JPH0331668B2 - - Google Patents
Info
- Publication number
- JPH0331668B2 JPH0331668B2 JP61102450A JP10245086A JPH0331668B2 JP H0331668 B2 JPH0331668 B2 JP H0331668B2 JP 61102450 A JP61102450 A JP 61102450A JP 10245086 A JP10245086 A JP 10245086A JP H0331668 B2 JPH0331668 B2 JP H0331668B2
- Authority
- JP
- Japan
- Prior art keywords
- carbide
- hafnium
- titanium
- weight
- added
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Expired - Lifetime
Links
- VBJZVLUMGGDVMO-UHFFFAOYSA-N hafnium atom Chemical compound [Hf] VBJZVLUMGGDVMO-UHFFFAOYSA-N 0.000 claims description 23
- MTPVUVINMAGMJL-UHFFFAOYSA-N trimethyl(1,1,2,2,2-pentafluoroethyl)silane Chemical compound C[Si](C)(C)C(F)(F)C(F)(F)F MTPVUVINMAGMJL-UHFFFAOYSA-N 0.000 claims description 19
- 229910052735 hafnium Inorganic materials 0.000 claims description 17
- 239000000843 powder Substances 0.000 claims description 16
- WHJFNYXPKGDKBB-UHFFFAOYSA-N hafnium;methane Chemical compound C.[Hf] WHJFNYXPKGDKBB-UHFFFAOYSA-N 0.000 claims description 11
- 229910052751 metal Inorganic materials 0.000 claims description 11
- 239000002184 metal Substances 0.000 claims description 11
- 239000010936 titanium Substances 0.000 claims description 11
- 229910010293 ceramic material Inorganic materials 0.000 claims description 10
- 238000005245 sintering Methods 0.000 claims description 10
- 239000011812 mixed powder Substances 0.000 claims description 9
- 229910052719 titanium Inorganic materials 0.000 claims description 6
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims description 5
- 150000004767 nitrides Chemical class 0.000 claims description 5
- 229910026551 ZrC Inorganic materials 0.000 claims description 4
- OTCHGXYCWNXDOA-UHFFFAOYSA-N [C].[Zr] Chemical compound [C].[Zr] OTCHGXYCWNXDOA-UHFFFAOYSA-N 0.000 claims description 4
- INZDTEICWPZYJM-UHFFFAOYSA-N 1-(chloromethyl)-4-[4-(chloromethyl)phenyl]benzene Chemical compound C1=CC(CCl)=CC=C1C1=CC=C(CCl)C=C1 INZDTEICWPZYJM-UHFFFAOYSA-N 0.000 claims description 3
- LRTTZMZPZHBOPO-UHFFFAOYSA-N [B].[B].[Hf] Chemical compound [B].[B].[Hf] LRTTZMZPZHBOPO-UHFFFAOYSA-N 0.000 claims description 2
- 150000001247 metal acetylides Chemical class 0.000 claims description 2
- -1 MnB2 Inorganic materials 0.000 claims 8
- 229910019918 CrB2 Inorganic materials 0.000 claims 4
- 229910015173 MoB2 Inorganic materials 0.000 claims 4
- 229910019742 NbB2 Inorganic materials 0.000 claims 4
- 229910004533 TaB2 Inorganic materials 0.000 claims 4
- 229910010055 TiB Inorganic materials 0.000 claims 3
- QIJNJJZPYXGIQM-UHFFFAOYSA-N 1lambda4,2lambda4-dimolybdacyclopropa-1,2,3-triene Chemical compound [Mo]=C=[Mo] QIJNJJZPYXGIQM-UHFFFAOYSA-N 0.000 claims 2
- 229910039444 MoC Inorganic materials 0.000 claims 2
- NFFIWVVINABMKP-UHFFFAOYSA-N methylidynetantalum Chemical compound [Ta]#C NFFIWVVINABMKP-UHFFFAOYSA-N 0.000 claims 2
- 229910003468 tantalcarbide Inorganic materials 0.000 claims 2
- UONOETXJSWQNOL-UHFFFAOYSA-N tungsten carbide Chemical compound [W+]#[C-] UONOETXJSWQNOL-UHFFFAOYSA-N 0.000 claims 2
- UNASZPQZIFZUSI-UHFFFAOYSA-N methylidyneniobium Chemical compound [Nb]#C UNASZPQZIFZUSI-UHFFFAOYSA-N 0.000 claims 1
- 229910052758 niobium Inorganic materials 0.000 claims 1
- 239000010955 niobium Substances 0.000 claims 1
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 claims 1
- FOZHTJJTSSSURD-UHFFFAOYSA-J titanium(4+);dicarbonate Chemical compound [Ti+4].[O-]C([O-])=O.[O-]C([O-])=O FOZHTJJTSSSURD-UHFFFAOYSA-J 0.000 claims 1
- 239000000463 material Substances 0.000 description 9
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 6
- 238000000034 method Methods 0.000 description 4
- 239000011148 porous material Substances 0.000 description 4
- 229910052786 argon Inorganic materials 0.000 description 3
- 239000000919 ceramic Substances 0.000 description 3
- 230000000052 comparative effect Effects 0.000 description 3
- 239000002245 particle Substances 0.000 description 3
- 239000002994 raw material Substances 0.000 description 3
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 2
- 230000007423 decrease Effects 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 229910002804 graphite Inorganic materials 0.000 description 2
- 239000010439 graphite Substances 0.000 description 2
- 239000001257 hydrogen Substances 0.000 description 2
- 229910052739 hydrogen Inorganic materials 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 230000001590 oxidative effect Effects 0.000 description 2
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 1
- 238000001493 electron microscopy Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 239000007789 gas Substances 0.000 description 1
- 238000010438 heat treatment Methods 0.000 description 1
- 150000002431 hydrogen Chemical class 0.000 description 1
- 230000002706 hydrostatic effect Effects 0.000 description 1
- 239000012770 industrial material Substances 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000002156 mixing Methods 0.000 description 1
- 238000000465 moulding Methods 0.000 description 1
- 238000003825 pressing Methods 0.000 description 1
- 238000007613 slurry method Methods 0.000 description 1
- 150000003608 titanium Chemical class 0.000 description 1
Landscapes
- Ceramic Products (AREA)
Description
＜産業上の利用分野＞
本発明は高強度、高硬度を有し切削工具や機械
部品材料として多くの用途を有する炭化チタニウ
ム・ハフニウム−ホウ化金属基セラミツクス焼結
材料に関するものである。
＜従来の技術及びその問題点＞
炭化ハフニウムは化学的に安定で多くの優れた
性質を有するが、難焼結性でしかも高価である為
に幅広い工業用材料として用いられるには至つて
いない。
上記炭化ハフニウムの優れた性質を損なう事な
く、より安価でしかも焼結性が良好な材料として
炭化チタニウム・ハフニウムが知られている。こ
の炭化チタニウム・ハフニウムは融点、硬度が高
く耐摩耗性に富み、切削工具材料や耐摩耗性機械
部材としての用途が期待されてはいるが、これの
みの単味の焼結体は抗析強度が小さく、靭性に乏
しいので未だ実用されるには至つていない。
＜発明の目的及び手段＞
本発明では上記炭化チタニウム・ハフニウム焼
結体の欠点を解消し、靭性が大で高強度の焼結体
を得る事を目的とする。
上記目的を達成する為に、炭化チタニウム・ハ
フニウムに対し種々のセラミツクス粉末を添加混
合し、得られた焼結体の特性を調べた結果、添加
混合するセラミツクス粉末としてMB2型あるい
はM2B5型（Ｍは金属を示す）で現わされるホウ
化金属が好ましい事を見出し、この知見に基づき
本発明をなすに至つた。
即ち、本発明はハフニウムが、ハフニウムとチ
タニウムの合計に対し、その原子数比で20〜50％
である炭化チタニウム・ハフニウム粉末に対し、
TiB2、CrB2、TaB2、MnB2、MoB2、VB2、
NbB2、HfB2、AlB2、ZrB2、W2B5、Mo2B5の
中から選ばれている１種以上のホウ化金属粉末を
全量に対し５〜95重量％添加混合した混合粉末を
焼結して成る炭化チタニウム・ハフニウム−ホウ
化金属基セラミツクス材料（以下第１発明とい
う）であり、この第１発明の成分にTiの炭化物、
窒化物又は炭窒化物を69重量％以下（０は含ま
ず）添加混合した混合粉末を焼結したセラミツク
ス材料（以下第２発明という）並びに第１発明の
成分及び第２発明の成分のそれぞれに更に炭化ハ
フニウム、炭化ジルコニウム、炭化バナジウム、
炭化ニオブ、炭化タンタル、炭化モリブデン、炭
化タングステンの中から選ばれる１種以上の炭化
物粉末を10重量％以下（０は含まず）添加混合し
た混合粉末を焼結したセラミツクス材料（以下第
３発明及び第４発明という）も上記第１発明及び
第２発明と同等あるいはそれ以上の抗折力及び靭
性を有している。
本発明で用いる炭化チタニウム・ハフニウム
は、ハフニウムが、ハフニウムとチタニウムの合
計に対し、その原子数比で20〜50％の範囲で適用
可能であり、その粉末は平均粒径2μｍ以下の微
粉末を用いるのが好ましい。又本発明で用いるホ
ウ化金属もその平均粒径は2μｍ以下、更には1μ
ｍ以下の微粉末を用いるのが好ましい。このホウ
化金属の添加量を５重量％未満としたのでは得ら
れる焼結体の強度向上効果が少なく、又95重量％
を越えると炭化チタニウム・ハフニウムの占める
割合が少なくなり過ぎて炭化チタニウム・ハフニ
ウムが本来具備する利点が無くなると共に、得ら
れる焼結体の強度も低下するのでホウ化金属の量
は全量の５〜95重量％とする。
本発明の第２発明及び第２発明及び第４発明で
用いるTiの炭化物、窒化物又は炭窒化物は全量
の69重量％を越えると焼結体の硬度が低下するの
でその添加量は69重量％以下とする。
次に本発明の第３発明及び第４発明で用いる炭
化ハフニウムや炭化ジルコニウム等の炭化物は、
材料の焼結性を向上せしめる働きをなすが、あま
り多量となると焼結体の強度を低下せしめるので
その添加量は10重量％以下とする。
本発明のセラミツクス材料は、前記各成分を混
合し、これまで知られているセラミツクス材料の
場合と同じような方法によつて製造することがで
きる。
例えば、原料粉末混合物を金型に充填して0.5
〜10ton／cm2程度のプレス圧により冷間圧縮し、
次いでラバープレスによりさらに0.5〜10ton／cm2
程度の静水圧で成形する。勿論どちらか一方で成
形してもよいし、また泥漿法により成形してもよ
い。次にこのようにして得られた圧粉体を真空中
又はアルゴン、水素などの非酸化性雰囲気中に於
いて、1400〜2300℃の温度で30〜300分間焼結す
る。さらに必要であれば、熱間静水圧焼成法によ
りアルゴンガスなどによる2ton／cm2以下程度の圧
力のもとで、1300〜2000℃で５〜300分間焼結す
る。
また、別の方法によると、原料粉末混合物を例
えば黒鉛型などの型に充填したのち、真空中又は
アルゴン、水素等の非酸化性雰囲気中に於いて、
ダイ圧力50〜300Kg／cm2、温度1300〜2300℃の条
件で、10〜200分間加熱焼結する、所謂ホツトプ
レス法を用いて焼結できる。
このようにして、切削工具などとして好適なセ
ラミツクス材料が得られる。
＜実施例＞
以下本発明の実施例を比較例と共に示す。
実施例 １
下記第１表に示す如き各種割合に配合した原料
粉末から成る試料を、金型成型及びラバープレス
（3ton／cm2）により圧粉体となし、該圧粉体を第
１表に示す条件で90分間常圧を行ない、得られた
焼結体の特性を測定した結果を同じく第１表に示
す。焼結体特性の項目中で組織中の気孔の状態は
電子顕微鏡観察に依つた。なお第１表中＊を付す
試料No.１−１、１−４、、及び１−18は比較例を
示す。
<Industrial Application Field> The present invention relates to a titanium carbide hafnium boride based ceramic sintered material which has high strength and high hardness and has many uses as a material for cutting tools and machine parts. <Conventional technology and its problems> Hafnium carbide is chemically stable and has many excellent properties, but it is difficult to sinter and is expensive, so it has not been used as a wide range of industrial materials. . Titanium carbide/hafnium carbide is known as a material that is cheaper and has good sinterability without impairing the excellent properties of hafnium carbide. This titanium/hafnium carbide has a high melting point, hardness, and wear resistance, and is expected to be used as cutting tool materials and wear-resistant mechanical parts, but a single sintered body of this material has a high anti-deposition strength. Because of its small size and poor toughness, it has not yet been put into practical use. <Objects and Means of the Invention> The present invention aims to eliminate the drawbacks of the titanium carbide/hafnium sintered body and to obtain a sintered body with high toughness and high strength. In order to achieve the above objective, various ceramic powders were added and mixed to titanium carbide/hafnium carbide, and the characteristics of the obtained sintered body were investigated. As a result, the ceramic powder to be added and mixed was MB 2 type or M 2 B 5. It has been found that metal borides represented by the type (M represents metal) are preferable, and based on this knowledge, the present invention has been accomplished. That is, in the present invention, hafnium has an atomic ratio of 20 to 50% of the total of hafnium and titanium.
For titanium carbide/hafnium powder,
TiB 2 , CrB 2 , TaB 2 , MnB 2 , MoB 2 , VB 2 ,
A mixed powder containing 5 to 95% by weight of one or more metal boride powders selected from NbB 2 , HfB 2 , AlB 2 , ZrB 2 , W 2 B 5 , and Mo 2 B 5 based on the total amount. This is a titanium carbide/hafnium-metal boride based ceramic material (hereinafter referred to as the first invention) formed by sintering Ti carbide, a titanium carbide,
A ceramic material obtained by sintering a mixed powder containing nitride or carbonitride in an amount of 69% by weight or less (not including 0) (hereinafter referred to as the second invention), and each of the components of the first invention and the second invention. Furthermore, hafnium carbide, zirconium carbide, vanadium carbide,
A ceramic material (hereinafter referred to as the third invention and The fourth invention) also has transverse rupture strength and toughness equivalent to or greater than those of the first and second inventions. The titanium carbide/hafnium used in the present invention can be used in a range of 20 to 50% of the atomic ratio of hafnium to the total of hafnium and titanium, and the powder is a fine powder with an average particle size of 2 μm or less. It is preferable to use Furthermore, the average particle size of the metal boride used in the present invention is 2 μm or less, and even 1 μm.
It is preferable to use fine powder with a particle diameter of m or less. If the amount of metal boride added is less than 5% by weight, the effect of improving the strength of the obtained sintered body will be small;
If the amount exceeds 5 to 95% of the total amount, the proportion of titanium carbide/hafnium becomes too small and the inherent advantages of titanium carbide/hafnium are lost, and the strength of the obtained sintered body also decreases. Weight%. If the Ti carbide, nitride, or carbonitride used in the second invention, second invention, and fourth invention of the present invention exceeds 69% by weight of the total amount, the hardness of the sintered body will decrease, so the amount added is 69% by weight. % or less. Next, carbides such as hafnium carbide and zirconium carbide used in the third and fourth inventions of the present invention are
It works to improve the sinterability of the material, but if it is too large it will reduce the strength of the sintered body, so the amount added should be 10% by weight or less. The ceramic material of the present invention can be produced by mixing the above-mentioned components and using a method similar to that used for conventionally known ceramic materials. For example, fill the raw powder mixture into a mold and
Cold compressed with a press pressure of ~10ton/ cm2 ,
Then, further 0.5 to 10 ton/cm 2 using a rubber press.
Shape with moderate hydrostatic pressure. Of course, it may be molded using either one, or may be molded by a slurry method. Next, the green compact thus obtained is sintered in vacuum or in a non-oxidizing atmosphere such as argon or hydrogen at a temperature of 1400 to 2300°C for 30 to 300 minutes. Further, if necessary, sintering is performed at 1300 to 2000° C. for 5 to 300 minutes using a hot isostatic pressure sintering method under a pressure of about 2 tons/cm 2 or less using argon gas or the like. According to another method, after filling a raw material powder mixture into a mold such as a graphite mold, in a vacuum or in a non-oxidizing atmosphere such as argon or hydrogen,
Sintering can be carried out using the so-called hot press method, in which heating and sintering is performed for 10 to 200 minutes at a die pressure of 50 to 300 Kg/cm 2 and a temperature of 1300 to 2300°C. In this way, a ceramic material suitable for cutting tools and the like is obtained. <Examples> Examples of the present invention will be shown below together with comparative examples. Example 1 Samples consisting of raw material powders mixed in various proportions as shown in Table 1 below were molded into green compacts by molding and rubber pressing (3 ton/cm 2 ). Table 1 also shows the results of measuring the properties of the sintered body obtained by applying normal pressure for 90 minutes under the conditions shown. Among the characteristics of the sintered body, the state of pores in the structure was determined by electron microscopy observation. Note that Sample Nos. 1-1, 1-4, and 1-18 marked with * in Table 1 are comparative examples.
【表】【table】
【表】
実施例 ２
下記第２表に示す如き各種割合に配合した原料
粉末から成る試料を、黒鉛型に充填し、第２表に
示す条件で60分間ホツトプレス焼結を行ない、得
られた焼結体の特性を同じく第２表に示す。焼結
体の気孔の状態は同じく電子顕微鏡観察に依つ
た。なお第２表中＊を付す試料No.２−４は比較例
を示す。[Table] Example 2 Samples consisting of raw material powders mixed in various proportions as shown in Table 2 below were filled into graphite molds, and hot press sintered for 60 minutes under the conditions shown in Table 2. The properties of the bodies are also shown in Table 2. The state of the pores in the sintered body was also determined by electron microscopic observation. Note that Sample No. 2-4 marked with * in Table 2 indicates a comparative example.
【表】【table】
【表】
＜発明の効果＞
以上述べて来た如く本発明によれば、炭化チタ
ニウム・ハフニウム単味の焼結体と比べその抗折
力が大幅に向上している。即ち炭化チタニウム・
ハフニウム単味から成る焼結体（第１表中試料No.
１−４はその抗折力が25Kg／mm2しかなく、しかも
焼結体の組織中には多量の気孔が存在している
が、本発明材料はそれよりも相当大きな抗折力と
示し組織中に気孔は見られず硬さ、靭性とも十分
な値を示している。
従つて本発明材料は炭化チタニウム・ハフニウ
ムの有する安価で焼結性に富むという利点をその
まゝ活かしつゝ硬さ、強度共に大きな材料として
多くの用途に用いる事が出来るものである。[Table] <Effects of the Invention> As described above, according to the present invention, the transverse rupture strength is significantly improved compared to a sintered body of titanium carbide/hafnium alone. That is, titanium carbide
Sintered body made of hafnium (sample No. in Table 1)
1-4 has a transverse rupture strength of only 25 Kg/ mm2 , and there are a large number of pores in the structure of the sintered body, but the material of the present invention exhibits a considerably larger transverse rupture strength and a structure of No pores were observed inside, and both hardness and toughness were sufficient. Therefore, the material of the present invention can be used for many purposes as a material with high hardness and strength while taking advantage of the advantages of titanium carbide and hafnium carbide, such as being inexpensive and having high sinterability.
Claims (1)
に対し、その原子数比で20％〜50％である炭化チ
タニウム・ハフニウム粉末に対し、TiB2、
CrB2、TaB2、MnB2、MoB2、VB2、NbB2、
HfB2、AlB2、ZrB2、W2B5、Mo2B5の中から選
ばれる１種以上のホウ化金属粉末を全量に対し５
〜95重量％添加混合した混合粉末を焼結して成る
炭化チタニウム・ハフニウム−ホウ化金属基セラ
ミツクス材料。 ２ ハフニウムが、ハフニウムとチタニウムの合
計に対し、その原子数比で20〜50％である炭化チ
タニウム・ハフニウム粉末に対し、TiB2、
CrB2、TaB2、MnB2、MoB2、VB2、NbB2、
HfB2、AlB2、ZrB2、W2B5、Mo2B5の中から選
ばれる１種以上のホウ化金属粉末を全量に対し５
〜95重量％添加混合した混合粉末に、Tiの炭化
物、窒化物又は炭窒化物を全量に対し69重量％以
下（０は含まず）添加混合した混合粉末を焼結し
て成る炭化チタニウム・ハフニウム−ホウ化金属
基セラミツクス材料。 ３ ハフニウムが、ハフニウムとチタニウムの合
計に対し、その原子数比で20〜50％である炭化チ
タニウム・ハフニウム粉末に対し、TiB2、
CrB2、TaB2、MnB2、MoB2、VB2、NbB2、
HfB2、AlB2、ZrB2、W2B5、Mo2B5の中から選
ばれる１種以上のホウ化金属粉末を全量に対し５
〜95重量％添加混合した混合粉末に、炭化ハフニ
ウム、炭化ジルコニウム、炭化バナジウム、炭化
ニオブ、炭化タンタル、炭化モリブデン、炭化タ
ングステンの中から選ばれる１種以上の炭化物粉
末を全量に対し10重量％以下（０は含まず）添加
混合した混合粉末を焼結して成る炭チタニウム・
ハフニウム−ホウ化金属基セラミツクス材料。 ４ ハフニウムが、ハフニウムとチタニウムの合
計に対し、その原子数比で20〜50％である炭化チ
タニウム・ハフニウム粉末に対し、TiB2、
CrB2、TaB2、MnB2、MoB2、VB2、NbB2、
HfB2、AlB2、ZrB2、W2B5、Mo2B5の中から選
ばれる１種以上のホウ化金属粉末を全量に対し５
〜95重量％添加混合した混合粉末に、Tiの炭化
物、窒化物又は炭窒化物を全量に対し69重量％以
下（０は含まず）添加混合し、更に炭化ハフニウ
ム、炭化ジルコニウム、炭化バナジウム、炭化ニ
オブ、炭化タンタル、炭化モリブデン、炭化タン
グステンの中から選ばれる１種以上の炭化物粉末
を全量に対し10重量％以下（Ｏは含まず）添加混
合した混合粉末を焼結して成る炭チタニウム・ハ
フニウム−ホウ化金属基セラミツクス材料。[Scope of Claims] 1 TiB 2 ,
CrB2 , TaB2 , MnB2 , MoB2 , VB2 , NbB2 ,
One or more metal boride powders selected from HfB 2 , AlB 2 , ZrB 2 , W 2 B 5 , Mo 2 B 5 are added to the total amount of 5
A titanium carbide/hafnium-metal boride based ceramic material made by sintering a mixed powder containing ~95% by weight. 2 For titanium carbide/hafnium powder in which hafnium accounts for 20 to 50% of the total atomic ratio of hafnium and titanium, TiB 2 ,
CrB2 , TaB2 , MnB2 , MoB2 , VB2 , NbB2 ,
One or more metal boride powders selected from HfB 2 , AlB 2 , ZrB 2 , W 2 B 5 , Mo 2 B 5 are added to the total amount of 5
Titanium carbide/hafnium made by sintering a mixed powder in which up to 95% by weight of a Ti carbide, nitride, or carbonitride is added and mixed to a mixed powder of up to 69% by weight (not including 0) of Ti carbide, nitride, or carbonitride. -Metal boride based ceramic materials. 3 For titanium carbide/hafnium powder in which hafnium accounts for 20 to 50% of the total atomic ratio of hafnium and titanium, TiB 2 ,
CrB2 , TaB2 , MnB2 , MoB2 , VB2 , NbB2 ,
One or more metal boride powders selected from HfB 2 , AlB 2 , ZrB 2 , W 2 B 5 , Mo 2 B 5 are added to the total amount of 5
Up to 10% by weight or less of one or more carbide powders selected from hafnium carbide, zirconium carbide, vanadium carbide, niobium carbide, tantalum carbide, molybdenum carbide, and tungsten carbide are added to the mixed powder at ~95% by weight based on the total amount. (0 is not included) Titanium carbonate made by sintering mixed powder with addition.
Hafnium-boride based ceramic material. 4 For titanium carbide/hafnium powder in which hafnium accounts for 20 to 50% of the total atomic ratio of hafnium and titanium, TiB 2 ,
CrB2 , TaB2 , MnB2 , MoB2 , VB2 , NbB2 ,
One or more metal boride powders selected from HfB 2 , AlB 2 , ZrB 2 , W 2 B 5 , Mo 2 B 5 are added to the total amount of 5
Up to 69% by weight (not including 0) of Ti carbides, nitrides, or carbonitrides are added to the mixed powder of ~95% by weight, and further mixed with hafnium carbide, zirconium carbide, vanadium carbide, and carbide. Titanium carbide/hafnium carbide made by sintering a mixed powder in which one or more carbide powders selected from niobium, tantalum carbide, molybdenum carbide, and tungsten carbide are added and mixed in an amount of 10% by weight or less based on the total amount (excluding O). -Metal boride based ceramic materials.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP61102450A JPS62260775A (en) | 1986-05-01 | 1986-05-01 | Titanium carbide-hafnium-boride metal base ceramic material(2) |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP61102450A JPS62260775A (en) | 1986-05-01 | 1986-05-01 | Titanium carbide-hafnium-boride metal base ceramic material(2) |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS62260775A JPS62260775A (en) | 1987-11-13 |
| JPH0331668B2 true JPH0331668B2 (en) | 1991-05-08 |
Family
ID=14327807
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP61102450A Granted JPS62260775A (en) | 1986-05-01 | 1986-05-01 | Titanium carbide-hafnium-boride metal base ceramic material(2) |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS62260775A (en) |
Families Citing this family (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH07100626B2 (en) * | 1987-02-20 | 1995-11-01 | 東芝セラミックス株式会社 | TiB 2) Manufacturing method of base ceramics |
| JPH0679978B2 (en) * | 1987-12-25 | 1994-10-12 | 株式会社エス・ティー・セラミックス研究所 | Titanium boride ceramics sintered body |
-
1986
- 1986-05-01 JP JP61102450A patent/JPS62260775A/en active Granted
Also Published As
| Publication number | Publication date |
|---|---|
| JPS62260775A (en) | 1987-11-13 |
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| EXPY | Cancellation because of completion of term |