JPH04135105A - Coated hard alloy tool - Google Patents
Coated hard alloy toolInfo
- Publication number
- JPH04135105A JPH04135105A JP10823890A JP10823890A JPH04135105A JP H04135105 A JPH04135105 A JP H04135105A JP 10823890 A JP10823890 A JP 10823890A JP 10823890 A JP10823890 A JP 10823890A JP H04135105 A JPH04135105 A JP H04135105A
- Authority
- JP
- Japan
- Prior art keywords
- layer
- micron
- tin
- tic
- deveta
- 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
- 229910045601 alloy Inorganic materials 0.000 title claims abstract description 9
- 239000000956 alloy Substances 0.000 title claims abstract description 9
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 claims abstract description 16
- 238000000576 coating method Methods 0.000 claims abstract description 11
- 150000004767 nitrides Chemical class 0.000 claims abstract description 11
- 239000011248 coating agent Substances 0.000 claims abstract description 9
- 230000000737 periodic effect Effects 0.000 claims abstract description 3
- 239000000758 substrate Substances 0.000 claims description 16
- 239000002184 metal Substances 0.000 claims description 4
- 229910052751 metal Inorganic materials 0.000 claims description 4
- 150000001247 metal acetylides Chemical class 0.000 claims description 2
- 239000000203 mixture Substances 0.000 claims description 2
- 238000006243 chemical reaction Methods 0.000 abstract description 4
- PNEYBMLMFCGWSK-UHFFFAOYSA-N aluminium oxide Inorganic materials [O-2].[O-2].[O-2].[Al+3].[Al+3] PNEYBMLMFCGWSK-UHFFFAOYSA-N 0.000 abstract description 2
- 229910052593 corundum Inorganic materials 0.000 abstract description 2
- 229910001845 yogo sapphire Inorganic materials 0.000 abstract description 2
- JMANVNJQNLATNU-UHFFFAOYSA-N oxalonitrile Chemical compound N#CC#N JMANVNJQNLATNU-UHFFFAOYSA-N 0.000 abstract 1
- 239000010410 layer Substances 0.000 description 30
- 238000005520 cutting process Methods 0.000 description 20
- 239000012071 phase Substances 0.000 description 12
- 239000000843 powder Substances 0.000 description 8
- 239000000463 material Substances 0.000 description 5
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 4
- 229910052799 carbon Inorganic materials 0.000 description 4
- 238000005229 chemical vapour deposition Methods 0.000 description 4
- 229910009043 WC-Co Inorganic materials 0.000 description 3
- 239000012298 atmosphere Substances 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 238000000034 method Methods 0.000 description 3
- 239000012299 nitrogen atmosphere Substances 0.000 description 3
- 239000002245 particle Substances 0.000 description 3
- -1 TiC or TiN Chemical class 0.000 description 2
- 239000011247 coating layer Substances 0.000 description 2
- 239000007789 gas Substances 0.000 description 2
- VNWKTOKETHGBQD-UHFFFAOYSA-N methane Chemical compound C VNWKTOKETHGBQD-UHFFFAOYSA-N 0.000 description 2
- 238000005245 sintering Methods 0.000 description 2
- 238000004381 surface treatment Methods 0.000 description 2
- 238000003466 welding Methods 0.000 description 2
- 229910000746 Structural steel Inorganic materials 0.000 description 1
- 238000005299 abrasion Methods 0.000 description 1
- 239000011230 binding agent Substances 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 238000005255 carburizing Methods 0.000 description 1
- 150000001875 compounds Chemical class 0.000 description 1
- 238000005336 cracking Methods 0.000 description 1
- 238000005262 decarbonization Methods 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 239000007791 liquid phase Substances 0.000 description 1
- 238000003754 machining Methods 0.000 description 1
- 238000003801 milling Methods 0.000 description 1
- 229910052757 nitrogen Inorganic materials 0.000 description 1
- 238000005498 polishing Methods 0.000 description 1
- 230000002250 progressing effect Effects 0.000 description 1
- 230000001902 propagating effect Effects 0.000 description 1
- 239000000126 substance Substances 0.000 description 1
Abstract
Description
【発明の詳細な説明】
[産業上の利用分野]
本発明は超硬合金の被覆、特に基体と皮膜の密着性の改
良に関する。DETAILED DESCRIPTION OF THE INVENTION [Industrial Application Field] The present invention relates to coatings of cemented carbide, particularly to improving the adhesion between a substrate and a coating.
[従来の技術]
従来、超硬合金にT i C,T j、 N、 A
]、 zos等を被覆した工具に関し、ては数多くの製
品が実用化されているが、その傾向は耐摩耗性の向上を
主眼とした改善であった。[Conventional technology] Conventionally, cemented carbide has T i C, T j, N, A
], ZOS, etc., many products have been put into practical use, but the trend has been to improve their wear resistance.
しかし、被覆工具の用途拡大によってその使用される領
域も拡大し、荒加工、重断続切削等にも使用可能な工具
が要求されている。However, as the applications of coated tools expand, the areas in which they are used also expand, and tools that can be used for rough machining, heavy interrupted cutting, etc. are required.
また、高速切削化も進み、中または軽断続切削では仕上
げに近い速度で行われるため、化学的な安定性にたいし
ても長寿命化が求められている。In addition, high-speed cutting is progressing, and medium or lightly interrupted cutting is performed at a speed close to finishing, so there is a need for longer life in terms of chemical stability.
しかし、超硬合金は基本的に脆性材料であるためチッピ
ング、衝撃等による欠けが生じやすく、また皮膜に関し
ても連続切削でないため、膜相互間の密着性が十分でな
いと剥離しやすい。However, since cemented carbide is basically a brittle material, it is prone to chipping and chipping due to impact, etc. Also, since the coating is not continuously cut, it is likely to peel off if the adhesion between the coatings is not sufficient.
つぎに、超硬合金の基体については、従来M20〜M3
0相当の合金にTiN等の窒化物を添加し、表面近傍に
、いわゆる脱ベータ層を作り(基体表面から5〜50ミ
クロン程度をWC−Co相とする)、皮膜から伝播する
クラック等の伸展を阻害し、基体−皮膜の強度を高める
方法が取られている。 (特開開54−87119)し
かし、この方法では、
1)基体中に多量の窒化物を添加するため、焼結性が悪
くなり、欠陥が発生しやすくなる。Next, regarding the cemented carbide base, conventional M20 to M3
By adding nitrides such as TiN to an alloy equivalent to 0, a so-called deveta layer is created near the surface (approximately 5 to 50 microns from the base surface is the WC-Co phase), and cracks propagating from the film are prevented. Methods have been taken to inhibit this and increase the strength of the substrate-film. (Unexamined Japanese Patent Publication No. 54-87119) However, in this method: 1) Since a large amount of nitride is added to the substrate, sinterability deteriorates and defects are likely to occur.
2)皮膜最内層がTiC,TiN等のTi化合物であり
、接合部分が同種の材料でないため、密着強度が弱く、
特にTiCの場合にはカーボンの移動による脱炭相が生
じやすい等の欠点がある。2) The innermost layer of the film is a Ti compound such as TiC or TiN, and the bonding parts are not made of the same type of material, so the adhesion strength is weak.
Particularly in the case of TiC, there are drawbacks such as a tendency to generate a decarburized phase due to the movement of carbon.
そのため、特開昭54−87119では、基体中にフリ
ーカーボンを0.01〜0.5%程度含有させる等の対
策を講じている。Therefore, in JP-A-54-87119, measures are taken such as containing about 0.01 to 0.5% of free carbon in the substrate.
つぎに、皮膜については、その要因は数多くあり、用途
により特長を持たせる事が可能である。Next, there are many factors that affect the film, and it is possible to give it features depending on the application.
そのため化学蒸着法(CVD)の特長を生かして、強度
を優先する皮膜の適用、すなわち、基体と皮膜間の脱炭
層を少なくするためにはカーボンの移動を阻害する膜質
を選定し、かつ、基体−皮膜間の密着性を確保するため
1つの層を薄くすることに効果がある。Therefore, by taking advantage of the characteristics of chemical vapor deposition (CVD), it is necessary to apply a film that prioritizes strength.In other words, in order to reduce the decarburized layer between the substrate and the film, it is necessary to select a film quality that inhibits the movement of carbon, and to - It is effective to make one layer thinner to ensure adhesion between films.
そのため、本発明者らはJIS M系層硬合金におい
て脱ベータ相を前提とし、脆弱な脱炭層の生成の防止に
関して種々検討した結果、CVD法でTiN皮膜を組み
合わせると脱炭層の原因となるカーボンの移動が減少し
脱炭層の生成が著しく減少するが、同時に窒化物を基体
上に被覆するため基体−皮膜間の密着が悪く実用には適
さなかった。しかし、最内層にTiCを密着性が改善さ
れる程度組み合わせる事により双方のバランスがとれ、
脱ベータ相による強度の向上、密着性をおとさずに、脱
炭層を減少する事が可能となり、総合的に重断続切削の
衝撃によるチ、ツビングや皮膜の剥離に対し、十分な強
度の被覆工具が得られた。Therefore, the present inventors assumed a de-beta phase in the JIS M layered hard alloy, and as a result of various studies on preventing the formation of a brittle decarburized layer, we found that when a TiN film is combined with the CVD method, the carbon that causes the decarburized layer is removed. However, since the nitride is coated on the substrate, the adhesion between the substrate and the coating is poor, making it unsuitable for practical use. However, by combining TiC in the innermost layer to an extent that improves adhesion, a balance between the two can be achieved.
Improved strength due to the de-beta phase, it is possible to reduce the decarburized layer without compromising adhesion, and overall it is a coated tool with sufficient strength against cracking, tubbing and peeling of the coating due to the impact of heavy interrupted cutting. was gotten.
以上のごとく、本発明は周期律表の4a′、5a。 As described above, the present invention applies to items 4a' and 5a of the periodic table.
6a族の炭化物、窒化物、炭窒化物の1種以上と、Fe
族、Cr族の1種以上よりなる超硬質合金を基体とし、
該基体表面に5〜50ミクロンの脱ベータ相を生成し、
その基体上に
1)最内層としてTiC0,2〜1ミクロン2)第2層
としてTiN1.0〜5ミクロン3)第3層としてTi
C,T1CNまたはAL203の1種または2種以上5
〜15ミクロン4)最外層としてTiNを1.0〜5ミ
クロン被覆したことを特徴とする被覆超硬合金工具であ
る。One or more of group 6a carbides, nitrides, and carbonitrides, and Fe
The base material is a super-hard alloy made of one or more members of the Cr group and the Cr group,
producing a deveta phase of 5 to 50 microns on the surface of the substrate;
On the substrate 1) TiC0.2-1 micron as the innermost layer 2) TiN1.0-5 micron as the second layer 3) Ti as the third layer
One or more of C, T1CN or AL2035
~15 microns 4) A coated cemented carbide tool characterized by having a TiN coating of 1.0 to 5 microns as the outermost layer.
本発明による被覆工具の脱ベータ相、皮膜は以下の理由
により限定される。The deveta phase and coating of the coated tool according to the present invention are limited for the following reasons.
1)脱ベータ相 5〜50ミクロン
脱ベータ相の厚さが5ミクロン未満では充分な強度を付
与することが出来ず、50ミクロンをこえると耐摩耗性
(耐溶着性)が悪くなるため5〜50ミクロンとした。1) Debeta phase 5 to 50 microns If the thickness of the deveta phase is less than 5 microns, sufficient strength cannot be imparted, and if it exceeds 50 microns, wear resistance (welding resistance) will deteriorate. It was set to 50 microns.
また、脱ベータ相を生成するた゛めには窒化物を添加し
、その脱窒現象を応用した溶質移動により生成する方法
が一般的に行われているが、本発明では焼結時の雰囲気
調整を窒素雰囲気と浸炭性雰囲気を調整することにより
結合金属量をほぼ同量に保ちつつ生成する事ができる。In addition, in order to generate the de-beta phase, a method is generally used in which nitride is added and the solute transfer is applied to the denitrification phenomenon, but in the present invention, the atmosphere adjustment during sintering is By adjusting the nitrogen atmosphere and the carburizing atmosphere, it is possible to generate the metal while keeping the amount of bonded metal approximately the same.
また、TiNでも十分生成出来るが、他の窒化物でも、
例えばTa、Nb等の5a族の窒化物、炭窒化物でもそ
の添加量と窒素雰囲気調整により十分生成する事ができ
る。In addition, although TiN can be used satisfactorily, other nitrides can also be used.
For example, 5a group nitrides and carbonitrides such as Ta and Nb can be sufficiently produced by adjusting the amount of addition and nitrogen atmosphere.
2)最内層 TiC0,2〜1ミクロン基体WC−Co
合金との密着性を保つためには0.2ミクロン以上必要
であり、また1ミクロンを越えると界面に脱炭層を生じ
やすくなるため0゜2〜1ミクロンとした。2) Innermost layer TiC0.2-1 micron substrate WC-Co
In order to maintain adhesion with the alloy, it is necessary to have a thickness of 0.2 microns or more, and if it exceeds 1 micron, a decarburized layer is likely to occur at the interface, so it is set to 0.2 to 1 micron.
3)第2層 TiN1.O〜5ミクロン基体WC−Co
合金からの脱カーボンを阻害するため、1ミクロン以上
必要であり、また5ミクロンを越えると耐摩耗性の付与
が十分でないため1.0〜5ミクロンとした。3) Second layer TiN1. O~5 micron substrate WC-Co
In order to inhibit decarbonization from the alloy, it is necessary to have a thickness of 1 micron or more, and if it exceeds 5 microns, it will not provide sufficient wear resistance, so it is set to 1.0 to 5 microns.
3)第3層 TiC,T1CNまたハA 1205(0
1種または2種以上
5〜15ミクロン
耐摩耗性を十分にもたせるため、5ミクロン以上必要で
あり、また15ミクロンを越えると皮膜全体の厚さが厚
くなり剥離を生じやすくなるため、5〜15ミクロンと
した。3) Third layer TiC, T1CN or HaA 1205 (0
One or more types of 5 to 15 microns In order to have sufficient abrasion resistance, 5 microns or more is required, and if the thickness exceeds 15 microns, the overall thickness of the film becomes thick and peeling easily occurs, so 5 to 15 microns is required. Micron.
4)最外層 TiN1.O〜5ミクロン耐溶着性を十分
にもたせるため、1.0ミクロン以上必要であり、また
5ミクロンを越えると剥離を生じやすくなるため、1.
0〜5ミクロンとした。4) Outermost layer TiN1. O ~ 5 microns In order to have sufficient welding resistance, 1.0 micron or more is required, and if it exceeds 5 microns, peeling tends to occur, so 1.
The diameter was 0 to 5 microns.
以下、本発明に関し具体的に説明する。The present invention will be specifically explained below.
[実施例1]
市販のWC粉末(平均粒度5.0μm) 、TiC粉
末(同1.O,um) 、TiN粉末(同1゜0μm
)、TaC粉末(1,5μm)及び結合相としてCo粉
末を使用して、−aに旋削用の基体に使用されるJIS
M20相当(組成86WC=2TiC−5TaC−
7Co−0,2TiN)になるように配合した。これら
の粉末をN量を変化させつつ配合し、混合終了後、転帰
した債、プレス成形し、メタン、窒素雰囲気を調整した
真空中1400℃でlhr焼結したのち、SNMA43
2の形状に加工した。[Example 1] Commercially available WC powder (average particle size 5.0 μm), TiC powder (average particle size 1.0 μm), TiN powder (average particle size 1°0 μm)
), using TaC powder (1,5 μm) and Co powder as binder phase, JIS used for turning substrate in -a
Equivalent to M20 (composition 86WC=2TiC-5TaC-
7Co-0,2TiN). These powders were blended while varying the amount of N, and after mixing, the resulting bond was press-molded and sintered for 1 hour at 1400°C in a vacuum with a methane and nitrogen atmosphere adjusted, and then made into SNMA43.
Processed into 2 shapes.
このチップを研磨し脱ベータ層の厚さを測定した結果を
第工表に示す、N量が少ないと十分な脱ベータ層は生成
できずある程度以上の添加量が必要であり、また、添加
はTiNとして実施した。The results of polishing this chip and measuring the thickness of the de-beta layer are shown in the table below. It was implemented as TiN.
第1表
第2表
[実施例2]
実施例1と同様な粉末とTaN粉末(1,5μm)Nb
N粉末(1,5μm)を使用して、液相発生温度以下に
おける焼結時の真空度、保持時間を変化させる事により
脱ベータ層の厚さを変化させ、実施例1と同様な方法で
測定した。第2表にその脱ベータ層の厚さ示す。Table 1 Table 2 [Example 2] Powder similar to Example 1 and TaN powder (1.5 μm) Nb
Using N powder (1.5 μm), the thickness of the deveta layer was changed by changing the degree of vacuum and holding time during sintering below the liquid phase generation temperature, and in the same manner as in Example 1. It was measured. Table 2 shows the thickness of the deveta layer.
TaN、NbN等の窒化物でも添加量と雰囲気の調整に
より十分な厚さの脱ベータ層が得られる。Even with nitrides such as TaN and NbN, a sufficiently thick deveta layer can be obtained by adjusting the amount added and the atmosphere.
[実施例3]
実施例1、試料番号3で用いたJIS M30相当の
超硬合金(脱ベータ相25ミクロンを生成)、でSNM
A432を製作した。その表面に目的に応じて様々な表
面処理を実施した。TiCはCVD反応炉中に設置し、
H,ガスを流しながら、1000℃まで昇温しTiCl
42%、CH44%、H2残からなる混合気体を流量7
リツタ一/min圧力40mmHgの条件で供給し0.
2時間〜3時間反応させ基体上にTiCを0.2〜5ミ
クロンの畿覆層を形成させた。また同様にTiNの場合
はガス系をN22%に変更し0. 2時間〜3時間反応
させ基体上にTiNを0.2〜5ミクロンの被覆層を形
成させた。制作した資料の膜質と膜厚を第1表に示す。[Example 3] SNM was made using the cemented carbide equivalent to JIS M30 used in Example 1 and sample number 3 (produces a deveta phase of 25 microns).
A432 was produced. Various surface treatments were performed on the surface depending on the purpose. TiC was installed in a CVD reactor,
TiCl was heated to 1000°C while flowing H and gas.
42% CH, 44% CH, and the remainder H2 at a flow rate of 7
Supplied under the condition of 1/min pressure of 40 mmHg.
The reaction was carried out for 2 to 3 hours to form a TiC covering layer of 0.2 to 5 microns on the substrate. Similarly, in the case of TiN, change the gas system to 22% N. The reaction was carried out for 2 to 3 hours to form a TiN coating layer of 0.2 to 5 microns on the substrate. Table 1 shows the film quality and thickness of the materials produced.
第1表
結果 ◇;剥離によるもの
ロ:チヅビングを生じたもの
○;正常摩耗
そのチップの耐欠損性と、剥離性を確認するため、 フ
ライス工具での1枚方切削にて切削試験を実施した。Results in Table 1: ◇: Caused by peeling ○: Chizubing occurred ○: Normal wear In order to confirm the fracture resistance and peelability of the chip, a cutting test was conducted by cutting one piece with a milling tool.
ホルダー ダブルネガタイプ 1枚方
チップ SNMA432
被削材 SCM−440H345
切削速度 200 m / m i n送り 0.
3mm/刃
切り込み 約5mm
寿命判定 5分切削徨の損傷観察
切削後の損傷状態は、剥離によるもの、チッピングを生
じたもの、正常摩耗の3種類に分類できるが、その結果
を第3表に併記する。Holder Double negative type Single insert SNMA432 Work material SCM-440H345 Cutting speed 200 m/min Feed 0.
3mm/blade depth of cut: approx. 5mm Lifespan judgment Observation of damage after 5 minutes of cutting The state of damage after cutting can be classified into three types: peeling, chipping, and normal wear.The results are also listed in Table 3. do.
第3表より最内層TiNではある程度薄くても剥離を生
じたがTiC層の場合には剥離はなく正常な摩耗を示し
た。しかし、最内層TiCが厚くなるにしたがい脱炭層
の生成が多くなり耐チッピング性が劣化する傾向にある
。As shown in Table 3, peeling occurred in the innermost TiN layer even if it was thin to some extent, but in the case of the TiC layer, there was no peeling and normal wear was observed. However, as the innermost TiC layer becomes thicker, more decarburized layers are formed and the chipping resistance tends to deteriorate.
[実施例4コ
実施例1、試料番号5で用いたJIS M30相当の
超硬合金(脱ベータ相35ミクロンを生成)、でSNM
A432を製作した。その表面に目的に応じて様々な表
面処理を実施した。その層構造を第4表に示す。[Example 4] The cemented carbide equivalent to JIS M30 used in Example 1 and sample number 5 (produced a deveta phase of 35 microns) was used for SNM.
A432 was produced. Various surface treatments were performed on the surface depending on the purpose. The layer structure is shown in Table 4.
第4表
ネ:34の層構造はTiC−TiN−1,5μAl2O
,−2,0TiN−−1,5μ Al2O3”2.0μ
TiN切削試験の条件は構造用鋼丸棒の断続切削にて
実施した。断続切削では負荷が衝撃的に加わり、切削性
能上重要な耐チッピング性をN認した。Table 4: Layer structure of 34 is TiC-TiN-1, 5μAl2O
,-2,0TiN--1,5μ Al2O3”2.0μ
The conditions for the TiN cutting test were intermittent cutting of a structural steel round bar. In interrupted cutting, the load is applied shockingly, and chipping resistance, which is important for cutting performance, has been evaluated as N.
切削速度 200 m / m i n送り 0
. 2mm/rev
切込み 3.0mm
切削時間 2m1n
その結果、本発明のチップは皮膜の多層化に伴い、正常
な摩耗を示し、かつ、チッピングもなかった。さらに耐
摩耗性を比較する力め同様な切削条件で継続して行った
。切削時間10分では各チップとも大差ないが、30分
切削後の逃げ面過大摩耗量ではいずれも正常摩耗を示し
、多層化の効果が確認できた。Cutting speed 200 m/min feed 0
.. 2 mm/rev Depth of cut 3.0 mm Cutting time 2 m1n As a result, the tip of the present invention exhibited normal wear and no chipping due to the multilayered coating. Furthermore, the cutting process was continued under the same cutting conditions to compare wear resistance. At a cutting time of 10 minutes, there was no significant difference between the chips, but after 30 minutes of cutting, the excessive wear on the flank surface showed normal wear, confirming the effect of multilayering.
本発明の被覆超硬合金工具は脱ベータ層と皮膜最内層T
iCを特定することにより、基体中の強度アップと、脱
炭層の減少を達成し、刃先強度を増し、耐チッピング性
、耐摩耗性を向上させたものであり、被覆工具を断続分
野へより適用範囲を広げた工具である。The coated cemented carbide tool of the present invention has a deveta layer and an innermost coating layer T.
By specifying iC, we have achieved increased strength in the base and reduced decarburized layer, increased cutting edge strength, and improved chipping resistance and wear resistance, making coated tools more applicable to interrupted fields. It is a tool that has expanded its range.
Claims (6)
炭窒化物の1種以上と、Fe族、Cr族の1種以上より
なる超硬質合金を基体とし、該基体表面に5〜50ミク
ロンの脱ベータ相を生成し、その基体上に 1)最内層としてTiC0.2〜1ミクロン 2)第2層としでTiN1.0〜5ミクロン 3)第3層としてTiC、TiCNまたはAl_2O_
3の1種または2種以上5〜15ミクロン 4)最外層としてTiを1.0〜5ミクロン被覆したこ
とを特徴とする被覆超硬合金工具。1. Carbides and nitrides of groups 4a, 5a, and 6a of the periodic table,
A superhard alloy consisting of one or more carbonitrides and one or more of Fe group and Cr group is used as a base, a deveta phase of 5 to 50 microns is generated on the surface of the base, and 1) Inner layer: TiC 0.2-1 micron 2) Second layer: TiN 1.0-5 micron 3) Third layer: TiC, TiCN or Al_2O_
4) A coated cemented carbide tool characterized by being coated with Ti as an outermost layer with a thickness of 1.0 to 5 microns.
ータ相を生成するため、窒化物を含有させた事を特徴と
する硬質合金工具。2. A hard metal tool according to claim 1, characterized in that a nitride is contained in order to generate a deveta phase directly on the surface of the substrate.
ータ相を生成するため、TiNをN量に換算して0.0
5〜0.5%含有してなることを特徴とする超硬質合金
工具。3. In claim 2, in order to generate a deveta phase on the surface of the substrate, TiN is 0.0 in terms of N amount.
A cemented carbide tool characterized by containing 5 to 0.5%.
ータ相を生成するため、TaNをN量に換算して0.1
〜1.0%含有してなることを特徴とする超硬質合金工
具。4. In claim 2, in order to generate a deveta phase on the surface of the substrate, TaN is converted into an amount of N of 0.1
A superhard alloy tool characterized by containing ~1.0%.
ータ相は、基体の組成と比較して結合金属がほぼ近似し
ている事を特徴とする超硬質合金工具。5. 2. A cemented carbide tool according to claim 1, wherein the deveta phase on the surface of the base has a bond metal that is almost similar in composition to that of the base.
l_2O_3の複層から成る事を特徴とする超硬質合金
工具。6. In claim 1, the third layer coating is A.
A cemented carbide tool characterized by being composed of multiple layers of l_2O_3.
Priority Applications (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2108238A JP2657235B2 (en) | 1990-04-24 | 1990-04-24 | Coated super hard alloy tool |
Applications Claiming Priority (1)
Application Number | Priority Date | Filing Date | Title |
---|---|---|---|
JP2108238A JP2657235B2 (en) | 1990-04-24 | 1990-04-24 | Coated super hard alloy tool |
Publications (2)
Publication Number | Publication Date |
---|---|
JPH04135105A true JPH04135105A (en) | 1992-05-08 |
JP2657235B2 JP2657235B2 (en) | 1997-09-24 |
Family
ID=14479574
Family Applications (1)
Application Number | Title | Priority Date | Filing Date |
---|---|---|---|
JP2108238A Expired - Lifetime JP2657235B2 (en) | 1990-04-24 | 1990-04-24 | Coated super hard alloy tool |
Country Status (1)
Country | Link |
---|---|
JP (1) | JP2657235B2 (en) |
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US5499173A (en) * | 1993-09-30 | 1996-03-12 | Honda Giken Kogyo Kabushiki Kaisha | Head lamp device for motor vehicle |
Citations (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS55148762A (en) * | 1979-05-08 | 1980-11-19 | Mitsubishi Metal Corp | Surface-coated super hard alloy tool |
JPH0238559A (en) * | 1988-07-29 | 1990-02-07 | Mitsubishi Metal Corp | Cutting tool having excellent impact resistance made of surface coated tungsten carbide-base sintered hard alloy |
-
1990
- 1990-04-24 JP JP2108238A patent/JP2657235B2/en not_active Expired - Lifetime
Patent Citations (2)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
JPS55148762A (en) * | 1979-05-08 | 1980-11-19 | Mitsubishi Metal Corp | Surface-coated super hard alloy tool |
JPH0238559A (en) * | 1988-07-29 | 1990-02-07 | Mitsubishi Metal Corp | Cutting tool having excellent impact resistance made of surface coated tungsten carbide-base sintered hard alloy |
Cited By (1)
Publication number | Priority date | Publication date | Assignee | Title |
---|---|---|---|---|
US5499173A (en) * | 1993-09-30 | 1996-03-12 | Honda Giken Kogyo Kabushiki Kaisha | Head lamp device for motor vehicle |
Also Published As
Publication number | Publication date |
---|---|
JP2657235B2 (en) | 1997-09-24 |
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