a) phase. Accordingly, it is preferable that the content of chromium be from 1 to 25% by weight.
In the case of a sintered hard alloy containing nickel, it is presumed that nickel will substitute for cobalt and be solid solute into the cobalt base alloy matrix phase, and improve the mechanical properties, corrosion resistance and heat-resistance of the hard alloy. With the substitution of nickel below 0.2% by weight of cobalt content, the aforementioned improvements of mechanical properties and the like can not be attained, and with the substitution of nickel above 30% by weight of cobalt, abrasion resistance is reduced due to the decrease of hardness.
Accordingly, it is preferable that nickel substitute for cobalt in the range of 0.2 to 30 % by weight of cobalt content.
Iron substitutes mainly for cobalt in the WCoB type complex boride and the cobalt base alloy matrix phase, and improves the strength at low temperature. With the substitution of iron below 0.2 by weight of cobalt content, the aforementioned improvement is not attained, and with the substitution of iron more than 15% by weight of cobalt content, the hard alloy becomes less resistant to corrosion, heat and oxidation. Accordingly, in the case of the sintered hard alloy containing iron, it is preferable that iron substitute for cobalt in the range of 0.2 to 15% by weight of cobalt content.
Copper substitutes for cobalt and is solid solute into the cobalt base alloy matrix phase, and improves the corrosion resistance and heat conductivity of the sintered hard alloy. With the substitution of copper below 0.1 by weight of cobalt content, the above improvements are not attained, and with the substitution of copper more than 7.5% by weight of cobalt content, the mechanical properties and heat-resistance are degraded.
Accordingly, it is preferable that copper substitute for cobalt in the range of 0.1 to 7.5% by weight of cobalt content, when copper is added to the sintered hard alloy.
The unavoidable impurities contained in the sintered hard alloy are mainly silicon, aluminum, manganese, magnesium, phosphorus, sulfur, nitrogen, oxygen, carbon or the like, and it is desirable that the content of these impurity elements be as little as possible. However, in the case where the total amount of these impurity elements is less than 1.0% by weight, the detrimental effects thereof to the properties of the sintered hard alloy are relatively small. Accordingly, it is preferable that the total content of the unavoidable impurities be less than 1 0% by weight, more preferably less than 0.5% by weight.
In the case where the sintered hard alloy is employed for a wear-resistant coating in which the strength is not of critical importance-, and silicon and aluminum or the like are added intentionally so as to improve the oxidation resistance of the coating, the total content of the aforementioned elements may be over 1.0% by weight.
The sintered hard alloy is made by mixing boride powders of tungsten, cobalt, chromium, nickel and iron; alloy powders of boron, with at least one of tungsten, cobalt, chromium, nickel, iron and copper; or boron powder and metal powders of tungsten, cobalt, chromium, nickel, iron and copper, or- alloy powders containing at least two of these metallic elements, thereafter wet milling the mixture with an organic solvent by means of a vibrating ball mill or the like, drying, granulating, and forming, followed by liquid phase sintering of the green compact in a non-oxidizing atmosphere such as in vacuum, a reducing gas, or an inert gas.
The hard phase, that is the WCoB type complex boride of the sintered hard alloy, is formed by the reaction during sintering.
A powder mixture obtained by blending metal powders such as cobalt, chromium and nickel to form the Co base alloy matrix phase, with the WCoB type complex boride such as WCoB and (WxCoyCrz)B which are prepared by reacting tungsten boride, cobalt boride, boron powder with metal powders such as tungsten, cobalt and chromium etc. in a furnace in advance, may be employed as the raw material powders also.
The liquid phase sintering is usually carried out at the temperature range of 1100 to 14000C and for 5 to 90 minutes depending on the composition of the hard alloy. A hot press method, a hot isostatic pressing method, and an electric resistance sintering method or the like may be also employed.
EXAMPLES
The compound powders listed in Table 1 and metal powders listed in Table 2 were blended in the compositions shown in Table 3 with the blending ratios shown in Table 5. The blended powders were wet milled with acetone by means of a vibrating ball mill for 28 hours and then dried and granulated. The powders thus obtained were pressed into a predetermined shape. The green compacts were sintered at the temperature of 1150 to 13000C for 30 minutes in vacuum.
The transverse rupture strength and Rockwell A scale hardness (RA) at room temperature, the transverse rupture strength at 9000C, and the weight gain by oxidation after holding at the temperature of 9000C for 1 hour in still air of the samples of the hard alloys thus obtained are shown in Table 7.
Sample Nos. 1 to 10 all show extreme hardness and high transverse rupture strength at room temperature as well as high transverse upture strength and excellent oxidation resistance at the high temperature. A hot extruding die was prepared using the hard alloy of sample No. 6, and a pure copper rod was extruded through the die. It was possible to extrude the rod 50 to 100 times satisfactorily. A similar die formed with a WC-Co type hard alloy could not be used practically for the pure copper rod hot extrusion.
COMPARATIVE EXAMPLES
The compound powders listed in Table 1 and the metal powders listed Table 2 were blended in the composition shown in Table 4 with the blending ratios shown in Table 6.
The hard alloys were prepared by the same method as shown in the EXAMPLES, and the properties thereof are shown in Table 8.
Sample No. 11 has a W/B ratio less than 0.75, and exhibits low transverse rupture strength at room temperature as well as the high temperature. Sample No. 12 exhibits low transverse rupture strength at the high temperature and poor oxidation resistance due to the content of iron being higher than 10% by weight, though it shows high transverse rupture strength at room temperature. Sample
No. 13, containing a MoCoB type complex boride instead of the WCoB type complex boride, exhibits low transverse rupture strength at room temperature as well as the high temperature, compared with the samples of EXAMPLES having approximately the same hardness. Sample
No. 14 containing a Mo2 FeB2 type complex boride exhibits low transverse rupture strength at high temperature and poor oxidation resistance.
A similar hot extruding die as described in the EXAMPLES was prepared using the hard alloy of Sample No. 14, and a copper rod was extruded in the same manner as in the case of the EXAMPLES.
Only 5 to 10 times extruding was possible with the die.
Table 1
Compound B C N O W Fe Cr Mo powder wt% wt% wt% wt% wt% wt% we% wt% WB 5.5 0.03 0.1 0.07 94.3 - - CrB 17.4 0.20 0.04 0.16 - - 82.2 MoB 10.0 0.05 0.02 0.2 - 0.03 - 89.7 Table 2
Metal Purity Metal Purity powder wt% powder wt% w 99.95 Fe 99.69 Cr 99.75 Cu 99.9 Ni 99.75 Co 99.87 Table 3
Sample Composition (wit) W/B Amount of No ratio complex B W Cr Ni Fe Cu Co boride (wt%) 1 3.0 51.4 - - - - bal. 1.0 71 2 1.9 35.5 15.0 - - - bal. 1,1 44 3 1.9 42.0 10.0 - - - ( bal. 1.3 1 44 4 2.2 29.9 15.0 --- bal. 0.8 41 5 3.0 54.3 5.0 - - - bal. 1.05 70 6 2.0 34.3 21.0 5.0 - - bal.1.0 46 7 3.08 58.2 5.0 1.0 - - - bal. 0.9 80 8 1.7 29.1 21.0 5.0 5.0 - bal. 1.0 39 9 2.5 46.8 10.0 10.0 0.2 - bal. 1.1 58 10 1.9 33.5 10.0 3.0 - 2.0 bal. 1.0 44 Table 4
Sample Composition (wt%) W/B Amount of No. zzratio complex B W Cr Ni Fe Mo Co boride (wt%) 11 2.4 28.6 7.0 - - - bal. 0.7 39 12 3.0 51.4 5.0 - 15.0 - bal. 1.0 70 13 3.0 - 21.0 5.0 - 26.9 bal. - MoCoB 45 14 4.0 - 17.1 10.0 bal. 33.7 - - 2 Mo2FeB2 57 Table 5
Sample WB W Cr Ni Fe Cu CrB Co No. wt% wt% wt% wtt wt% wt wt% wtt 1 54.5 - - - - - 45.5 2 34.5 3.0 15.0 - - - - 47.5 3 a4.5 9.5 10.0 - - - - 46.0 4 31.7 - 12.9 - - - 2.6 52.8 5 54.5 2.0 5.0 - - - - 38.5 6 36.4 - 21.0 5.0 - - - 37.6 7 61.7 - 3.0 1.0 - - 2.4 31.9 8 30.9 - 21.0 5 0 5.0 - - 38.1 9 45.5 3.9 10.0 10.0 0.2 - - 30.4 10 34.5 - 10.0 3.0 - 2.0 - 50.5 Table 6
Sample WB W Cr Ni Fe MoB CrB Co No. wt% wt% wtt wt% wt% wt% wt% wt% 11 30.3 - 3.5 - - - 4.2 62.0 12 54.5 - 5.0 - 15.0 - - 25.5 13 - - 21.0 5.0 - 30.0 - 44.0 14 - - 16.0 10.0 35.1 37.6 1.3 Table 7
Sample Transverse Hardness Transverse Oxidation rupture rupture weight No. strength strength gain (RT, GPa) (RA) (900 C, GPa) (mg/mm2/h) 1 1.95 82.7 1.79 9.76 2 3.08 79.2 1.90 0.84 3 2.67 79.2 1.94 1.27 4 2.24 78.3 1.95 0.42 5 2.29 84.5 1.97 4.24 6 2.01 77.9 1.80 0.84 7 1.85 89.5 1.71 3.18 8 2.56 76.2 1.83 0.84 9 2.46 80.8 2.03 1.15.
10 2.70 78.0 1.81 1.39 Table 8
Samgle Transverse Hardness Transverse Oxidation rupture rupture weight No. strength strength gain (RT, GPa) (RA) (900 C, GPa) (mg/mm2/h) 11 1.63 81.6 1.42 6.37 12 2.31 85.5 1.63 -13.9 13 1.81 78.7 1.28 1.63 14 1.93 79.1 1.39 20.4
Claims (7)
- Claims 1. A heat-resistant sintered hard alloy comprising 35 to 95% by weight of a WCoB type complex boride in a cobalt base alloy matrix phase.
- 2. A heat-resistant sintered hard alloy as claimed in claim 1, comprising 1.5 to 4.18 by weight of boron, 19.1 to 69.7% by weight of tungsten, the balance being cobalt and a maximum of 1%, by weight of the alloy, of incidental impurities.
- 3. A heat-resistant sintered hard alloy as claimed in claim 1 or claim 2, which further comprises chromium in the range of 1 to 25% by weight.
- 4. A heat-resistant sintered hard alloy as claimed in any one of the preceding claims, which further comprises at least one of nickel, iron and copper, wherein nickel, when present, substitutes for cobalt in the range of 0.2 to 30% by weight of cobalt content, iron, when present, substitutes for cobalt in the range of 0.2 to 15% by weight of cobalt content, and 1 copper, when present, substitutes for cobalt in the range of 0.1 to 7.5% by weight of cobalt content.
- 5. A heat-resistant hard alloy as claimed in claim 1 substantially as herein described with reference to the Examples.
- 6. A hot extrusion die for extruding a copper rod, when manufactured from a heat-resistant hard alloy as claimed in any one of the preceding claims.
- 7. A process for manufacturing a sintered hard alloy as claimed in claim 1, comprising sintering a green compact comprising 35 to 95% by weight of a WCoB type complex boride in a cobalt base alloy matrix phase.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| GB9201927A GB2263704B (en) | 1992-01-29 | 1992-01-29 | Heat-resistant sintered hard alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| GB9201927A GB2263704B (en) | 1992-01-29 | 1992-01-29 | Heat-resistant sintered hard alloy |
Publications (3)
| Publication Number | Publication Date |
|---|---|
| GB9201927D0 GB9201927D0 (en) | 1992-03-18 |
| GB2263704A true GB2263704A (en) | 1993-08-04 |
| GB2263704B GB2263704B (en) | 1995-08-30 |
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| GB9201927A Expired - Fee Related GB2263704B (en) | 1992-01-29 | 1992-01-29 | Heat-resistant sintered hard alloy |
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| Country | Link |
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| GB (1) | GB2263704B (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2004040030A1 (en) * | 2002-10-29 | 2004-05-13 | Iowa State University Research Foundation, Inc. | A1mgb14 based cermet with ductile co-mn binder phase |
| CN109351979A (en) * | 2018-11-28 | 2019-02-19 | 西安交通大学 | A kind of WCoB-B4The preparation method of C ceramic matric composite |
| EP3408422A4 (en) * | 2016-01-25 | 2019-05-29 | Supermetalix, Inc. | Binder compositions of tungsten tetraboride and abrasive methods thereof |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| GB747483A (en) * | 1953-01-23 | 1956-04-04 | British Thomson Houston Co Ltd | A bonded boride composite material |
| GB1404734A (en) * | 1973-01-18 | 1975-09-03 | Nippon Tungsten | Boride containing hard alloy |
| US4671822A (en) * | 1985-06-19 | 1987-06-09 | Asahi Glass Company, Ltd. | ZrB2 -containing sintered cermet |
| EP0332463A1 (en) * | 1988-03-11 | 1989-09-13 | Vermont American Corporation | Boron-treated hard metal |
-
1992
- 1992-01-29 GB GB9201927A patent/GB2263704B/en not_active Expired - Fee Related
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| GB747483A (en) * | 1953-01-23 | 1956-04-04 | British Thomson Houston Co Ltd | A bonded boride composite material |
| GB1404734A (en) * | 1973-01-18 | 1975-09-03 | Nippon Tungsten | Boride containing hard alloy |
| US4671822A (en) * | 1985-06-19 | 1987-06-09 | Asahi Glass Company, Ltd. | ZrB2 -containing sintered cermet |
| EP0332463A1 (en) * | 1988-03-11 | 1989-09-13 | Vermont American Corporation | Boron-treated hard metal |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2004040030A1 (en) * | 2002-10-29 | 2004-05-13 | Iowa State University Research Foundation, Inc. | A1mgb14 based cermet with ductile co-mn binder phase |
| EP3408422A4 (en) * | 2016-01-25 | 2019-05-29 | Supermetalix, Inc. | Binder compositions of tungsten tetraboride and abrasive methods thereof |
| US11033998B2 (en) | 2016-01-25 | 2021-06-15 | The Regents Of The University Of California | Binder compositions of tungsten tetraboride and abrasive methods thereof |
| CN109351979A (en) * | 2018-11-28 | 2019-02-19 | 西安交通大学 | A kind of WCoB-B4The preparation method of C ceramic matric composite |
| CN109351979B (en) * | 2018-11-28 | 2020-06-19 | 西安交通大学 | WCoB-B4Preparation method of C ceramic matrix composite |
Also Published As
| Publication number | Publication date |
|---|---|
| GB9201927D0 (en) | 1992-03-18 |
| GB2263704B (en) | 1995-08-30 |
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Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PCNP | Patent ceased through non-payment of renewal fee |
Effective date: 20070129 |