JPS63203743A - Titanium nitride cermet - Google Patents
Titanium nitride cermetInfo
- Publication number
- JPS63203743A JPS63203743A JP62035723A JP3572387A JPS63203743A JP S63203743 A JPS63203743 A JP S63203743A JP 62035723 A JP62035723 A JP 62035723A JP 3572387 A JP3572387 A JP 3572387A JP S63203743 A JPS63203743 A JP S63203743A
- Authority
- JP
- Japan
- Prior art keywords
- powder
- solid solution
- cermet
- tic
- sintering
- 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.)
- Granted
Links
- 239000011195 cermet Substances 0.000 title claims abstract description 21
- NRTOMJZYCJJWKI-UHFFFAOYSA-N Titanium nitride Chemical compound [Ti]#N NRTOMJZYCJJWKI-UHFFFAOYSA-N 0.000 title abstract description 7
- 239000000843 powder Substances 0.000 claims abstract description 42
- 239000006104 solid solution Substances 0.000 claims abstract description 25
- 238000005245 sintering Methods 0.000 claims abstract description 10
- 239000000203 mixture Substances 0.000 claims abstract description 9
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 claims abstract description 8
- 229910052751 metal Inorganic materials 0.000 claims abstract description 6
- 239000002184 metal Substances 0.000 claims abstract description 6
- 239000000463 material Substances 0.000 claims description 13
- 229910003178 Mo2C Inorganic materials 0.000 abstract 2
- 150000002739 metals Chemical class 0.000 abstract 2
- 230000000052 comparative effect Effects 0.000 description 7
- 239000012071 phase Substances 0.000 description 5
- 239000002245 particle Substances 0.000 description 4
- 239000000956 alloy Substances 0.000 description 3
- 229910045601 alloy Inorganic materials 0.000 description 3
- 239000011230 binding agent Substances 0.000 description 3
- 239000010936 titanium Substances 0.000 description 3
- 230000015572 biosynthetic process Effects 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 230000005496 eutectics Effects 0.000 description 2
- 239000007791 liquid phase Substances 0.000 description 2
- 238000001000 micrograph Methods 0.000 description 2
- 229910052757 nitrogen Inorganic materials 0.000 description 2
- 230000003287 optical effect Effects 0.000 description 2
- 230000035939 shock Effects 0.000 description 2
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 229910001873 dinitrogen Inorganic materials 0.000 description 1
- 239000007789 gas Substances 0.000 description 1
- 239000011261 inert gas Substances 0.000 description 1
- 239000007788 liquid Substances 0.000 description 1
- 230000008018 melting Effects 0.000 description 1
- 238000002844 melting Methods 0.000 description 1
- 238000010298 pulverizing process Methods 0.000 description 1
- 238000005204 segregation Methods 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 230000003068 static effect Effects 0.000 description 1
- -1 that is Substances 0.000 description 1
- 101150051314 tin-10 gene Proteins 0.000 description 1
Abstract
Description
【発明の詳細な説明】
［産業上の利用分野］
この発明は、工具材料等に適した耐摩耗性の窒化チタン
系サーメットに関するものである。DETAILED DESCRIPTION OF THE INVENTION [Industrial Field of Application] The present invention relates to a wear-resistant titanium nitride cermet suitable for tool materials and the like.
［従来の技術］
ＴｉＣ基サーメットは、炭化物ＴＩＣの特性を生かした
耐摩耗焼結合金として知られている。[Prior Art] TiC-based cermet is known as a wear-resistant sintered alloy that takes advantage of the characteristics of carbide TIC.
しかしこのサーメットは高硬度なるが故に靭性に乏しく
、切削用工具材料として使用した場合、しばしばチッピ
ング破損の問題を生じた。このため、ＴｉＣ基サーメッ
トに：、Ｔ ｉ Ｎを添加した窒化チタン系サーメット
が用いられている。However, because of its high hardness, this cermet has poor toughness, and when used as a cutting tool material, it often suffers from chipping and breakage. For this reason, a titanium nitride cermet is used, which is a TiC-based cermet to which TiN is added.
この窒化チタン系サーメットは、従来、真空あるいは不
活性ガス雰囲気高温炉により焼結体が得られていた。Conventionally, sintered bodies of this titanium nitride-based cermet have been obtained in a vacuum or inert gas atmosphere high-temperature furnace.
［発明が解決しようとする問題点］
窒化チタン系サーメットを得るためＴ：Ｃ粉末にＴｉＮ
粉末を添加した場合、他成分への各々の固溶率の違いか
ら焼結体内部に遊離窒素ガスを生じ、合金組織中に内部
ボアを発生する。[Problems to be solved by the invention] Adding TiN to T:C powder to obtain titanium nitride cermet
When powder is added, free nitrogen gas is generated inside the sintered body due to the difference in solid solution rate of each component to other components, and internal bores are generated in the alloy structure.
このため、焼結体の靭性は著しく低下し、ＴｉＮのもつ
靭性、耐熱衝撃性を充分発揮することができなかった。As a result, the toughness of the sintered body was significantly reduced, and the toughness and thermal shock resistance of TiN could not be fully exhibited.
かかる焼結における現象については種々の研究報告がな
され、以下の事象が明らかとなっている。Various research reports have been made regarding such phenomena in sintering, and the following phenomena have been clarified.
まず、焼結開始後１２８０℃でＮｔ−”ｒｒ−ｃの三元
共晶の液相が発生し、１３０７℃を越えると、Ｎ１−Ｔ
ｌＮ−Ｔｉｅ共存域ではＴｉ（Ｃ，Ｎ）固溶相が出現し
、それまで存在していたＮｉ−ＴｉＣ液相中へのＴｉＮ
溶解が始まり、熱的に安定でおるＴｉ（Ｃ，Ｎ）固溶体
−ＴｉＣ共晶液中に溶解し難いＴｉＮからの脱窒素ガス
が圧粉体内に残存して、内部ボアとなるのである。First, a ternary eutectic liquid phase of Nt-"rr-c occurs at 1280°C after the start of sintering, and when the temperature exceeds 1307°C, N1-T
In the lN-Tie coexistence region, a Ti(C,N) solid solution phase appears, and TiN enters the previously existing Ni-TiC liquid phase.
When melting begins, denitrification gas from TiN, which is difficult to dissolve in the thermally stable Ti(C,N) solid solution-TiC eutectic liquid, remains in the green compact and forms internal bores.
そこで内部ボアの発生のない焼結体が望まれている。Therefore, a sintered body without internal bores is desired.
［問題点を解決するための手段］
この発明は、上記問題点を解決するためのもので、Ｔ
ｉ Ｃ−Ｔ １Ｎ−ＷＣ−ＴａＣの四元系固溶粉末７０
〜８０ｗｔ％とＣｏとＮｉよりなる結合相金属１０〜２
０ｗｔ％およびＭＯ２Ｇ２０〜５ｗｔ％よりなる材料を
真空焼結してなるサーメットであって、前記固溶粉末の
組成は、ＴｉＣ５０〜ｅｏｗｔ％、ＴｉＮ１０〜３０ｗ
ｔ％、ＷＣ１０〜３０ｗｔ％、ＴａＣ５〜１５ｗｔ％で
あり、ＣｏとＮｉの組成比は１ ： ０．８〜１．２
の範囲内であることを特徴とする窒化チタン系サーメッ
トである。[Means for Solving the Problems] This invention is intended to solve the above problems.
i C-T 1N-WC-TaC quaternary solid solution powder 70
Binding phase metal 10-2 consisting of ~80wt% Co and Ni
A cermet formed by vacuum sintering a material consisting of 0wt% and 20-5wt% of MO2G, the composition of the solid solution powder being 50-eowt% of TiC, 10-30w of TiN.
t%, WC 10-30 wt%, TaC 5-15 wt%, and the composition ratio of Co and Ni is 1:0.8-1.2.
This is a titanium nitride-based cermet characterized by having a
すなわち、この発明はＴ ｉ ＣＳＴ ｉ Ｎ ｓ Ｗ
Ｃ５ＴａＣを固溶した形で用いるが、その理由はＴ；
ＣとＴｉＮの固溶化を一度行ったＴｉ （Ｃ。That is, this invention is T i CST i N s W
C5TaC is used in solid solution form, and the reason is T;
Ti (C.
Ｎ）固溶粉、すなわち、脱窒素反応の終了した粉末を用
いることにより、ボアの発生を防止するとともに、ＷＣ
とＴ ａ Ｃを同時に固溶しておくことによって、靭性
および高温特性を高めるためである。これらの四成分を
単独あるいは三元系以下の固溶粉の形で用いた場合には
、合金組織中へ微細分散することが難しく、粗大偏析を
生じたり、上述の理由による内部ボアの発生を防ぐこと
ができず靭性が低下する。そして、この四元系固溶粉に
おいて充分な耐摩耗性、高温特性を確保するためには、
Ｔｉ０５０〜６０ｗｔ％、Ｔ ｉ Ｎ １０〜３０ｗｔ
％、ＷＱ１０〜３０ｗｔ％、ＴａＣ５〜１５ｗｔ％の範
囲である必要がある。これ以外の範囲では所期の目的を
達成しない。N) By using solid solution powder, that is, powder that has undergone denitrification reaction, it is possible to prevent the formation of bores and to reduce WC.
This is to improve toughness and high-temperature properties by solidly dissolving and T a C at the same time. When these four components are used alone or in the form of a ternary solid solution powder, it is difficult to finely disperse them into the alloy structure, resulting in coarse segregation and the formation of internal bores for the reasons mentioned above. This cannot be prevented and the toughness decreases. In order to ensure sufficient wear resistance and high temperature properties in this quaternary solid solution powder,
Ti050~60wt%, TiN10~30wt
%, WQ 10 to 30 wt%, and TaC 5 to 15 wt%. In any other range, the intended purpose will not be achieved.
結合相を形成するＧＯｌＮｉは四元系固溶粉末を用いた
場合に充分な靭性を付与するために、Ｃｏ：Ｎｉの量比
を１ ： ０．８〜１．２ （７）範囲トスる。In order to impart sufficient toughness to GOlNi forming the binder phase when a quaternary solid solution powder is used, the Co:Ni ratio is set in the range of 1:0.8 to 1.2 (7).
そして、四元系固溶粉末と結合相金属の組成割合は前者
が７０〜８０ｗｔ％に対し後者は１０〜２０ｗｔである
ものが、切削用工具材料として特に優れたものとなる。The composition ratio of the quaternary solid solution powder and the binder phase metal is 70 to 80 wt % for the former and 10 to 20 wt % for the latter, which is particularly excellent as a cutting tool material.
ただ、これらの両者はそのままでは濡れ性に劣るので、
この発明では２０〜５ｗｔ％のＭＯ２Ｃを添加して、両
者の濡れ性を改善する。However, both of these have poor wettability as they are, so
In this invention, 20 to 5 wt% of MO2C is added to improve the wettability of both.
ＭＯ２Ｃがこの範囲を逸脱すると、前記四元系固溶粉末
と結合相金属の効果を十分に発揮せしめることができな
い。If MO2C deviates from this range, the effects of the quaternary solid solution powder and the binder phase metal cannot be fully exhibited.
［実施例］ 以下実施例並びに比較例について説明する。[Example] Examples and comparative examples will be described below.
実施例１
Ｔ ｉ Ｃ３０ｗｔ％、Ｔ ｉ Ｎ２０ｗｔ％、ＷＱ２
０ｗｔ％、ＴａＣｌ０ｗｔ％よりなる平均粒径１．５μ
ｍの固溶粉末７０ｗｔ％と、平均粒径２．ＯｆｌｍのＭ
Ｏ２Ｃ粉１５Ｗ１％および平均粒径１．２μｍ１１のＧ
ｏ粉７．５ｗｔ％と平均粒径２，３μｍのＮｉ粉７．５
ｗｔ％とを用い、これらを振動ボールミルで４０時間粉
砕混合した後、１．５Ｔｂ
粉体に成形し、ついでこの圧粉体をに力１０−２ｍｍＨ
Ｄの真空中、温度１３６０℃に１時間保持の条件で焼結
した。Example 1 T i C 30 wt%, T i N 20 wt%, WQ2
0wt%, TaCl0wt%, average particle size 1.5μ
solid solution powder of 70 wt% and an average particle size of 2. Oflm's M
O2C powder 15W1% and G with average particle size 1.2μm11
7.5wt% of O powder and 7.5% of Ni powder with an average particle size of 2.3μm
After pulverizing and mixing them in a vibrating ball mill for 40 hours, they were molded into a 1.5 Tb powder, and then this green compact was subjected to a force of 10-2 mmH.
Sintering was carried out in a vacuum of D under conditions of holding the temperature at 1360° C. for 1 hour.
得られたこの発明のサーメットについて、常温硬度（Ｈ
ＲＡ）、高温硬度（６００℃）、常温抗折力を測定した
ところ、それぞれ下記のとおりであった。The obtained cermet of the present invention has a room temperature hardness (H
RA), high-temperature hardness (600°C), and room-temperature transverse rupture strength were measured, and the results were as follows.
常温硬度・・・ＨＲＡ９２．０
高温硬度・・・Ｈｖ ８６０（６００℃）常温抗折力・
２００ｋＯｆ／ｍｍ ２
ざらに同材料よりＴＮＰ−３３１の形状をもった切削チ
ップを切出し、下記の条件での連続切削試験を行った。Room temperature hardness...HRA92.0 High temperature hardness...Hv 860 (600℃) Room temperature transverse rupture strength
A cutting tip having a shape of TNP-331 was cut out from the same rough material and subjected to a continuous cutting test under the following conditions.
被削材 ５４５Ｃ（ＨＲＣ２５）
切削速度 １９０ｍ／ｍ ｉ ｎ
切り込み １．５ｍｍ
送り ０．２１１１１ｍ／ｒｐＨｌ切削時間 ６ｍ
１ｎ
結果は下記のとおりであり、靭性、耐摩耗性に優れた材
料であることが分った。Work material 545C (HRC25) Cutting speed 190m/min Depth of cut 1.5mm Feed 0.21111m/rpHl Cutting time 6m
1n The results are as follows, and it was found that the material had excellent toughness and wear resistance.
ノーズ変形量 ０．０４ｍｍ
境界摩耗１ ０．４ｍｍ
実施例２
実施例１において作成したこの発明のサーメットをもっ
て、５ＤＫＮ４２ＺＴＮの形状をもった切削チップを切
出し、下記の条件での断続切削試験を行った。Nose deformation amount 0.04 mm Boundary wear 1 0.4 mm Example 2 A cutting tip having a shape of 5DKN42ZTN was cut from the cermet of the present invention prepared in Example 1, and an interrupted cutting test was conducted under the following conditions.
被剛材 ＳＫＳ ３
切削速度 ８８［１１／ｍ ｉ ｎ
切り込み １゜ｓｍｍ
送り ０．１１＋ｎ＋ｎ／ｒｐｍ
切削時間 １６０１１１ ｔ ｎ
結果は下記のとおりであり、耐熱衝撃性に優れた材料で
あることが分った。Rigid material: SKS 3 Cutting speed: 88 [11/min Depth of cut: 1゜smm Feed: 0.11+n+n/rpm Cutting time: 160111 t n The results are as follows, and it was found that the material has excellent thermal shock resistance. Ta.
サーマルクラック発生数 ０〜１個
逃げ面摩耗幅 ０．０２１１１［１１実施例
３
実施例１と同じ固溶粉末７５ｗｔ％と、ＭＯ２Ｇ粉１ｏ
ｗｔ％、Ｎ１粉７．５ｗｔ％、Ｃｏ粉７．５１＃ｔ％と
を用い、実施例１と同様にしてこの発明のサーメットを
得た。Number of thermal cracks: 0 to 1 Flank wear width: 0.02111 [11 Example 3 75 wt% of the same solid solution powder as Example 1 and 1 o of MO2G powder
A cermet of the present invention was obtained in the same manner as in Example 1 using 7.5 wt% of N1 powder and 7.51 #t% of Co powder.
得られたものについて実施例１と同様にして試験をした
ところ、下記の結果を得た。When the obtained product was tested in the same manner as in Example 1, the following results were obtained.
常温硬度・・・ＨＲＡ９１．８
高温硬度−Ｈｖ８２０（６００℃）
常温抗折力・・・１９０ｋＯｆ／ｍｍ２実施例４
実施例１と同じ固溶粉末８０ｗｔ％と、ＭＯ２Ｃ粉５ｗ
ｔ％、Ｎｉ粉７．５ｗｔ％、Ｃ６粉７．５ｗｔ％とを用
い、実施例１と同様にしてこの発明のサーメットを得た
。Room temperature hardness: HRA91.8 High temperature hardness: Hv820 (600°C) Room temperature transverse rupture strength: 190 kOf/mm2 Example 4 80 wt% of the same solid solution powder as Example 1 and 5 w of MO2C powder
A cermet of the present invention was obtained in the same manner as in Example 1 using 7.5 wt% of Ni powder and 7.5 wt% of C6 powder.
得られたものについて実施例１と同様にして試験をした
ところ、下記の結果を得た。When the obtained product was tested in the same manner as in Example 1, the following results were obtained.
常温硬度・−１（ＲＡ９１．０
高温硬度・・・Ｈｖ８００ （６００℃）常温抗折力・
・・ｋｇｆ／ｍｍ２
実施例５
固溶粉末の組成中、ＴｉＣを５５ｗｔ％、ＴａＣを５ｗ
ｔ％にした以外は実施例１と同様にして試験をしたとこ
ろ下記の結果を得た。Room temperature hardness: -1 (RA91.0 High temperature hardness: Hv800 (600℃) Room temperature transverse rupture strength:
...kgf/mm2 Example 5 In the composition of the solid solution powder, 55wt% of TiC and 5w of TaC were added.
A test was conducted in the same manner as in Example 1 except that the amount was changed to t%, and the following results were obtained.
常温硬度・・・ＨＲＡ９１．８
高温硬度−Ｈｖ７９０（６００℃）
常温抗折力−１８０ｋ（Ｊｆ／ｍ１ｌ１２実施例６
固溶粉末を７５ｗｔ％、ＭＯ２Ｃを１０ｗｔ％とした以
外は実施例１と同様にして、この発明のサーメットを得
た。Room temperature hardness: HRA91.8 High temperature hardness - Hv790 (600°C) Room temperature transverse rupture strength - 180k (Jf/ml12 Example 6 Same as Example 1 except that the solid solution powder was 75 wt% and MO2C was 10 wt%. Thus, the cermet of this invention was obtained.
得られたものについて実施例１と同様にして試験をした
ところ、下記の結果を得た。When the obtained product was tested in the same manner as in Example 1, the following results were obtained.
常温硬度・・・ＨＲＡ９１．３
高温硬度−Ｈｖ７２０ （６００℃）
常温抗折力・・・１６０ｋ（Ｊｆ／ １１ｍ２実施例７
固溶粉末を８０ｗｔ％、ＭＯ２Ｃを５ｗｔ％とした以外
は実施例４と同様にして、この発明のサーメットを得た
。Room temperature hardness: HRA91.3 High temperature hardness: Hv720 (600°C) Room temperature transverse rupture strength: 160k (Jf/ 11m2 Example 7 Same as Example 4 except that the solid solution powder was 80wt% and the MO2C was 5wt%. Similarly, a cermet of the present invention was obtained.
得られたものについて、実施例１と同様にして試験をし
たところ、下記の結果を得た。The obtained product was tested in the same manner as in Example 1, and the following results were obtained.
常温硬度・−ＨＲＡ９０．８
高温硬度−ＨＶ７００（６００℃）
常温抗折力・−１＆Ｏｋｇｆ／ｍ１ｌ１２比較例１
Ｔ ｉ Ｎ５０ｗｔ％とＴ ｉ Ｃ３０ｗｔ％の固溶粉
末２９．４ｗｔ％、Ｗ Ｃ５０ｗｔ％とＴ ｉ Ｃ３０
ｗｔ％とＴａＣ２０ｗｔ％の固溶粉末３９．２ｗｔ％、
Ｔ ｉ Ｃ４，９ｗｔ％にＭ Ｏ２Ｃ１１，８ｗｔ％、
Ｎｉ粉１４．７ｗｔ％を用いて実施例１と同様にして比
較用のサーメットを得た。Room temperature hardness - HRA90.8 High temperature hardness - HV700 (600°C) Room temperature transverse rupture strength -1 & Okgf/ml12 Comparative example 1 29.4 wt% solid solution powder of TiN50wt% and TiC30wt%, WC50wt% and T iC30
solid solution powder of 39.2 wt% and 20 wt% of TaC,
M O2C11.8wt% to T i C4.9wt%,
A comparative cermet was obtained in the same manner as in Example 1 using 14.7 wt % of Ni powder.
得られたものについてその組織を光学顕微鏡（ｘ １５
０）で観察したところ、第１図に示すように多くの内部
ボアが見られた。The structure of the obtained material was examined using an optical microscope (x 15
0), many internal bores were seen as shown in Figure 1.
比較例２
Ｔ ＋ ｃ５ｓｗｔ％、Ｔ ｉ Ｎ２８ｗｔ％、Ｗ Ｃ
１７ｗｔ％よりなる固溶体６８．７５ｗｔ％と、Ｔ ａ
Ｃ８０ｗｔ％、Ｗ Ｑ ２０ｗｔ％よりなる固溶体６
．２５＊ｔ％とＭＯ２Ｃｉｏｗｔ％、Ｎｉ粉１５ｗｔ％
を用いて実施例１と同様にして比較用のサーメットを得
た。Comparative example 2 T + c5swt%, T i N28wt%, W C
68.75 wt% solid solution consisting of 17 wt%, and T a
Solid solution 6 consisting of C80wt% and WQ 20wt%
．． 25*t% and MO2 Ciowt%, Ni powder 15wt%
A comparative cermet was obtained in the same manner as in Example 1.
得られたものについてその組織を光学顕微鏡（ｘ １５
０）で観察したところ第２図に示すように細かい内部ボ
アが多数見られた。The structure of the obtained material was examined using an optical microscope (x 15
0), many fine internal bores were seen as shown in Figure 2.
［発明の効采］
この発明によれば、真空焼結であるにも拘らず焼結時の
脱窒素反応が抑υｊされ、内部ボアのない焼結体が得ら
れ、１ノかも該焼結体の静的常温破壊強度が高い。これ
を工具材料として用いると、断続、連続切削（おいて、
耐チッピング性、耐摩耗性に優れたものとなる。[Effects of the Invention] According to the present invention, the denitrification reaction during sintering is suppressed despite vacuum sintering, and a sintered body without internal bores can be obtained. The body has high static fracture strength at room temperature. When this is used as a tool material, it can be used for intermittent and continuous cutting (
It has excellent chipping resistance and wear resistance.
第１図は比較例１の、第２図は比較例２の組織を示す顕
微鏡写真である。FIG. 1 is a micrograph showing the structure of Comparative Example 1, and FIG. 2 is a micrograph showing the structure of Comparative Example 2.
Claims (1)
８０ｗｔ％とＣｏとＮｉよりなる結合相金属１０〜２０
ｗｔ％およびＭＯ＿２Ｃ２０〜５ｗｔ％よりなる材料を
真空焼結してなるサーメットであつて、前記固溶粉末の
組成は、ＴｉＣ５０〜６０ｗｔ％、ＴｉＮ１０〜３０ｗ
ｔ％、ＷＣ１０〜３０ｗｔ％、ＴａＣ５〜１５ｗｔ％で
あり、ＣｏとＮｉの組成比は１：０．８〜１．２の範囲
内であることを特徴とする窒化チタン系サーメット。TiC-TiN-WC-TaC quaternary solid solution powder 70~
Binding phase metal 10-20 consisting of 80wt% Co and Ni
The cermet is made by vacuum sintering a material consisting of 20 to 5 wt% of TiC and 20 to 5 wt% of MO_2C, and the composition of the solid solution powder is 50 to 60 wt% of TiC and 10 to 30 wt% of TiN.
t%, WC10-30wt%, TaC 5-15wt%, and the composition ratio of Co and Ni is within the range of 1:0.8-1.2.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP62035723A JPH0635625B2 (en) | 1987-02-20 | 1987-02-20 | Method for producing wear resistant titanium nitride cermet |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP62035723A JPH0635625B2 (en) | 1987-02-20 | 1987-02-20 | Method for producing wear resistant titanium nitride cermet |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS63203743A true JPS63203743A (en) | 1988-08-23 |
| JPH0635625B2 JPH0635625B2 (en) | 1994-05-11 |
Family
ID=12449773
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP62035723A Expired - Lifetime JPH0635625B2 (en) | 1987-02-20 | 1987-02-20 | Method for producing wear resistant titanium nitride cermet |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH0635625B2 (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0288729A (en) * | 1988-09-27 | 1990-03-28 | Nippon Tungsten Co Ltd | Production of sintered hard alloy |
Citations (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS54149311A (en) * | 1978-05-16 | 1979-11-22 | Mitsubishi Metal Corp | Tough cermet |
| JPS5510657A (en) * | 1978-07-07 | 1980-01-25 | Laurel Bank Machine Co | Device for preventing illegal take out in bill dispenser |
| JPS5687648A (en) * | 1979-12-14 | 1981-07-16 | O S G Kk | Cermet coated with hard metal compound |
| JPS57169058A (en) * | 1981-04-07 | 1982-10-18 | Sumitomo Electric Ind Ltd | Sintered hard alloy for working of hard to machine material |
| JPS5931584A (en) * | 1982-07-15 | 1984-02-20 | 松下電工株式会社 | Cord bushing |
| JPS60106941A (en) * | 1983-11-14 | 1985-06-12 | Hitachi Choko Kk | Tough cermet |
| JPS60106938A (en) * | 1983-11-14 | 1985-06-12 | Hitachi Choko Kk | Tough cermet |
| JPS613853A (en) * | 1984-06-18 | 1986-01-09 | Sumitomo Electric Ind Ltd | Manufacture of sintered hard alloy |
| JPS61243139A (en) * | 1985-04-19 | 1986-10-29 | Sumitomo Electric Ind Ltd | Manufacture of sintered hard alloy |
-
1987
- 1987-02-20 JP JP62035723A patent/JPH0635625B2/en not_active Expired - Lifetime
Patent Citations (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS54149311A (en) * | 1978-05-16 | 1979-11-22 | Mitsubishi Metal Corp | Tough cermet |
| JPS5510657A (en) * | 1978-07-07 | 1980-01-25 | Laurel Bank Machine Co | Device for preventing illegal take out in bill dispenser |
| JPS5687648A (en) * | 1979-12-14 | 1981-07-16 | O S G Kk | Cermet coated with hard metal compound |
| JPS57169058A (en) * | 1981-04-07 | 1982-10-18 | Sumitomo Electric Ind Ltd | Sintered hard alloy for working of hard to machine material |
| JPS5931584A (en) * | 1982-07-15 | 1984-02-20 | 松下電工株式会社 | Cord bushing |
| JPS60106941A (en) * | 1983-11-14 | 1985-06-12 | Hitachi Choko Kk | Tough cermet |
| JPS60106938A (en) * | 1983-11-14 | 1985-06-12 | Hitachi Choko Kk | Tough cermet |
| JPS613853A (en) * | 1984-06-18 | 1986-01-09 | Sumitomo Electric Ind Ltd | Manufacture of sintered hard alloy |
| JPS61243139A (en) * | 1985-04-19 | 1986-10-29 | Sumitomo Electric Ind Ltd | Manufacture of sintered hard alloy |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0288729A (en) * | 1988-09-27 | 1990-03-28 | Nippon Tungsten Co Ltd | Production of sintered hard alloy |
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0635625B2 (en) | 1994-05-11 |
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