JP2660180B2 - Coated carbide tool - Google Patents
Coated carbide toolInfo
- Publication number
- JP2660180B2 JP2660180B2 JP3163993A JP16399391A JP2660180B2 JP 2660180 B2 JP2660180 B2 JP 2660180B2 JP 3163993 A JP3163993 A JP 3163993A JP 16399391 A JP16399391 A JP 16399391A JP 2660180 B2 JP2660180 B2 JP 2660180B2
- Authority
- JP
- Japan
- Prior art keywords
- layer
- thickness
- tin
- coated
- coating
- 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
Landscapes
- Other Surface Treatments For Metallic Materials (AREA)
- Cutting Tools, Boring Holders, And Turrets (AREA)
- Chemical Vapour Deposition (AREA)
Description
【０００１】[0001]
【産業上の利用分野】本発明は耐摩耗性に優れた切削用
及び耐摩耗用の被覆超硬質合金工具に関するものであ
る。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention relates to a cutting and wear-resistant coated super-hard alloy tool having excellent wear resistance.
【０００２】[0002]
【従来の技術】従来、超硬合金を基体とし、その表面に
耐摩耗性に富んだＴｉＣ、ＴｉＮなどの硬質皮膜を被覆
した被覆超硬合金工具は、表面の耐摩耗性と基体の強靭
性を兼ね備えており、広く実用に供されている。しか
し、ＴｉＣ、ＴｉＮ被覆の合金はすくい面上のクレータ
ー摩耗が著しく、工具寿命が短くなるなどの欠点があっ
た。このため、上記欠点を除く手段として、種々の皮膜
を形成する方法が提案されているが、いずれも問題点を
有し、かならずしも満足出来るものは実現されていな
い。例えば、 ＴｉＣ、ＴｉＮのかわりにＡｌ2Ｏ3単
層を被覆する方法−特開昭５４−１５８７８０号等、
ＴｉＣ、ＴｉＮのかわりにＴｉＢ2 単層を被覆する方
法−特開昭５４−７４８１６号等、 ＴｉＣ、ＴｉＮ
の表面に更にＡｌ2Ｏ3を被覆し、２層構造の皮膜とする
方法（２層）−特開昭５５−１１９１６５号等、 Ｔ
ｉＢ2の表面にＡｌ2Ｏ3を被覆し、２層構造皮膜を形成
する方法−特開昭５５−８４８５号等、が示されてい
る。2. Description of the Related Art Conventionally, a coated cemented carbide tool in which a cemented carbide is used as a base and its surface is coated with a hard coating such as TiC or TiN which is rich in abrasion resistance is provided by abrasion resistance of the surface and toughness of the base. It is widely used for practical use. However, alloys coated with TiC and TiN have drawbacks such as significant crater wear on the rake face and shortened tool life. For this reason, methods for forming various coatings have been proposed as means for eliminating the above-mentioned drawbacks, but all of them have problems, and none of them has always been satisfactory. For example, a method of coating a single layer of Al 2 O 3 instead of TiC or TiN-Japanese Patent Application Laid-Open No. 54-158780,
TiC, a method for coating a TiB 2 monolayers in place of TiN - JP 54-74816, etc., TiC, TiN
A method of forming a two-layered film by further coating Al 2 O 3 on the surface of the film (two layers)-JP-A-55-119165, T
coated with Al 2 O 3 on the surface of iB 2, a method of forming a two-layer structure film - like 55-8485 JP, are the shown.
【０００３】の方法では、超硬質基体とＴｉＢ2の親
和性が弱いこと、及び被削材の鉄と２硼化物とが反応
し、クレーター摩耗を生じやすいことなどの欠点を有し
ている。 の方法は、超硬質基体とＡｌ2Ｏ3間の親和性が弱く、
基体と皮膜の結合力は十分でないという欠点を有してい
る。 の方法によるＴｉＣ−Ａｌ2Ｏ3被覆された品物は上記
及びに比較し、より好ましい特性をもつため広く実
用に供されているが、Ａｌ2Ｏ3とＴｉＣ又はＴｉＮ間の
親和性が弱く、その結合力は改善の余地がある。 の方法は、上記の方法と同様、密着強度が不十分で
あるが、被削材との反応をＡｌ2Ｏ3層によって防止して
いるため、耐クレーター性は良好である。[0003] The method described above has disadvantages such as that the affinity between the super-hard substrate and TiB 2 is weak, and that iron and diboride of the work material react with each other and crater wear easily occurs. Is weak in affinity between the super-hard substrate and Al 2 O 3 ,
It has the disadvantage that the bonding strength between the substrate and the coating is not sufficient. The article coated with TiC-Al 2 O 3 by the method of the above is widely used for practical purposes because it has more preferable characteristics as compared with the above, but the affinity between Al 2 O 3 and TiC or TiN is weak, Its bonding strength can be improved. This method has insufficient adhesion strength as in the above method, but has good crater resistance because the reaction with the work material is prevented by the Al 2 O 3 layer.
【０００４】そのため、上記単層皮膜及び２層構造皮膜
の特長を維持しながら、その欠点を解消するために、例
えばＴｉＣ、ＴｉＮの表面に中間層としてＴｉ（Ｃ、
Ｎ）、Ｔｉ（Ｃ、Ｏ）、Ｔｉ（Ｃ、Ｎ、Ｏ）を被覆し、
その上に外層としてＡｌ2Ｏ3を被覆し３層構造の皮膜を
形成する方法（特開昭５５−１４８７６４号等）が提案
されている。[0004] Therefore, in order to eliminate the drawbacks while maintaining the features of the single-layer coating and the two-layer coating, for example, Ti (C,
N), Ti (C, O), Ti (C, N, O),
A method of forming a three-layered film by coating Al 2 O 3 as an outer layer thereon (Japanese Patent Application Laid-Open No. 55-148768) has been proposed.
【０００５】[0005]
【発明が解決しようとする課題】この方法は上記の方
法の欠点を改善するために、内層のＴｉＣ層と中間層の
被覆方法を変えることにより形成したものであり、その
両者の特徴を最大限に生かそうとするものである。さら
に、切削加工工具に要求されるより一層の長寿命化（耐
摩耗性の向上）を計ったものである。本発明は上記実情
に鑑み成されたものであり上記従来技術の欠点を改良
し、皮膜各層間−特に内層と中間層の粒度に着目し、特
に耐摩耗性に優れる被覆超硬合金を提供することを目的
とするもので有る。This method is formed by changing the coating method of the inner TiC layer and the intermediate layer in order to improve the drawbacks of the above-mentioned method. To make the most of it. Further, the life of the cutting tool is further extended (the wear resistance is improved). SUMMARY OF THE INVENTION The present invention has been made in view of the above circumstances, improves the above-mentioned disadvantages of the prior art, and provides a coated cemented carbide that is particularly excellent in wear resistance, focusing on the particle size of each layer of the coating-particularly the inner layer and the intermediate layer. It is intended for that purpose.
【０００６】[0006]
【課題を解決するための手段】本発明は超硬質合金基体
の表面に、内層として、まず第１層にＴｉＮを被覆し、
第２層にＴｉＣＮを柱状に成膜し、かつ、中間層、すな
わち第３層としてＴｉの炭化物、窒化物、炭窒化物の１
種又は２種以上を設け、外層、すなわち第４層としてＡ
ｌ2Ｏ3層又はＴｉＮ層の１種又は２種以上を設け、第３
層の粒子は第２層の影響により粗粒化しやすいため、第
２層を柱状にし粒度を細かくすることによって、第２層
の厚膜化と、それより外側の層の耐摩耗性を兼ね備えた
構成としたものである。According to the present invention, a first layer is first coated with TiN as an inner layer on the surface of a super-hard alloy substrate.
A TiCN film is formed in a columnar shape on the second layer, and one of Ti carbide, nitride and carbonitride is formed as an intermediate layer, that is, as a third layer.
A seed or two or more kinds are provided, and A is used as an outer layer, that is, a fourth layer.
One or more of an l 2 O 3 layer or a TiN layer is provided, and a third
Since the particles of the layer are easily coarsened by the influence of the second layer, the second layer has a columnar shape and a small particle size, so that both the thickness of the second layer and the wear resistance of the outer layer are provided. It is configured.
【０００７】本発明における基体としての超硬質合金
は、周期率表の４ａ、５ａ、６ａ族の炭化物、窒化物、
炭窒化物のうちの一種以上と、Ｆｅ、Ｎｉ、Ｃｏ、Ｗ、
Ｍｏ、Ｃｒのうちの一種以上とよりなる超硬質合金が適
用される。また、本発明における各被覆層を形成するこ
とは、既知の成膜法を応用することによって可能であ
り、例えば内層を構成するＴｉＣＮまたはＴｉＮ皮膜に
ついては、 ＴｉＣｌ4＋（ＣＨ3）ＣＮ＋２Ｈ2→ＴｉＣＮ＋ＨＣｌ ＴｉＣｌ4＋２Ｈ2 →Ｔｉ＋４ＨＣｌ ＣＨ4 →Ｃ＋２Ｈ2 Ｔｉ＋Ｃ →ＴｉＣ あるいは、 ＴｉＣｌ4＋２Ｈ2 →Ｔｉ＋４ＨＣｌ Ｔｉ＋１／２Ｎ2 →ＴｉＮ のように、Ｔｉのハロゲン化物を気化し、還元及び炭化
あるいは窒化反応によって得ることができる。[0007] The super-hard alloy as a substrate in the present invention includes carbides, nitrides of groups 4a, 5a and 6a of the periodic table.
One or more of carbonitrides, Fe, Ni, Co, W,
A super-hard alloy consisting of one or more of Mo and Cr is applied. The formation of each coating layer in the present invention is possible by applying a known film forming method. For example, for the TiCN or TiN film constituting the inner layer, TiCl 4 + (CH 3 ) CN + 2H 2 → TiCN + HCl TiCl 4 + 2H 2 → Ti + 4HCH 4 → CH 4 → C + 2H 2 Ti + C → TiC or TiCl 4 + 2H 2 → Ti + 4HCl Ti + 1 / 2N 2 → TiN Vaporization of Ti halide and reduction and carbonization or nitriding to obtain it Can be.
【０００８】次に、内層の厚さを２．０〜１０μｍ、中
間層の厚さを０．１〜５μｍ、外層の厚さを０．５〜１
０μｍとすることが望ましい。その理由は以下の通りで
ある。 （１）内層のＴｉＮ、ＴｉＣＮのうちのいずれか一種か
らなる内層の厚さが２．０μｍ未満では柱状晶の生成が
十分でなく、また１０μｍを超えるとＴｉＣＮ等の層は
本質的に脆く欠損しやすくなるため、内層の厚さは２．
０〜１０μｍとするのが望ましい。Next, the thickness of the inner layer is 2.0 to 10 μm, the thickness of the intermediate layer is 0.1 to 5 μm, and the thickness of the outer layer is 0.5 to 1 μm.
Desirably, it is 0 μm. The reason is as follows. (1) If the thickness of the inner layer made of any one of TiN and TiCN is less than 2.0 μm, columnar crystals are not sufficiently generated, and if it exceeds 10 μm, the layer such as TiCN is essentially brittle and defective. The inner layer has a thickness of 2.
Desirably, the thickness is 0 to 10 μm.
【０００９】（２）中間層のＴｉの炭化物、窒化物、炭
窒化物の１種以上から構成される中間層の厚さが０．１
μｍ未満では粒度を調整するのに不十分であり、また５
μｍを超えると全体の厚さが厚くなり脆く成るため、欠
損しやすくなる。このため中間層の厚さは０．１〜５μ
ｍとするのが望ましい。また、この層の構造はＴｉの炭
化物、窒化物、炭窒化物を組み合わせた方が特性を効果
的に発揮できるため、２層以上とするのが望ましい。 （３）外層のＡｌ2Ｏ3層及び／又はＴｉＮ層は、０．５
μｍ未満では中間層の欠点である被削材との反応を防止
できず、また、５μｍを越えるとＡｌ2Ｏ3層は本質的に
脆いため、欠損しやすくなるため０．５〜５μｍとする
のが良い。(2) The thickness of the intermediate layer composed of at least one of Ti carbide, nitride and carbonitride is 0.1
If it is less than μm, it is insufficient to adjust the particle size.
If it exceeds μm, the entire thickness becomes thick and brittle, so that it is easily broken. Therefore, the thickness of the intermediate layer is 0.1 to 5 μm.
m is desirable. In addition, the structure of this layer is desirably two or more layers because the characteristics can be more effectively exhibited by combining Ti carbide, nitride, and carbonitride. (3) The outer Al 2 O 3 layer and / or TiN layer is 0.5
If the thickness is less than μm, the reaction with the work material, which is a defect of the intermediate layer, cannot be prevented. If the thickness exceeds 5 μm, the Al 2 O 3 layer is inherently brittle and easily breaks. Is good.
【００１０】[0010]
【実施例】次に本発明による被覆超硬質合金を実施例に
よって具体的に説明する。但し、本発明はこれら実施例
の範囲に限定されるものでないことは言うまでもない。
超硬質体の基体としてＷＣ７２％、８％ＴｉＣ、（Ｔａ
Ｎｂ）Ｃ１１％、Ｃｏ９％（重量％）なる組成に粉末を
配合し、真空中１４００℃で一時間焼結し、得られた焼
結体からＧ級のスローアウェィチップを作成した。次い
で以下に示す各成膜条件で被覆処理することにより表１
に示す皮膜構造の試料１〜３を得た。尚、膜厚の測定は
チップを研摩しＳＥＭ（走査型電子顕微鏡）にて、組織
観察を行い測定した。Next, the coated super-hard alloy according to the present invention will be described in detail with reference to examples. However, it goes without saying that the present invention is not limited to the scope of these examples.
WC 72%, 8% TiC, (Ta
Nb) Powder was blended with a composition of 11% C and 9% Co (% by weight), and sintered at 1400 ° C. for 1 hour in a vacuum. Next, coating was performed under each of the film forming conditions described below to obtain the results shown in Table 1.
Samples 1 to 3 having the film structures shown in Table 1 were obtained. The film thickness was measured by polishing the chip and observing the structure with an SEM (scanning electron microscope).
【００１０】（１）試料Ｎｏ１の成膜は、スローアウェ
ィチップを耐熱合金製反応容器内で８００℃に加熱、２
０Ｔｏｒｒの減圧化で、ＴｉＣｌ4 ４％ Ｎ2 ４％
Ｈ2９６％の割合で混合したガスを５ｌ／ｍｉｎの流量
で流し、０．３時間反応させ０．５μｍのＴｉＮ層を被
覆した後、Ｔｉ（ＣＨ3）ＣＮ ４％ Ｎ2 ４％、Ｈ2
９２％の割合で混合したガスを５ｌ／ｍｉｎの流量で
送り、２時間反応させ４μｍのＴｉＣＮ層を被覆し内層
４．５μｍとした。その後、１０Ｔｏｒｒに真空排気
し、１０２０℃に昇温し、ＴｉＣｌ4 ４％ＣＨ4 ４％
Ｈ2 ９２％の割合で混合したガスを２０ｍｉｎ流
し、２μｍのＴｉＣ膜を生成し、中間層とした。次い
で、ＡｌＣｌ3 ５％ ＣＯ2 ５％、ＣＯ １５％ Ｈ
2 ７５％の割合で混合したガスを供給し、温度は１０
２０℃、２時間保持し、１．５μｍのＡｌ2Ｏ3層を被覆
し、最後に、ＴｉＮ膜を０．５μｍ、前記と同様の方法
で成膜し、表面を金色とした。このチップを、曲げ試験
において破断した後、ＳＥＭ（走査型電子顕微鏡）に
て、その破面を観察をした結果を図１に示す。内層部分
は柱状晶がよく発達しているのに対し、中間層は粒状に
成膜されていることが分かり、外層／最外層も中間層の
粒度に近似し、粗粒化していないことが分かる。また、
図２に最外層の表面観察した結果も併せて示す。（写真
の倍率はいずれも５０００倍）(1) The sample No. 1 was formed by heating a throw-away tip to 800 ° C. in a heat-resistant alloy reaction vessel.
At reduced pressure of 0 Torr, 4% TiCl 4 4% N 2
A gas mixed at a rate of 96% of H 2 was flowed at a flow rate of 5 l / min, reacted for 0.3 hours to coat a 0.5 μm TiN layer, and then Ti (CH 3 ) CN 4% N 2 4% Two
A gas mixed at a rate of 92% was sent at a flow rate of 5 l / min and reacted for 2 hours to coat a 4 μm TiCN layer to form an inner layer of 4.5 μm. Thereafter, the chamber is evacuated to 10 Torr, the temperature is raised to 1020 ° C., and TiCl 4 4% CH 4 4%
A gas mixed at a rate of 92% of H 2 was flowed for 20 minutes to form a 2 μm TiC film, which was used as an intermediate layer. Then, AlCl 3 5% CO 2 5%, CO 15% H
2 A gas mixture of 75% was supplied, and the temperature was 10
The temperature was maintained at 20 ° C. for 2 hours, and a 1.5 μm Al 2 O 3 layer was coated. Finally, a 0.5 μm TiN film was formed by the same method as described above, and the surface was colored gold. FIG. 1 shows the result of observing the fracture surface of this chip by a SEM (scanning electron microscope) after breaking it in a bending test. It can be seen that the columnar crystals are well developed in the inner layer portion, whereas the intermediate layer is formed in a granular form, and the outer layer / outermost layer is similar to the particle size of the intermediate layer and is not coarse-grained. . Also,
FIG. 2 also shows the results of surface observation of the outermost layer. (All photos are 5000x magnification)
【００１１】（２）試料Ｎｏ２の成膜は耐熱合金製反応
容器内で８００℃に加熱し、２０Ｔｏｒｒの減圧化でＴ
ｉＣｌ4 ４％ Ｎ2 ４％ Ｈ2 ９６％の割合で混合
したガスを５ｌ／ｍｉｎの流量で流し、０．５時間反応
させ１．０μｍのＴｉＮ被覆層を得た。その後、試料Ｎ
ｏ１と同様の方法により被覆した。(2) The film of sample No. 2 is heated to 800 ° C. in a reaction vessel made of a heat-resistant alloy, and T
A gas mixed at a rate of iCl 4 4% N 2 4% H 2 96% was flowed at a flow rate of 5 l / min, and reacted for 0.5 hour to obtain a 1.0 μm TiN coating layer. Then, sample N
Coating was carried out in the same manner as in o1.
【００１２】（３）試料Ｎｏ３の成膜は、従来例のひと
つである耐熱合金製反応容器内で１０５０℃に加熱し、
２０Ｔｏｒｒの減圧化でＴｉＣｌ4 ４％ ＣＨ4 ２％
Ｎ2 ３０％、Ｈ2 ６４％の割合で混合したガスを５
ｌ／ｍｉｎの流量で流し、２．５時間反応させ５μｍの
ＴｉＣＮ被覆層を得た。その後、試料Ｎｏ１と同様の方
法によりに被覆した。(3) The film of sample No. 3 is heated to 1050 ° C. in a heat-resistant alloy reaction vessel, which is one of the conventional examples.
At reduced pressure of 20 Torr, TiCl 4 4% CH 4 2%
A gas mixture of 30% N 2 and 64% H 2
The mixture was allowed to react at a flow rate of 1 / min for 2.5 hours to obtain a TiCN coating layer of 5 μm. Then, it coated by the same method as the sample No1.
【００１３】これら３種のチップを用い以下の切削条
件、すなわち 鋳物連続切削 被削材 ＦＣ２５（ＨＢ２３０） 切削速度 １８０ｍ／ｍｉｎ 送り ０．３ｍｍ／ｒｅｖ 切り込み １．５ｍｍ 水溶性切削油使用 で切削試験を行った。表１に平均逃げ面摩耗量が０．４
ｍｍ、クレーター摩耗が０．１ｍｍのどちらかに達した
時間を寿命と判断し、その時間を示す。Using these three types of inserts, the following cutting conditions were used: continuous casting of cutting work material FC25 (HB230) Cutting speed 180 m / min Feeding 0.3 mm / rev Cutting depth 1.5 mm A cutting test was performed using a water-soluble cutting oil. went. Table 1 shows that the average flank wear was 0.4
and the time when the crater wear reached either 0.1 mm was determined as the life, and the time is indicated.
【００１４】[0014]
【表１】 [Table 1]
【００１５】試料Ｎｏ（３）のスローアウェイチップは
２５分間の切削で寿命に達しているのに対し、本発明に
よる（１）、（２）は表１から明からかなように４０〜
５０分間切削出来ることがわかる。また本発明によるチ
ップの寿命はいずれも平均逃げ面の摩耗によるものであ
りクレーター摩耗は寿命まで切削してもブレークされず
良好な摩耗形態を示した。The throw-away insert of sample No. (3) has reached the end of its life after cutting for 25 minutes, while (1) and (2) according to the present invention have a life of 40 to 40 as shown in Table 1.
It can be seen that cutting can be performed for 50 minutes. In addition, the life of each of the tips according to the present invention was due to wear of the average flank, and the crater wear did not break even after cutting until the life, showing a favorable wear mode.
【００１６】更に、前記実施例で用いたものと同じ基体
からなるスローアウェイチツプにＴｉＣ、ＴｉＮまたは
ＴｉＣＮ層の厚さ、Ａｌ2Ｏ3の厚さを種々に変化させた
ものを作成した。成膜の条件は実施例１と同様に行い、
時間の調整で膜厚をコントロールした。得られたものの
膜の構成、膜厚等を表２に示す。また、これらのものを
用い、実施例１と同様な方法で切削試験を行った結果も
同表に示す。Further, a throw-away chip made of the same substrate as that used in the above-mentioned embodiment was prepared by changing the thickness of the TiC, TiN or TiCN layer and the thickness of Al 2 O 3 in various ways. The conditions for film formation were the same as in Example 1,
The film thickness was controlled by adjusting the time. Table 2 shows the structure, thickness, and the like of the film obtained. The same table also shows the results of cutting tests performed using these materials in the same manner as in Example 1.
【００１７】[0017]
【表２】 [Table 2]
【００１８】表２から明らかなように、本発明による被
覆超硬合金はいずれも優れた耐クレーター摩耗性を有
し、また寿命も永いことがわかる。As is clear from Table 2, all the coated cemented carbides according to the present invention have excellent crater wear resistance and long life.
【００１９】[0019]
【発明の効果】上述のように、本発明被覆超硬質合金
は、内層にＴｉＮ、ＴｉＣＮと外層Ａｌ2Ｏ3等の中間に
両者と親和性の良い粒状のＴｉの炭化物等を被覆するこ
とによって、層間の粒度を異ならせ、特に耐摩耗性に富
む高性能な被覆超硬工具が得られる。As described above, the coated super-hard alloy of the present invention is obtained by coating the inner layer of TiN, TiCN, the outer layer of Al 2 O 3, etc. with a granular Ti carbide having good affinity for both. In addition, a high-performance coated cemented carbide tool having a different grain size between layers and having particularly high wear resistance can be obtained.
【図１】図１は、本発明被覆超硬工具の金属組織を走査
型電子顕微鏡（ＳＥＭ）でその断面破面を観察した結果
を示す。FIG. 1 shows the results of observing the cross-sectional fracture surface of the metal structure of the coated carbide tool of the present invention with a scanning electron microscope (SEM).
【図２】図２は、図１と同一の試料の金属組織を走査型
電子顕微鏡（ＳＥＭ）で最表面を観察した結果を示す。FIG. 2 shows the result of observing the outermost surface of a metal structure of the same sample as in FIG. 1 by using a scanning electron microscope (SEM).
───────────────────────────────────────────────────── フロントページの続き (51)Int.Cl.6 識別記号 庁内整理番号 ＦＩ 技術表示箇所 Ｃ２３Ｃ 16/40 Ｃ２３Ｃ 16/40 28/04 28/04 ──────────────────────────────────────────────────続 き Continued on the front page (51) Int.Cl. 6 Identification code Agency reference number FI Technical display location C23C 16/40 C23C 16/40 28/04 28/04
Claims (1)
ａ族の炭化物、窒化物、炭窒化物の１種以上、結合金属
としてＦｅ族、Ｃｒ族の１種以上よりなる超硬質合金を
基体とし、前記基体の表面に、内層としてＴｉＮ層上に
ＴｉＣＮ層を設け、かつ、前記ＴｉＣＮ層が２．０〜１
０μｍの膜厚で柱状晶であり、中間層はＴｉの炭化物、
窒化物、炭窒化物の１種又は２種以上が０．１〜５μｍ
の膜厚で粒状をなし、外層がＡｌの酸化物又はＴｉの窒
化物、炭窒化物の１種又は２種が０．５〜５μｍの膜厚
であることを特徴とする被覆超硬工具。1. A hard phase comprising 4a, 5a, 6 of the periodic table
A super-hard alloy consisting of at least one of carbides, nitrides, and carbonitrides of group a, and at least one of at least one of Fe group and Cr group as a bonding metal is used as a base material.
A TiCN layer is provided, and the TiCN layer is 2.0 to 1
It is a columnar crystal with a thickness of 0 μm, and the intermediate layer is a carbide of Ti,
One or more of nitrides and carbonitrides are 0.1 to 5 μm
A coated carbide tool characterized in that the outer layer has a thickness of 0.5 to 5 [mu] m, wherein the outer layer has a thickness of 0.5 to 5 [mu] m.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP3163993A JP2660180B2 (en) | 1991-06-07 | 1991-06-07 | Coated carbide tool |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP3163993A JP2660180B2 (en) | 1991-06-07 | 1991-06-07 | Coated carbide tool |
Related Child Applications (4)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP08323398A Division JP3115246B2 (en) | 1996-11-19 | 1996-11-19 | Coated carbide tools for turning |
| JP8323400A Division JP2974284B2 (en) | 1996-11-19 | 1996-11-19 | Manufacturing method of coated carbide tool |
| JP08323399A Division JP3115247B2 (en) | 1996-11-19 | 1996-11-19 | Coated cemented carbide indexable inserts |
| JP8323401A Division JP2974285B2 (en) | 1996-11-19 | 1996-11-19 | Manufacturing method of coated carbide tool |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH0734250A JPH0734250A (en) | 1995-02-03 |
| JP2660180B2 true JP2660180B2 (en) | 1997-10-08 |
Family
ID=15784724
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP3163993A Expired - Lifetime JP2660180B2 (en) | 1991-06-07 | 1991-06-07 | Coated carbide tool |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP2660180B2 (en) |
Families Citing this family (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2927182B2 (en) * | 1994-05-31 | 1999-07-28 | 三菱マテリアル株式会社 | Surface coated tungsten carbide based cemented carbide cutting tool with excellent interlayer adhesion with hard coating layer |
| JP2005262386A (en) * | 2004-03-18 | 2005-09-29 | Sumitomo Electric Hardmetal Corp | Surface coated cutting tool |
| CN104046874B (en) * | 2014-07-11 | 2016-02-10 | 辽阳斯佳机械配件有限公司 | A kind of pelletizing template tungsten-bast alloy |
Family Cites Families (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0364469A (en) * | 1989-08-01 | 1991-03-19 | Hitachi Tool Eng Ltd | Coated sintered hard alloy tool |
| JP2645340B2 (en) * | 1989-09-08 | 1997-08-25 | 日立ツール 株式会社 | Manufacturing method of coated cemented carbide tool |
-
1991
- 1991-06-07 JP JP3163993A patent/JP2660180B2/en not_active Expired - Lifetime
Also Published As
| Publication number | Publication date |
|---|---|
| JPH0734250A (en) | 1995-02-03 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| US6214247B1 (en) | Substrate treatment method | |
| KR960015546B1 (en) | Diffusion barrier coating material | |
| JP4711714B2 (en) | Surface coated cutting tool | |
| JPH066788B2 (en) | Cutting tool made of coated carbide alloy | |
| JP4832108B2 (en) | Surface coated cutting tool | |
| JPH0615714B2 (en) | Sintered hard metal products | |
| JP4330859B2 (en) | Coated cemented carbide and method for producing the same | |
| KR20040084781A (en) | Coated cutting tool insert for machining of cast irons | |
| JP5383259B2 (en) | Cutting tools | |
| JP2002543997A (en) | Cutting tool coated with Al2O3 | |
| JPH10156606A (en) | Aluminum oxide coating tool and manufacture thereof | |
| JPH0615717B2 (en) | High toughness coating material and manufacturing method thereof | |
| JP2660180B2 (en) | Coated carbide tool | |
| JP4351521B2 (en) | Surface coated cutting tool | |
| JP2974285B2 (en) | Manufacturing method of coated carbide tool | |
| JP3115247B2 (en) | Coated cemented carbide indexable inserts | |
| JP2004291162A (en) | Surface coated cutting tool | |
| JP3115246B2 (en) | Coated carbide tools for turning | |
| JP2974284B2 (en) | Manufacturing method of coated carbide tool | |
| JPH10237650A (en) | Wc base cemented carbide and its production | |
| JP4284144B2 (en) | Surface coated cutting tool | |
| JP2917555B2 (en) | Hard layer coated cemented carbide cutting tool and its manufacturing method | |
| JP2733809B2 (en) | Coated tool | |
| JP4936742B2 (en) | Surface coating tools and cutting tools | |
| JP4663248B2 (en) | Surface coated cutting tool |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| R250 | Receipt of annual fees |
Free format text: JAPANESE INTERMEDIATE CODE: R250 |
|
| R250 | Receipt of annual fees |
Free format text: JAPANESE INTERMEDIATE CODE: R250 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20090613 Year of fee payment: 12 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20090613 Year of fee payment: 12 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20100613 Year of fee payment: 13 |
|
| S531 | Written request for registration of change of domicile |
Free format text: JAPANESE INTERMEDIATE CODE: R313531 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20100613 Year of fee payment: 13 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20100613 Year of fee payment: 13 |
|
| R360 | Written notification for declining of transfer of rights |
Free format text: JAPANESE INTERMEDIATE CODE: R360 |
|
| R370 | Written measure of declining of transfer procedure |
Free format text: JAPANESE INTERMEDIATE CODE: R370 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20100613 Year of fee payment: 13 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20100613 Year of fee payment: 13 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20110613 Year of fee payment: 14 |
|
| EXPY | Cancellation because of completion of term |