JPS6119708B2 - - Google Patents
Info
- Publication number
- JPS6119708B2 JPS6119708B2 JP54061650A JP6165079A JPS6119708B2 JP S6119708 B2 JPS6119708 B2 JP S6119708B2 JP 54061650 A JP54061650 A JP 54061650A JP 6165079 A JP6165079 A JP 6165079A JP S6119708 B2 JPS6119708 B2 JP S6119708B2
- Authority
- JP
- Japan
- Prior art keywords
- cemented carbide
- weight
- free carbon
- base material
- carbide parts
- 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
Links
Classifications
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C30/00—Coating with metallic material characterised only by the composition of the metallic material, i.e. not characterised by the coating process
- C23C30/005—Coating with metallic material characterised only by the composition of the metallic material, i.e. not characterised by the coating process on hard metal substrates
Landscapes
- Chemical & Material Sciences (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Other Surface Treatments For Metallic Materials (AREA)
- Cutting Tools, Boring Holders, And Turrets (AREA)
- Powder Metallurgy (AREA)
- Chemical Vapour Deposition (AREA)
Description
【発明の詳細な説明】
WCを主成分とし、主として鉄族元素で結合し
てなるいわゆる超硬合金部品を基材とし、その表
面に、TiC等の耐摩耗性のある物質よりなる薄膜
を被覆した被覆超硬合金部品は基材の強靭性と、
表面の耐摩耗性とを兼ね備えており、従来の超硬
合金部品より一段とすぐれた切削工具材料として
広く用いられている。
この表面被覆工具材（以下コーテイングチツプ
と略称する。）の性能は、被覆物質と基材たる超
硬合金部品との接着性、基材たる超硬合金部品表
面付近の特性、および超硬合金部品そのものの性
質などによることが知られており、種々の検討お
よび提案がなされている。
本発明は被覆物質と基材たる超硬合金部品との
接着性の向上した工具基材用被覆超硬合金部品の
提供を目的とするものである。
本発明者の一人（以下一部発明者と略称す
る。）は、被覆物質と基材たる超硬合金部品との
接着性に関し、種々検討を行い、
被覆物質のうち基材と接する最内層被覆物質
はTi、Zr、Hf、Ｖ、Nb、Ta、Cr、Mo、Ｗの
一種もしくはそれ以上の炭化物および／または
炭窒化物であること、
基材たる超硬合金部品は0.01〜0.5重量％の
遊離炭素を含有すること。
の二点が必須であるという知見を得ている。
しかしながら、かかる遊離炭素を安定させて該
超硬合金部品に含有せしめることは超硬合金部品
製造業者にとつて非常に困難なことであつた。
これは通常このような超硬合金部品はWC、
（Ti、Nb、Ta、Ｗ）ＣおよびCoの夫々の微粉末
を粉砕、混合して作成した原料粉を型押し成型し
てなる型押し体を真空または還元雰囲気等で焼結
するいわゆる粉末治金法によつて製造されている
が、原料粉末は非常に微少なため、その製造ロツ
トによつて該原料粉末の酸化度が著しく異なるこ
と、そして該原料粉末を型押し成型して型押し体
を焼結する際に該原料粉末の酸化度に応じて原料
粉末中のＣが消費され最終的には超硬合金部品の
含有遊離炭素が著しく異なるということは当該業
界の常識とされていた。
従つて、このような遊離炭素を一定量含有せし
めた超硬合金部品を製造するには非常に精密かつ
厳格な工程管理を必要とし、それでも現実にはあ
まり歩留りのよいものではなかつた。
一方、一部発明者は長らくTi、Zr、Hf、Ｖ、
Nb、Ta、Cr、Mo、Ｗの一種もしくはそれ以上
のフエーズセンターキユービツク炭化物および／
または炭窒化物（いわゆるＢ−１型固溶体）を硬
質相とする超硬合金部品の焼結安定性につき種々
詳細に検討を行い、その結果、例えば（Ti、
Ｗ）（Ｃ、Ｎ）を例にして説明すると、（他のZr、
Hf、Ｖ、Nb、Ta、Cr、Mo遷移金属元素でも同
じ）（Ｔ、Ｗ）（Ｃ、Ｎ）炭窒化物を硬質相とする
超硬合金部品を焼結する際その焼結雰囲気中の窒
素分圧が該（Ti、Ｗ）（Ｃ、Ｎ）の平衡窒素分圧
よりも高いと、（Ti、Ｗ）（Ｃ、Ｎ）のＣがＮで
置換されると共にＣが遊離炭素としてはき出され
るとの知見を得た。
そこでこの知見をコーテイングチツプ基材用超
硬合金部品の製造に応用するならば、いかに超硬
合金部品の製造ロツトが異なつていても焼結段階
において焼結雰囲気の窒素分圧を適当に調整する
ことによつて該超硬合金部品中のＢ−１型固溶体
よりＣが適宜はき出され最終超硬合金部品中の遊
離炭素の量を如何ようにも調整しうるのではない
かと考えた。この考え方に基いて各種コーテイン
グチツプ基材用超硬合金部品を試作したところ何
れも良好な遊離炭素含有量を示し、本発明の有効
性が実証された。
なお本発明においては窒素がＢ−１型固溶体に
働きかけることによつて遊離炭素を析出せしめる
のであるから自ら窒素等の超硬合金部品中での含
有量にも制約があつて、その量は0.01〜1.0重量
％である。これは0.01重量％以下では効果が認め
がたく、また1.0重量％以上では強度の低下を来
たすためである。
また遊離炭素量は0.01重量％以下では効果がな
く0.5重量％以上ではコーテイングチツプ基材と
して性能劣化が著しいため0.01〜0.5重量％特に
0.02〜0.1重量％が好ましい。
また本発明はＢ−１型固溶体の焼結安定性を利
用しているのであるからTi、Zr、Hf、Ｖ、Nb、
Ta、Cr、Mo、Ｗの一種もしくはそれ以上の遷移
金属元素の炭窒化物（いわゆるＢ−１型固溶体）
の使用は不可欠である。コーテイングチツプの基
材としては強度面からはＢ−１型固溶体以外に
Cr、Mo、Ｗの一種もしくはそれ以上からなるヘ
キサゴナルモノカーバイドも不可欠であり、これ
等硬質相を結合するにはCr、Mo、Ｗ、Fe、Co、
Niの一種もしくはそれ以上の遷移金属元素が好
ましい。
次に本発明の被覆工具基材用超硬合金部品の製
造法についてのべると、本発明は原料であるＢ−
１型固溶体の平衡窒素分圧と焼結雰囲気の窒素分
圧において後者が大なる場合、該Ｂ−１型固溶体
が分解し、Ｃをはき出すという考えに基くので焼
結雰囲気の窒素分圧が1Torr以下では効果が認め
難くまた1000Torr以上では焼結完了後の該超硬
合金部品中の含有炭素量が0.5重量％をこえ、か
つ通常当該超硬合金部品の製造業界において超硬
合金部品を焼結する冷壁抵抗加熱型真空炉におい
て窒素による熱伝導のため炉壁が高温となり、経
済上や安全上好ましくない。
従つて本発明の効果を一層有効にするには該超
硬合金部品の原料に用いるＢ−１型固溶体のうち
少くとも一種以上は窒素を含有する炭窒化物であ
つて、かつ該炭窒化物中のＣとＮの比率が原子比
率でＣとＮの合金量に対し窒素が0.01〜0.5が好
ましい。以下本発明を実施例によつて説明する。
実施例 １
WC84.5重量％（Ti、Nb、Ta、Ｗ）（CN）10.0
％（Ｎ／Ｃ＋Ｎ＝0.31）Co5.5重量％を秤取し、
ボールミルにてアセトンを溶媒として粉砕混合し
た。得られたスラリーにパラフインを１重量％添
加し、乾燥、造粒を行つた。得られた原料粉末を
型番SNU432の金型にて型押し成型を行つた。得
られた試料をＡとし、このＡをさらに湿度90％温
度30℃の恒湿恒温槽にて１週間放置したものをＢ
としてこれらを通常の方法で真空焼結したところ
Ａからは0.03重量％の遊離炭素が検出されたが、
Ｂからは全く検出されなかつた。このＢの試料を
用いて次いで600〜1325℃まで窒素分圧300Torr
にて加熱したのち焼結温度まで真空に保ち、その
雰囲気中で１時間焼結したところ得られた試料Ｂ
−１からは0.04重量％の遊離炭素が検出された。
上記のＡ、Ｂ、Ｂ−１の試料について夫々化学
蒸着法にてTiCを６μ被覆したのち、
被削材 S45C鍛造材
（50mmφ×300mm）
切削速度 100m/min
送 り 0.50mm/rev
切り込み １〜８mm
の切削条件で切削テストを行つたところＡチツプ
は19本、Ｂ−１チツプは21本切削出来たのにＢチ
ツプは被覆TiC層が剥離してしまい４本しか切削
出来なかつた。
実施例 ２
実施例１を全く同様の組成、工程にて作成した
型番SNU432の型押し体を室内大気中にて１ケ月
放置した。これを通常の真空焼結法にて焼結した
ものをＣ−１とし、600〜1325℃まで窒素分圧
150Torrにて加熱したのち焼結完了まで真空乾燥
したものをＣ−２とした。Ｃ−２からは0.06重量
％の遊離炭素が析出していたのに対し、Ｃ−１で
は全く認められなかつた。
次いでこのＣ−１、Ｃ−２のチツプ夫々に化学
蒸着法にてTiCを６μ、Ti（BN）0.5μ、Al2O3
を1.5μと順次被覆し、
被削材 FC30
切削速度 150m/min
送 り 0.71mm/rev
切り込み ２mm
切削油 使用せず
の条件で切削テストを行つたところＣ−２のチツ
プでは34分間も切削可能であつたがＣ−１のチツ
プは被覆膜剥離のため19分間しか切削できなかつ
た。
実施例 ３
WC84.5重量％、（Ti、Nb、Ta、Ｗ）C10重量
％（Ｎ／Ｃ＋Ｎ＜0.01）、Co5.5重量％を秤取し、
実施例１と同様の工程にて作成したSNU432の型
押し体をＤ、WC84.5重量％、（Ti、Nb、Ta、
Ｗ）（Ｃ、Ｎ）10重量％（Ｎ／Ｃ＋Ｎ＝0.53）
Co5.5重量％を秤取し、実施例１と同様の工程に
て作成した型押し体をＥとし、このＤ、Ｅいずれ
も湿度90％、30℃の恒湿恒温槽にて１週間放置し
た。
その後、このＤ、Ｅおよび実施例１のＢの三者
を第１表の条件にて焼結しその後の遊離炭素量お
よび含有窒素量の分析を行つたところ第１表の結
果を得た。
【表】[Detailed description of the invention] The base material is a so-called cemented carbide component made of WC as a main component and mainly bonded with iron group elements, and its surface is coated with a thin film made of a wear-resistant material such as TiC. coated cemented carbide parts have the toughness of the base material,
It has excellent surface wear resistance and is widely used as a cutting tool material that is superior to conventional cemented carbide parts. The performance of this surface-coated tool material (hereinafter referred to as coating chip) is determined by the adhesion between the coating material and the cemented carbide component that is the base material, the characteristics near the surface of the cemented carbide component that is the base material, and the properties of the cemented carbide component that is the base material. It is known that this depends on the properties of the material itself, and various studies and proposals have been made. An object of the present invention is to provide a coated cemented carbide component for a tool base material, which has improved adhesion between the coating material and the cemented carbide component as a base material. One of the inventors of the present invention (hereinafter partially referred to as the inventor) conducted various studies regarding the adhesion between the coating material and the cemented carbide component that is the base material, and developed the innermost layer of the coating material that is in contact with the base material. The substance is a carbide and/or carbonitride of one or more of Ti, Zr, Hf, V, Nb, Ta, Cr, Mo, and W. The cemented carbide component as the base material contains 0.01 to 0.5% by weight. Contains free carbon. We have obtained the knowledge that these two points are essential. However, it has been very difficult for manufacturers of cemented carbide parts to stably incorporate such free carbon into the cemented carbide parts. This usually includes cemented carbide parts such as WC,
(Ti, Nb, Ta, W) C and Co fine powders are pulverized and mixed, and raw material powder is pressed and molded into a molded body, which is then sintered in a vacuum or in a reducing atmosphere. Although it is manufactured by the metal method, since the raw material powder is very small, the degree of oxidation of the raw material powder varies significantly depending on the production lot, and the raw material powder is pressed and molded to make an embossed body. It is common knowledge in the industry that C in the raw material powder is consumed depending on the degree of oxidation of the raw material powder when sintering the raw material powder, and that the free carbon content of the cemented carbide component ultimately differs significantly. Therefore, manufacturing such cemented carbide parts containing a certain amount of free carbon requires very precise and strict process control, and even then, in reality, the yield is not very good. On the other hand, some inventors have long been working on Ti, Zr, Hf, V,
One or more phase center cubic carbides of Nb, Ta, Cr, Mo, W and/or
In addition, we conducted various detailed studies on the sintering stability of cemented carbide parts containing carbonitrides (so-called B-1 type solid solution) as the hard phase, and as a result, we found that, for example, (Ti,
W) (C, N) as an example, (other Zr,
The same applies to Hf, V, Nb, Ta, Cr, Mo transition metal elements) (T, W) (C, N) When sintering cemented carbide parts with carbonitride as a hard phase, When the nitrogen partial pressure is higher than the equilibrium nitrogen partial pressure of (Ti, W) (C, N), C in (Ti, W) (C, N) is replaced with N and C is expelled as free carbon. We have obtained the knowledge that this is possible. Therefore, if this knowledge is applied to the production of cemented carbide parts for coating chip substrates, it is possible to appropriately adjust the nitrogen partial pressure in the sintering atmosphere during the sintering stage, no matter how different the production lots of cemented carbide parts are. It was thought that by doing so, carbon could be appropriately expelled from the B-1 type solid solution in the cemented carbide part, and the amount of free carbon in the final cemented carbide part could be adjusted in any way. Based on this idea, various cemented carbide parts for coating chip substrates were prototyped, and all showed good free carbon content, demonstrating the effectiveness of the present invention. In addition, in the present invention, since nitrogen precipitates free carbon by acting on the B-1 type solid solution, there is a restriction on the content of nitrogen etc. in the cemented carbide parts, and the amount is 0.01 ~1.0% by weight. This is because if it is less than 0.01% by weight, the effect is hard to recognize, and if it is more than 1.0% by weight, the strength will decrease. In addition, if the amount of free carbon is less than 0.01% by weight, it will not be effective, and if it is more than 0.5%, the performance as a coating chip base material will deteriorate significantly.
0.02-0.1% by weight is preferred. Furthermore, since the present invention utilizes the sintering stability of the B-1 type solid solution, Ti, Zr, Hf, V, Nb,
Carbonitride of one or more transition metal elements such as Ta, Cr, Mo, and W (so-called B-1 type solid solution)
The use of is essential. In terms of strength, as a base material for coating chips, other than B-1 type solid solution is recommended.
Hexagonal monocarbide consisting of one or more of Cr, Mo, and W is also essential, and to bond these hard phases, Cr, Mo, W, Fe, Co,
One or more transition metal elements such as Ni are preferred. Next, referring to the manufacturing method of the cemented carbide parts for coated tool base materials of the present invention, the present invention uses B-
This is based on the idea that if the latter is large between the equilibrium nitrogen partial pressure of the type 1 solid solution and the nitrogen partial pressure of the sintering atmosphere, the type B-1 solid solution will decompose and release C, so the nitrogen partial pressure of the sintering atmosphere will be 1 Torr. Below 100 Torr, the carbon content in the cemented carbide parts exceeds 0.5% by weight after sintering is completed, and the cemented carbide parts are usually sintered in the manufacturing industry of the cemented carbide parts. In cold wall resistance heating type vacuum furnaces, the furnace walls become hot due to heat conduction by nitrogen, which is unfavorable from an economic and safety standpoint. Therefore, in order to make the effects of the present invention even more effective, at least one type of B-1 type solid solution used as a raw material for the cemented carbide parts is a carbonitride containing nitrogen, and The ratio of C and N in the alloy is preferably 0.01 to 0.5 relative to the alloy amount of C and N. The present invention will be explained below with reference to Examples. Example 1 WC84.5% by weight (Ti, Nb, Ta, W) (CN) 10.0
%(N/C+N=0.31)Co5.5% by weight was weighed out,
The mixture was ground and mixed in a ball mill using acetone as a solvent. 1% by weight of paraffin was added to the obtained slurry, followed by drying and granulation. The obtained raw material powder was pressed and molded using a mold with model number SNU432. The obtained sample was designated as A, and this A was further left in a constant humidity and temperature chamber at 90% humidity and 30°C for one week, and B was obtained.
When these were vacuum sintered using the usual method, 0.03% by weight of free carbon was detected in A.
It was not detected at all from B. Using this sample B, the temperature was then increased to 600 to 1325℃ under a nitrogen partial pressure of 300 Torr.
Sample B, which was obtained by heating the sample at
-1, 0.04% by weight of free carbon was detected. After coating the above samples A, B, and B-1 with 6μ of TiC using chemical vapor deposition, workpiece material: S45C forged material (50mmφ×300mm) Cutting speed: 100m/min Feed: 0.50mm/rev Depth of cut: 1~ When a cutting test was conducted under cutting conditions of 8 mm, 19 chips could be cut with the A chip and 21 chips with the B-1 chip, but only 4 chips could be cut with the B chip due to peeling of the TiC layer. Example 2 An embossed body with model number SNU432 prepared using exactly the same composition and process as in Example 1 was left in the indoor atmosphere for one month. This is sintered using the normal vacuum sintering method and is called C-1, with a nitrogen partial pressure of 600 to 1325℃.
C-2 was obtained by heating at 150 Torr and then vacuum drying until sintering was completed. While 0.06% by weight of free carbon was precipitated from C-2, no free carbon was observed at all from C-1. Next, 6μ of TiC, 0.5μ of Ti(BN), and Al 2 O 3 were applied to each of the C-1 and C-2 chips by chemical vapor deposition.
A cutting test was conducted under the following conditions: work material: FC30, cutting speed: 150 m/min, feed: 0.71 mm/rev, depth of cut: 2 mm, and no cutting oil was used. The C-2 chip could cut for 34 minutes. However, the C-1 chip could only be cut for 19 minutes due to peeling of the coating. Example 3 WC84.5% by weight, (Ti, Nb, Ta, W)C10% by weight (N/C+N<0.01), Co5.5% by weight were weighed out,
D, WC84.5% by weight, (Ti, Nb, Ta,
W) (C, N) 10% by weight (N/C+N=0.53)
5.5% by weight of Co was weighed out and the embossed body was created in the same process as in Example 1, and this was designated as E. Both D and E were left in a constant humidity and temperature chamber at 90% humidity and 30°C for one week. did. Thereafter, these three materials D, E, and B of Example 1 were sintered under the conditions shown in Table 1, and the amounts of free carbon and nitrogen content were analyzed, and the results shown in Table 1 were obtained. 【table】
Claims (1)
るヘキサゴナルモノカーバイド粉末とTi、Zr、
Hf、Ｖ、Nb、Ta、Cr、Mo、Ｗの一種もしくは
それ以上の遷移金属元素の一種もしくはそれ以上
のフエーズセンターキユービツクな炭化物およ
び／または炭窒化物（いわゆるＢ−１型固溶体）
のうち少なくとも一種以上がＮを含有する炭窒化
物であつて、該炭窒化物中のＣとＮの比率が原子
比率でＣとＮとの合量に対し、Ｎが0.01〜0.5で
ある粉末とCr、Mo、Ｗ、Fe、Co、Niの一種以上
を焼結雰囲気の一部または全部が１〜1000Torr
N2分圧をもつ雰囲気で焼結することによつて作
成した超硬合金部品の表面にTi、Zr、Hf、Ｖ、
Nb、Ta、Cr、Mo、Ｗの一種もしくはそれ以上
の遷移金属元素とＢ、Ｎ、Ｏ、Ｃの一種もしくは
それ以上の非金属元素の化合物および／または
Al2O3或いはZrO2からなる酸化物を一層もしくは
積層被覆した被覆工具材基材用超硬合金部品にお
いて、該超硬合金部品内組成分として0.01〜1.0
重量％の窒素、0.01〜0.5重量％の遊離炭素を含
有することを特徴とする表面被覆工具材基材用超
硬合金部品。1 Hexagonal monocarbide powder consisting of one or more of Cr, Mo, and W; Ti, Zr,
Phase-center cubic carbides and/or carbonitrides (so-called B-1 type solid solutions) of one or more transition metal elements such as Hf, V, Nb, Ta, Cr, Mo, and W.
A powder in which at least one of these is a carbonitride containing N, and the ratio of C and N in the carbonitride is 0.01 to 0.5 with respect to the total amount of C and N in terms of atomic ratio. and one or more of Cr, Mo, W, Fe, Co, and Ni. Part or all of the atmosphere is 1 to 1000 Torr.
Ti, Zr , Hf, V,
A compound of one or more transition metal elements such as Nb, Ta, Cr, Mo, and W and one or more nonmetallic elements such as B, N, O, and C; and/or
In cemented carbide parts for coated tool base materials coated with an oxide consisting of Al 2 O 3 or ZrO 2 in a single layer or in layers, the composition within the cemented carbide parts is 0.01 to 1.0.
A cemented carbide component for a surface-coated tool base material, characterized in that it contains % by weight of nitrogen and 0.01-0.5% by weight of free carbon.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP6165079A JPS55154562A (en) | 1979-05-18 | 1979-05-18 | Sintered hard alloy part for base material of surface-covered tool material and their manufacture |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP6165079A JPS55154562A (en) | 1979-05-18 | 1979-05-18 | Sintered hard alloy part for base material of surface-covered tool material and their manufacture |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS55154562A JPS55154562A (en) | 1980-12-02 |
| JPS6119708B2 true JPS6119708B2 (en) | 1986-05-19 |
Family
ID=13177306
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP6165079A Granted JPS55154562A (en) | 1979-05-18 | 1979-05-18 | Sintered hard alloy part for base material of surface-covered tool material and their manufacture |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS55154562A (en) |
Families Citing this family (12)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5867860A (en) * | 1981-10-19 | 1983-04-22 | Hitachi Metals Ltd | Coated sintered hard alloy and preparation thereof |
| JPS5867859A (en) * | 1981-10-19 | 1983-04-22 | Hitachi Metals Ltd | Coated sintered hard alloy and preparation thereof |
| JPS5873763A (en) * | 1981-10-29 | 1983-05-04 | Hitachi Metals Ltd | Coated sinteredhard alloy and its production thereof |
| JPS58126974A (en) * | 1981-12-16 | 1983-07-28 | カーボロイ インコーポレーテッド | Coated product and manufacture |
| AT377786B (en) * | 1981-12-24 | 1985-04-25 | Plansee Metallwerk | WEARING PART, IN PARTICULAR CARBIDE CUTTING INSERT FOR CHIP-REMOVING |
| WO1984004110A1 (en) * | 1983-04-18 | 1984-10-25 | Battelle Development Corp | HARD LAYER FORMED BY INCORPORATING NITROGEN INTO Mo OU W METAL AND METHOD FOR OBTAINING THIS LAYER |
| DE3332260A1 (en) * | 1983-09-07 | 1985-03-28 | Fried. Krupp Gmbh, 4300 Essen | COATED CARBIDE BODY |
| US4619865A (en) * | 1984-07-02 | 1986-10-28 | Energy Conversion Devices, Inc. | Multilayer coating and method |
| JPS61223180A (en) * | 1985-03-29 | 1986-10-03 | Mitsubishi Metal Corp | Cutting tool made of surface-coated tungsten carbide sintered hard alloy |
| JPS61223182A (en) * | 1985-03-29 | 1986-10-03 | Mitsubishi Metal Corp | Cutting tool made of surface-coated tungsten carbide sintered hard alloy |
| JPS61223181A (en) * | 1985-03-29 | 1986-10-03 | Mitsubishi Metal Corp | Cutting tool made of surface-coated tungsten carbide sintered hard alloy |
| CA1319497C (en) * | 1988-04-12 | 1993-06-29 | Minoru Nakano | Surface-coated cemented carbide and a process for the production of the same |
Family Cites Families (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| GB763409A (en) * | 1953-10-21 | 1956-12-12 | Uddeholms Ab | Hard metal alloy and method for producing the same |
| US4049876A (en) * | 1974-10-18 | 1977-09-20 | Sumitomo Electric Industries, Ltd. | Cemented carbonitride alloys |
| JPS5213201A (en) * | 1975-07-18 | 1977-02-01 | Nissan Motor Co Ltd | Automatic operation apparatus in chassis dynamo-meter |
-
1979
- 1979-05-18 JP JP6165079A patent/JPS55154562A/en active Granted
Also Published As
| Publication number | Publication date |
|---|---|
| JPS55154562A (en) | 1980-12-02 |
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