JPH04124271A - Coated sintered hard alloy - Google Patents
Coated sintered hard alloyInfo
- Publication number
- JPH04124271A JPH04124271A JP24117390A JP24117390A JPH04124271A JP H04124271 A JPH04124271 A JP H04124271A JP 24117390 A JP24117390 A JP 24117390A JP 24117390 A JP24117390 A JP 24117390A JP H04124271 A JPH04124271 A JP H04124271A
- Authority
- JP
- Japan
- Prior art keywords
- layer
- coated
- tic
- tac
- hard alloy
- 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.)
- Pending
Links
- 239000000956 alloy Substances 0.000 title claims abstract description 8
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 8
- 239000010410 layer Substances 0.000 claims abstract description 30
- 239000010953 base metal Substances 0.000 claims abstract description 13
- 239000011247 coating layer Substances 0.000 claims abstract description 11
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 7
- 229910052751 metal Inorganic materials 0.000 claims abstract description 6
- 239000002184 metal Substances 0.000 claims abstract description 6
- 239000002245 particle Substances 0.000 claims description 6
- 239000000203 mixture Substances 0.000 claims description 4
- 229910052721 tungsten Inorganic materials 0.000 abstract description 5
- 229910003074 TiCl4 Inorganic materials 0.000 abstract 1
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 abstract 1
- 229910052593 corundum Inorganic materials 0.000 abstract 1
- XJDNKRIXUMDJCW-UHFFFAOYSA-J titanium tetrachloride Chemical compound Cl[Ti](Cl)(Cl)Cl XJDNKRIXUMDJCW-UHFFFAOYSA-J 0.000 abstract 1
- 229910001845 yogo sapphire Inorganic materials 0.000 abstract 1
- 239000010936 titanium Substances 0.000 description 14
- 238000000576 coating method Methods 0.000 description 11
- 239000000463 material Substances 0.000 description 10
- 239000011248 coating agent Substances 0.000 description 9
- NFFIWVVINABMKP-UHFFFAOYSA-N methylidynetantalum Chemical compound [Ta]#C NFFIWVVINABMKP-UHFFFAOYSA-N 0.000 description 8
- 229910003468 tantalcarbide Inorganic materials 0.000 description 8
- NRTOMJZYCJJWKI-UHFFFAOYSA-N Titanium nitride Chemical compound [Ti]#N NRTOMJZYCJJWKI-UHFFFAOYSA-N 0.000 description 7
- 230000000052 comparative effect Effects 0.000 description 7
- 230000007423 decrease Effects 0.000 description 5
- 230000000694 effects Effects 0.000 description 3
- 230000003647 oxidation Effects 0.000 description 3
- 238000007254 oxidation reaction Methods 0.000 description 3
- 239000002994 raw material Substances 0.000 description 3
- 230000009257 reactivity Effects 0.000 description 3
- 229910000831 Steel Inorganic materials 0.000 description 2
- 239000002131 composite material Substances 0.000 description 2
- 230000006378 damage Effects 0.000 description 2
- 238000002156 mixing Methods 0.000 description 2
- 239000000843 powder Substances 0.000 description 2
- 238000005245 sintering Methods 0.000 description 2
- 239000010959 steel Substances 0.000 description 2
- 238000002230 thermal chemical vapour deposition Methods 0.000 description 2
- VEXZGXHMUGYJMC-UHFFFAOYSA-M Chloride anion Chemical compound [Cl-] VEXZGXHMUGYJMC-UHFFFAOYSA-M 0.000 description 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
- 230000004888 barrier function Effects 0.000 description 1
- 239000011230 binding agent Substances 0.000 description 1
- 239000010941 cobalt Substances 0.000 description 1
- 229910017052 cobalt Inorganic materials 0.000 description 1
- GUTLYIVDDKVIGB-UHFFFAOYSA-N cobalt atom Chemical compound [Co] GUTLYIVDDKVIGB-UHFFFAOYSA-N 0.000 description 1
- 238000013329 compounding Methods 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 238000009472 formulation Methods 0.000 description 1
- 239000002075 main ingredient Substances 0.000 description 1
- 238000000034 method Methods 0.000 description 1
- 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 description 1
- UONOETXJSWQNOL-UHFFFAOYSA-N tungsten carbide Chemical compound [W+]#[C-] UONOETXJSWQNOL-UHFFFAOYSA-N 0.000 description 1
Landscapes
- Chemical Vapour Deposition (AREA)
Abstract
Description
【発明の詳細な説明】
〈産業上の利用分野〉
本発明は、切削工具、特に高速切削用旋削工具として使
用される被覆超硬合金に関する。DETAILED DESCRIPTION OF THE INVENTION <Industrial Application Field> The present invention relates to a coated cemented carbide used as a cutting tool, particularly a turning tool for high-speed cutting.
〈従来の技術〉
従来より、例えば高速切削用旋削工具として被覆超硬合
金、すなわち、母材としてＷＣ（炭化タングステン）基
合金などを用い、これにＴｉＮ （窒化チタン）、Ｔｉ
Ｃ（炭化チタン）又はＡｊ２０．（ｌＩ化グアルミニウ
ムなどの被覆材を用いて被覆を施したものが用いられて
いる。<Prior art> Conventionally, for example, a coated cemented carbide, that is, a WC (tungsten carbide)-based alloy as a base material, has been used as a turning tool for high-speed cutting, and TiN (titanium nitride), Ti
C (titanium carbide) or Aj20. (Those coated with a coating material such as glaluminium chloride are used.
このような被覆超硬合金の母材は、被覆の脆さを補う必
要があるので靭性を有する必要がある。又、被覆の厚さ
は１〜ｌＯμｍと薄いことから、母材自身が靭性変形を
して被覆が損傷を受けることを阻止する必要がある。The base material of such a coated cemented carbide needs to have toughness to compensate for the brittleness of the coating. Further, since the thickness of the coating is as thin as 1 to 10 μm, it is necessary to prevent the base material itself from undergoing toughness deformation and damage to the coating.
そこで、一般には高硬度の炭化物としてのＷＣを主体と
し、これに、硬さ及び耐熱性改善のためにＴｉｃと、耐
酸化性を向上させると共にＷＣ，ＴｉＣの粒成長を抑制
するＴａＣ（炭化タンタル）とを混合し、結合金属とし
てＣｏ（コバルト）を用いた超硬合金が使用されている
。Therefore, in general, WC as a highly hard carbide is used as the main ingredient, and Tic is added to this to improve hardness and heat resistance, and TaC (tantalum carbide) is added to improve oxidation resistance and suppress grain growth of WC and TiC. ) and using Co (cobalt) as the bonding metal.
一方、被覆材としては、耐摩耗性が高く、耐熱性があり
、又超硬合金と被加工材との間の拡散を防止する効果的
なバリアとして働く化学的に安定であることが要求され
ている。On the other hand, the coating material must be highly wear resistant, heat resistant, and chemically stable to act as an effective barrier to prevent diffusion between the cemented carbide and the workpiece. ing.
このため従来ではＴｉＣ層を超硬合金の表面に第−層と
して被覆し、次にＴｉＮ、Ａｊ２０３等の被覆層を形成
して多層被覆を行っている。For this reason, conventionally, a TiC layer is coated on the surface of the cemented carbide as a third layer, and then a coating layer of TiN, Aj203, etc. is formed to perform multilayer coating.
〈発明が解決しようとする課題〉
しかし、前述した超硬合金を切創工具とした場合、被加
工材との摩擦熱により切削条件によっては刃先温度が１
２００℃にも上昇するので、室温ではほとんど塑性変形
しない超硬合金も塑性変形を起こすようになる。したが
って、これにより突出部ができて不均一に荷重がかかる
ため、ＴｉＣ，ＴｉＮ、Ａｊ Ｏなとの高温で安定な被
覆は、１〜１０μｍと薄いこともあって急速に摩耗して
しまい、工具の寿命を大幅に低下させる原因となる。<Problem to be solved by the invention> However, when the above-mentioned cemented carbide is used as a cutting tool, the temperature of the cutting edge may decrease to 1 depending on cutting conditions due to frictional heat with the workpiece.
Since the temperature rises to 200°C, cemented carbide, which hardly deforms plastically at room temperature, begins to undergo plastic deformation. Therefore, this creates protrusions and loads are applied unevenly, so coatings that are stable at high temperatures, such as TiC, TiN, and AjO, wear out quickly because they are thin (1 to 10 μm), and the tool wears out quickly. This causes a significant reduction in the lifespan of the product.
また、被覆超硬合金の寿命はこのような被覆の寿命に依
存すると共に、被覆が摩耗した部分の地金の耐摩耗性に
も影響される。Furthermore, the lifespan of the coated cemented carbide depends on the lifespan of such a coating, and is also influenced by the wear resistance of the base metal in the area where the coating is worn.
ところで、高硬度炭化物であるＷ Ｃ！！ 高温での硬
さは優れているが、耐酸化性が劣り、又、鉄鋼などの被
加工材との反応性の点でもＴｉＣ，ＴａＣより劣る。し
たがって、このように被加工材との反応性の高いＷＣの
割合の高い超硬合金の場合、地金が露出した部分の摩耗
が激しく、工具寿命が大幅に低下するという問題がある
。By the way, WC! is a high hardness carbide! ! Although it has excellent hardness at high temperatures, it has poor oxidation resistance and is also inferior to TiC and TaC in terms of reactivity with workpiece materials such as steel. Therefore, in the case of a cemented carbide having a high proportion of WC, which is highly reactive with the workpiece, there is a problem in that the parts where the bare metal is exposed are severely worn, and the tool life is significantly reduced.
一方、被覆層の第−層に被覆されるＴｉＣは母材の超硬
合金に比べて著しく脆（ＴｉＣ自身の破壊による剥離に
より、工具の耐摩耗性が決定されるという問題がある。On the other hand, the TiC coated in the first layer of the coating layer is significantly brittle compared to the base cemented carbide (there is a problem in that the wear resistance of the tool is determined by peeling off due to destruction of the TiC itself).
又、ＴｉＣの被覆時に母地との界面にｃｏ３Ｗ３Ｃ又は
ｃｏ、ｗ６Ｃ（η相）が生ずる場合があるが、このη相
は脆いため、特に地金の強靭性を低下させた場合にはη
相の発生を避けなくてはならないという問題がある。In addition, co3W3C or co, w6C (η phase) may be generated at the interface with the base metal when TiC is coated, but since this η phase is brittle, especially when the toughness of the base metal is reduced, η
There is a problem in that the generation of phases must be avoided.
本発明はこのような事情に鑑み、被覆超硬合金の耐摩耗
性及び寿命を大幅に増大させると共に工具として安定し
て用いることができる被覆超硬合金を提供することを目
的とする。In view of these circumstances, an object of the present invention is to provide a coated cemented carbide that can significantly increase the wear resistance and life of the coated cemented carbide and can be stably used as a tool.
く課題を解決するための手段〉
前記目的を達成する本発明の被覆超硬合金は、硬質相形
成成分としてＷＣ，（Ｗ、 Ｔｉ） Ｃ及びＴａＣを、
結合全異相としてＧｏを含有する被覆超硬合金工具用地
金の表面に、Ｔｉ （Ｃ，Ｎ）層を介して被覆層を設け
てなることを特徴とする。Means for Solving the Problems> The coated cemented carbide of the present invention that achieves the above object contains WC, (W, Ti) C, and TaC as hard phase forming components.
The present invention is characterized in that a coating layer is provided on the surface of a coated cemented carbide tool base metal containing Go as a combined heterophase with a Ti (C,N) layer interposed therebetween.
以下本発明の詳細な説明する。The present invention will be explained in detail below.
ここで本発明でＴｉ （Ｃ，Ｎ１層とは被覆超硬合金
工具用地金の表面の第一被覆層として被覆する複合チタ
ン層をいうものであり、ＴｉＣ層４． ＣＨ４，Ｎ、、
Ｈ，を原料として例えば熱ＣＶＤ法等のコーティング
方法によりＴｉ（Ｃ，Ｎ）層を形成するものである。こ
のＴＩＣｃｐ Ｎ）の硬さとしては、微小硬さでＴｉＣ
（３２００ｋｇｆ／ｍ ）とＴｉＮ （１９５０ｋｇｆ
／ ｙｍ” ）との中間であり、靭性の点ではＴｉＣよ
りも改善されている。Here, in the present invention, the Ti(C,N1 layer) refers to a composite titanium layer coated as the first coating layer on the surface of the coated cemented carbide tool base metal, and the TiC layer 4.CH4,N,...
A Ti(C,N) layer is formed by a coating method such as a thermal CVD method using H as a raw material. The hardness of this TICcp N) is micro hardness and TiC
(3200kgf/m) and TiN (1950kgf/m)
/ym”), and is improved over TiC in terms of toughness.
又、本発明で被覆超硬合金工具用地金（以下「地金」と
いう）とは、硬質相形成成分としｒＷｃ、（Ｗ、Ｔ ｉ
）Ｃ及びＴａＣを主成分とすると共に結合相としてＣ
ｏを用いてなるものであゆ、これらの所望配合によった
原料を金型ブレスを用いて真空焼結し、所望の切削用工
具を得るものである。In addition, in the present invention, the coated cemented carbide tool base metal (hereinafter referred to as "base metal") refers to hard phase forming components rWc, (W, Ti
) C and TaC as main components and C as a binder phase
The desired cutting tool is obtained by vacuum sintering the raw materials with the desired composition using a mold press.
特に切削温度近傍（約１２００℃）での塑性変形能を低
下させるためには、平均粒径２〜５μｍのＷＣが５５〜
６５重量％、平均粒径１〜２μｍの（Ｗ Ｏ，７、Ｔ
ｉ Ｏ，３） Ｃが２５〜３０重量％、平均粒径１〜２
μｍのＴａＣが８〜１２重量％、Ｃｏが３〜７重量％の
組成とすることが好ましい。In particular, in order to reduce the plastic deformability near the cutting temperature (approximately 1200°C), WC with an average grain size of 2 to 5 μm should be
65% by weight, average particle size 1-2 μm (WO,7,T
i O, 3) C 25-30% by weight, average particle size 1-2
It is preferable that the composition is 8 to 12% by weight of TaC and 3 to 7% by weight of Co.
ここで結合金属相としてのＣｏの配合量を７重量％以下
としたのは、例えば工具としたときの刃先温度が１２０
０℃程度になった場合の塑性変形を低下させ、工具寿命
の大幅な向上を図るという効果を得るためであるが、一
方、Ｃｏの配合量を低下させると、ポロシティ−が増す
と共に靭性が低下し、摩耗でなく欠損により工具寿命が
低下してしまうので、ｃｏは３重量％す上は必要である
。Here, the content of Co as a binding metal phase is set to 7% by weight or less because, for example, the cutting edge temperature when used as a tool is 120%.
This is to achieve the effect of reducing plastic deformation when the temperature reaches about 0°C and significantly improving tool life. On the other hand, if the Co content is reduced, porosity increases and toughness decreases. However, since the tool life is reduced due to chipping rather than wear, at least 3% by weight of Co is required.
また、本発明でＷＣの配合量を６５重量％息下としたの
は被加工材との反応性を低下させて工具寿命を増するた
めであるが、一方、ＷＣは高硬度炭化物の中でも靭性に
優れているので５５重量％以上は配合する必要がある。In addition, the reason why the blending amount of WC is 65% by weight in the present invention is to reduce the reactivity with the workpiece material and increase the tool life. Since it has excellent properties, it is necessary to incorporate it in an amount of 55% by weight or more.
また、本発明では、Ｃｏの配合量を低下させると共にＷ
Ｃの配合量を低下させることによる靭性の低下を補うた
め、使用するＷＣの平均粒径を従来の１μｍ程度から２
〜５μｍ程度まで粗くしている。In addition, in the present invention, the content of Co is reduced and W
In order to compensate for the decrease in toughness caused by reducing the amount of C blended, the average particle size of the WC used was increased from the conventional approximately 1 μm to 2 μm.
It is roughened to about 5 μm.
さらに、本発明では、ＷＣの配合を低下させた分、ＷＣ
とＴｉＣとの複合炭化物（Ｗｏ、７゜Ｔｉ０．３）Ｃで
補っている。ＷＣをＴｉＣやＴａＣで補うと靭性が著し
く低下して抗折力も大幅に低下するが、（Ｗ Ｏ，７、
Ｔ ｉ Ｏ，３） Ｃば被加工材との反応性ばＷＣより
も小さく、Ｔ２Ｏ程には靭性を低下させないものである
。Furthermore, in the present invention, by reducing the WC content, the WC
It is supplemented with a composite carbide (Wo, 7°Ti0.3) of C and TiC. When WC is supplemented with TiC or TaC, the toughness and transverse rupture strength decrease significantly, but (WO, 7,
T i O, 3) C has a lower reactivity with the workpiece than WC and does not reduce toughness as much as T2O.
そこで、本発明では（Ｗｏ、７ 、 Ｔ ｉ Ｏ，３）
Ｃを微細な１〜２μｍの平均粒径の粉体で２５〜３０
重量％の配合量としている。Therefore, in the present invention, (Wo, 7, T i O, 3)
C in fine powder with an average particle size of 1 to 2 μm at 25 to 30
The amount is expressed as % by weight.
一方、ＴａＣは従来のものと同様に耐酸化性の向上と共
にＷＣ、（Ｗ、 Ｔ ｉ ） Ｃの粒成長を抑制するた
めに必要であり、微細な１〜２μｍの平均粒径の粒体で
、配合量８〜１２重量％とじた。８重量％未満では上記
効果が発揮されず、１２重量％をこえると、靭性。On the other hand, TaC is necessary to improve oxidation resistance as well as to suppress grain growth of WC and (W, Ti)C, as in conventional products, and is used in fine grains with an average grain size of 1 to 2 μm. , the blending amount was 8 to 12% by weight. If the amount is less than 8% by weight, the above effects will not be exhibited, and if it exceeds 12% by weight, the toughness will deteriorate.
抗折力の低下が著しくなるためである。This is because the transverse rupture strength decreases significantly.
く実 施 例〉 以下、本発明を実施例に基づいて説明する。Example of implementation Hereinafter, the present invention will be explained based on examples.
第１表
第１表記載の配合比の原料粉末を混合し、スローアウェ
イチップ用の金型でプレスを行い、温度１４００℃で真
空焼結を行った。Raw material powders having the compounding ratios listed in Table 1 were mixed, pressed in a mold for an indexable chip, and vacuum sintered at a temperature of 1400°C.
その後、焼結して得た工具に刃付けを行い、第２表に示
す配合によって熱ＣＶＤ法により被覆し、切創試験を行
い、逃げ面摩耗量を測定した。Thereafter, the tools obtained by sintering were sharpened and coated by thermal CVD according to the formulation shown in Table 2, and a cut test was conducted to measure the amount of flank wear.
なお、逃げ面摩耗量ＶＢは第１図に示すように逃げ面の
摩耗した部分の最大幅をいう。また、試験には被削材と
して５０Ｍ４４０ （Ｈ２８５〜３００）を用い、送＾
０．３４ｍ／回、切り込み１．５＋ｍ、切削速度１６５
ｍ ／ ＋ｉｉｎと２００ｍ／組ｎで実施した。The amount of flank wear VB refers to the maximum width of the worn portion of the flank, as shown in FIG. In addition, 50M440 (H285-300) was used as the work material in the test, and the feed ^
0.34m/times, depth of cut 1.5+m, cutting speed 165
It was carried out at m/+iin and 200 m/set n.
第２図に切削速度１６５ ｍ／ｗｉｎの結果を示す。Figure 2 shows the results at a cutting speed of 165 m/win.
同図に示すように、実施例１のＴｉ （Ｃ，Ｎ）層／
Ｔ ｉ ０層の場合のものが比較例１，２より摩耗量が
最も少なくなっている。また、比較例１のＴｉＣ層単独
の場合、初期の摩耗量が大きく、切削距離が増しても摩
耗量は大きくなっている。これは初期にＴ ｉ Ｃが剥
離する傾向があるためである。また比較例２のＴｉＮ／
ＴｉＣ層の場合、ＴｉＣ層単独よりも摩耗量は少なくな
っているが、実施例１よりは劣っている。As shown in the figure, the Ti (C,N) layer of Example 1/
The amount of wear in the case of the T i 0 layer is the smallest compared to Comparative Examples 1 and 2. Further, in the case of the TiC layer alone in Comparative Example 1, the initial wear amount was large, and even when the cutting distance increased, the wear amount remained large. This is because T i C tends to peel off in the initial stage. In addition, TiN/
In the case of the TiC layer, the amount of wear is smaller than that of the TiC layer alone, but it is inferior to Example 1.
第３図に切削速度２００ ｍ ／ ｗｉｎの結果を示す
。Figure 3 shows the results at a cutting speed of 200 m/win.
同図に示すように、実施例１のＴｉ （Ｃ，Ｎ）層／
Ｔ ｉ ０層の場合のものが比較例１，２よりも摩耗量
が最も少なくなっている。また比較例については比較例
２のＴｉＮ層／ Ｔ ｉ ０層の場合がＴｉＣ層単独の
比較例１のものより摩耗量が高くなっていた。As shown in the figure, the Ti (C,N) layer of Example 1/
The amount of wear in the case of the T i 0 layer is the smallest compared to Comparative Examples 1 and 2. Regarding the comparative examples, the amount of wear in the case of the TiN layer/T i 0 layer of comparative example 2 was higher than that of comparative example 1 of the TiC layer alone.
以上の結果より、地金の表面にＴｉＣ（Ｃ，Ｎ）の複合
チタン層を介して例えばＴｉＣ層、 ＴｉＣ層／入／Ａ
ｌ２Ｏ３層被覆層を設けてなる被覆起硬合金は高速切削
において、非常に優れた特性を示すことが判明した。From the above results, for example, a TiC layer, a TiC layer/input/A
It has been found that the coated hardened alloy provided with the l2O3 coating layer exhibits very excellent properties in high-speed cutting.
このように地金に被覆層を形成するに際し、Ｔｉ （
Ｃ，Ｎ）層を介して例えばＴｉＣ層を被覆することによ
り、Ｔｉ （Ｃ，Ｎ）層が緩衝材の役割を果たしＴｉ
Ｃの剥離が大幅に改善されることとなる。When forming a coating layer on the base metal in this way, Ti (
For example, by coating a TiC layer through a Ti(C,N) layer, the Ti(C,N) layer acts as a buffer material and the Ti(C,N) layer acts as a buffer material.
The peeling of C is significantly improved.
〈発明の効果〉
以上説明したように、本発明は、被覆超硬合金工具用地
金表面にＴｉ （Ｃ，Ｎ）層を介して被覆層を設けて
なるので、該被覆層の剥離を大幅に改善し、例えば鋼の
高速切削性能を大幅に向上させることができる。<Effects of the Invention> As explained above, the present invention provides a coating layer on the surface of the base metal for coated cemented carbide tools via a Ti (C,N) layer, so that peeling of the coating layer can be greatly reduced. For example, the high-speed cutting performance of steel can be significantly improved.
第１図はチップの逃げ面摩耗量を示す説明図、第２図及
び第３図はそれぞれ本発明の実施例及び比較例の切創試
験結果を示すグラフである。FIG. 1 is an explanatory diagram showing the amount of wear on the flank face of the tip, and FIGS. 2 and 3 are graphs showing the results of the cut test of the example of the present invention and the comparative example, respectively.
Claims (2)
ＴａＣを、結合金属相としてＣｏを含有する被覆硬合金
工具用地金の表面に、Ｔｉ（Ｃ，Ｎ）層を介して被覆層
を設けてなることを特徴とする被覆超硬合金。(1) A coating layer is formed on the surface of a coated hard alloy tool ingot containing WC, (W,Ti)C and TaC as hard phase forming components and Co as a bonding metal phase via a Ti(C,N) layer. A coated cemented carbide characterized by being provided with.
超硬合金工具用地金の組成が平均粒径２〜５μｍのＷＣ
が５５〜６５重量％、平均粒径１〜２μｍの（Ｗ０．７
，Ｔｉ０．３）Ｃが２５〜３０重量％、平均粒径１〜２
μｍのＴａＣが８〜１２重量％、Ｃｏが３〜７重量％で
あることを特徴とする被覆超硬合金。(2) In the coated cemented carbide according to claim 1, the composition of the coated cemented carbide tool base metal is WC having an average grain size of 2 to 5 μm.
is 55 to 65% by weight, and the average particle size is 1 to 2 μm (W0.7
, Ti0.3) C 25-30% by weight, average particle size 1-2
A coated cemented carbide characterized in that TaC in μm is 8 to 12% by weight and Co is 3 to 7% by weight.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP24117390A JPH04124271A (en) | 1990-09-13 | 1990-09-13 | Coated sintered hard alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP24117390A JPH04124271A (en) | 1990-09-13 | 1990-09-13 | Coated sintered hard alloy |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JPH04124271A true JPH04124271A (en) | 1992-04-24 |
Family
ID=17070330
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP24117390A Pending JPH04124271A (en) | 1990-09-13 | 1990-09-13 | Coated sintered hard alloy |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPH04124271A (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US8326179B2 (en) | 2008-11-28 | 2012-12-04 | Brother Kogyo Kabushiki Kaisha | Tandem type photosensitive unit and image forming apparatus |
| CN110373592A (en) * | 2019-08-23 | 2019-10-25 | 株洲华锐精密工具股份有限公司 | A kind of Ti (C, N) based metal ceramic cutter material and preparation method thereof |
-
1990
- 1990-09-13 JP JP24117390A patent/JPH04124271A/en active Pending
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US8326179B2 (en) | 2008-11-28 | 2012-12-04 | Brother Kogyo Kabushiki Kaisha | Tandem type photosensitive unit and image forming apparatus |
| CN110373592A (en) * | 2019-08-23 | 2019-10-25 | 株洲华锐精密工具股份有限公司 | A kind of Ti (C, N) based metal ceramic cutter material and preparation method thereof |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| JPS5985860A (en) | Parts of cutting tool | |
| JPH0196084A (en) | Surface-coated cubic boron nitride-based material sintered under superhigh pressure to be used for cutting tool | |
| JPH0568548B2 (en) | ||
| JP2002129306A (en) | Dispersion strengthened composite hard coating and tools coated by the same | |
| JPH04124271A (en) | Coated sintered hard alloy | |
| JP2008296292A (en) | Surface-coated cutting tool having hard coating layer exhibiting superior chipping resistance | |
| JPS6225631B2 (en) | ||
| JP2607592B2 (en) | High wear resistant polycrystalline diamond tool and method of manufacturing the same | |
| JP3269305B2 (en) | Surface coated tungsten carbide based cemented carbide cutting tool with excellent interlayer adhesion with hard coating layer | |
| JP2926883B2 (en) | Surface-coated hard member with excellent wear resistance | |
| JP2625923B2 (en) | Surface coated cermet for cutting tools | |
| JPH10237650A (en) | Wc base cemented carbide and its production | |
| JP3099834B2 (en) | Surface coated titanium carbonitride based cermet cutting tool with excellent toughness | |
| JP2000336451A (en) | Modified sintered alloy, coated sintered alloy, and their production | |
| JPH10337602A (en) | Cutting tool made of surface covering cemented carbide and having thick artificial diamond covering layer having superior peeling resistance | |
| JPH0353070A (en) | Surface coated tool member having excellent wear resistance | |
| JP2018164951A (en) | Surface-coated cutting tool | |
| JPH0394062A (en) | Diamond-coated sintered hard alloy | |
| JPS6141873B2 (en) | ||
| JPH07164209A (en) | Composite cutting tool | |
| JPS6067638A (en) | Cermet for cutting tool and hot processing tool | |
| JP2970201B2 (en) | Surface coated Ti-based carbonitride-based cermet cutting tool with excellent adhesion of hard coating layer | |
| JPH032348A (en) | Base metal for coated sintered hard alloy tool | |
| JPH06170611A (en) | Surface coating tungsten carbide base cemented carbide cutting tool | |
| JPH0382767A (en) | Cutting tool made of surface coated tungsten carbide-base sintered hard alloy excellent in adhesive strength of hard coating layer |