JPH08187605A - Cutting tool of surface coated tungsten carbide based cemented carbide with its hard coating layer having excellent inter-layer adhesion - Google Patents
Cutting tool of surface coated tungsten carbide based cemented carbide with its hard coating layer having excellent inter-layer adhesionInfo
- Publication number
- JPH08187605A JPH08187605A JP34005894A JP34005894A JPH08187605A JP H08187605 A JPH08187605 A JP H08187605A JP 34005894 A JP34005894 A JP 34005894A JP 34005894 A JP34005894 A JP 34005894A JP H08187605 A JPH08187605 A JP H08187605A
- Authority
- JP
- Japan
- Prior art keywords
- layer
- cemented carbide
- hard coating
- cutting tool
- based cemented
- 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.)
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- Cutting Tools, Boring Holders, And Turrets (AREA)
- Physical Vapour Deposition (AREA)
- Chemical Vapour Deposition (AREA)
Abstract
Description
【０００１】[0001]
【産業上の利用分野】この発明は、硬質被覆層がすぐれ
た層間密着性を有し、したがって切削抵抗の大きい、例
えば軟鋼などの切削に用いた場合に長期に亘ってすぐれ
た切削性能を発揮する表面被覆炭化タングステン基超硬
合金製切削工具（以下、被覆超硬切削工具という）に関
するものである。BACKGROUND OF THE INVENTION 1. Field of the Invention The present invention has a hard coating layer having excellent interlayer adhesion, and therefore exhibits excellent cutting performance over a long period of time when used for cutting, for example, mild steel having a large cutting resistance. The present invention relates to a surface-coated tungsten carbide based cemented carbide cutting tool (hereinafter referred to as a coated cemented carbide cutting tool).
【０００２】[0002]
【従来の技術】従来、例えば特公昭５７−１５８５号公
報や特公昭５９−５２７０３号公報に記載されるよう
に、全体的に均質な炭化タングステン基超硬合金基体
や、結合相形成成分としての例えばＣｏなどの含有量が
基体内部に比して相対的に高い表面部、すなわち表面部
に結合相富化帯域を有する炭化タングステン基超硬合金
基体（以下、これらを総称して超硬合金基体という）の
表面に、化学蒸着法や物理蒸着法を用いて、窒化チタン
（以下、ＴｉＮで示す）の第１層、炭窒化チタン（以
下、ＴｉＣＮで示す）の第２層、炭化チタン（以下、Ｔ
ｉＣで示す）の第３層、および酸化アルミニウム（以
下、Ａｌ2 Ｏ3 で示す）の第４層、さらに必要に応じて
ＴｉＮの第５層からなる硬質被覆層を３〜３０μｍの平
均層厚で形成してなる被覆超硬切削工具が、主に合金鋼
や鋳鉄の施削やフライス切削などに用いられていること
は、良く知られているところである。2. Description of the Related Art Conventionally, as described in Japanese Patent Publication No. 57-1585 and Japanese Patent Publication No. 59-52703, for example, an entirely homogeneous tungsten carbide based cemented carbide substrate and a binder phase forming component have been used. For example, a tungsten carbide based cemented carbide substrate having a surface portion in which the content of Co or the like is relatively high compared to the inside of the substrate, that is, a surface portion having a binder phase enriched zone (hereinafter, these are collectively referred to as cemented carbide substrate. On the surface of chemical vapor deposition method or physical vapor deposition method, the first layer of titanium nitride (hereinafter referred to as TiN), the second layer of titanium carbonitride (hereinafter referred to as TiCN), titanium carbide (hereinafter referred to as , T
a hard coating layer composed of a third layer of iC), a fourth layer of aluminum oxide (hereinafter referred to as Al 2 O 3 ) and, if necessary, a fifth layer of TiN, having an average layer thickness of 3 to 30 μm. It is well known that the coated cemented carbide cutting tool formed in (4) is mainly used for machining of alloy steel and cast iron and milling.
【０００３】[0003]
【発明が解決しようとする課題】一方、近年の切削機械
のＦＡ化はめざましく、かつ切削加工の省力化の要求と
相まって、切削工具には汎用性が求められる傾向にある
が、上記の従来被覆超硬切削工具においては、これを合
金鋼や鋳鉄などの切削に用いた場合には問題はないが、
特に切削抵抗の高い軟鋼などの切削に用いた場合、硬質
被覆層の層間密着性が十分でないために、硬質被覆層に
層間剥離やチッピングが発生し易く、これが原因で比較
的短時間で使用寿命に至るのが現状である。On the other hand, in recent years, the use of FA in cutting machines has been remarkable, and in conjunction with the demand for labor saving in cutting work, cutting tools tend to be required to be versatile. For carbide cutting tools, there is no problem if this is used for cutting alloy steel or cast iron, etc.
Particularly when used for cutting mild steel with high cutting resistance, the interlayer adhesion of the hard coating layer is not sufficient, so that the hard coating layer is liable to delamination and chipping, which causes a relatively short service life. At present.
【０００４】[0004]
【課題を解決するための手段】そこで、本発明者等は、
上述のような観点から、上記の従来被覆超硬切削工具に
着目し、これを構成する硬質被覆層の層間密着性の向上
をはかるべく研究を行なった結果、 （ａ） 上記の従来被覆超硬切削工具を構成する硬質被
覆層において、超硬合金基体に対する第１層のＴｉＮ層
の密着性は相対的に高いが、第２層のＴｉＣＮ層と第１
層のＴｉＮ層および第３層のＴｉＣ層、並びに第４層の
Ａｌ2 Ｏ3 層と第３層のＴｉＣ層および第５層のＴｉＮ
層の密着性が不十分であり、これが原因で層間剥離やチ
ッピングが発生し易くなること。 （ｂ） 上記の従来被覆超硬切削工具を構成する硬質被
覆層において、第１層のＴｉＮ層、第２層のＴｉＣＮ
層、第３層のＴｉＣ層、さらに必要に応じて形成される
第５層のＴｉＮ層はいずれも粒状結晶組織をもち、第４
層のＡｌ2 Ｏ3 層はアルファ型結晶組織をもつが、前記
第２層のＴｉＣＮ層を縦長成長結晶組織とすると共に、
前記第４層のＡｌ2 Ｏ3 層をカッパー型結晶を主体とす
る組織、望ましくは、カッパー型結晶が５０容量％以上
を占め、残りがアルファ型結晶からなる混合組織、さら
に望ましくは実質的にカッパー型結晶からなる組織とす
ると、前記第２層に対する第１層のＴｉＮ層および第３
層のＴｉＣ層、並びに前記第４層に対する第３層のＴｉ
Ｃ層、および第５層のＴｉＮ層の密着性が著しく向上す
ること。 （ｃ） 第２層のＴｉＣＮ層または第３層のＴｉＣ層形
成後に、１０〜１００torrの水素雰囲気中、温度：８５
０〜１１００℃に１〜５時間保持の条件で加熱処理を施
すと、超硬合金基体を構成する成分のうち少なくともＷ
とＣｏ成分が毛細管現象により第１，２層または第１〜
３層の粒界に拡散移動し、これらの層の粒界に少なくと
もＷとＣｏが含有するようになり、この結果結晶粒間密
着性の向上と相まって層間密着性が一段と向上するよう
になること。以上（ａ）〜（ｃ）に示される研究結果を
得たのである。Therefore, the present inventors have
From the viewpoints described above, as a result of focusing on the above-mentioned conventional coated carbide cutting tool and conducting a study for improving the interlayer adhesion of the hard coating layer constituting the same, (a) the above conventional coated carbide In the hard coating layer constituting the cutting tool, the adhesion of the TiN layer of the first layer to the cemented carbide substrate is relatively high, but the TiCN layer of the second layer and the first layer
TiN layer and third TiC layer, and fourth Al 2 O 3 layer and third TiC layer and fifth TiN layer
Insufficient adhesion of layers, which tends to cause delamination and chipping. (B) In the hard coating layer constituting the conventional coated carbide cutting tool, the first TiN layer and the second TiCN layer
The third layer, the third TiC layer, and the fifth TiN layer, which is formed as necessary, all have a granular crystal structure,
Although the Al 2 O 3 layer of the layer has an alpha-type crystal structure, the TiCN layer of the second layer has a vertically elongated crystal structure, and
The fourth layer Al 2 O 3 layer has a structure mainly composed of kappa-type crystals, preferably a mixed structure in which the kappa-type crystals occupy 50% by volume or more and the rest is alpha-type crystals, and more preferably substantially When the structure is made of a copper type crystal, the TiN layer of the first layer and the third layer of the second layer are formed.
TiC layer, and a third Ti layer for the fourth layer
The adhesion of the C layer and the TiN layer of the fifth layer is remarkably improved. (C) After forming the second TiCN layer or the third TiC layer, in a hydrogen atmosphere of 10 to 100 torr, temperature: 85
When the heat treatment is performed at 0 to 1100 ° C. for 1 to 5 hours, at least W out of the constituents of the cemented carbide substrate is obtained.
And Co components are the first and second layers or the first to first layers due to the capillary phenomenon.
Diffusion and migration to the grain boundaries of the three layers, and at least W and Co are contained in the grain boundaries of these layers, and as a result, the interlayer adhesion is further improved in combination with the improvement of the inter-grain adhesion. . The research results shown in (a) to (c) above were obtained.
【０００５】この発明は、上記の研究結果にもとづいて
なされたものであって、超硬合金基体の表面に、第１層
のＴｉＮ層、第２層のＴｉＣＮ層、第３層のＴｉＣ層、
および第４層のＡｌ2 Ｏ3 層、さらに必要に応じて第５
層のＴｉＮ層からなる硬質被覆層を３〜３０μｍの平均
層厚で形成してなる被覆超硬切削工具において、（ａ）
上記第１層、上記第３層、および上記第５層を粒状結
晶組織、上記第２層を縦長成長結晶組織、上記第４層を
カッパー型結晶を主体とした組織とすると共に、（ｂ）
上記第１，２層または上記第１〜３層の結晶粒界に、
上記超硬合金基体を構成する成分のうちの少なくともＷ
とＣｏを含有させること、以上（ａ）および（ｂ）によ
り上記硬質被覆層にすぐれた層間密着性を具備せしめた
被覆超硬切削工具に特徴を有するものである。The present invention has been made on the basis of the above-mentioned research results. The first layer of TiN layer, the second layer of TiCN layer, and the third layer of TiC layer are formed on the surface of a cemented carbide substrate.
And a fourth Al 2 O 3 layer, and optionally a fifth layer
A hard coating layer made of a TiN layer having a mean layer thickness of 3 to 30 μm, wherein (a)
The first layer, the third layer, and the fifth layer have a granular crystal structure, the second layer has a vertically elongated crystal structure, and the fourth layer has a structure mainly composed of kappa-type crystals, and (b)
In the grain boundaries of the first and second layers or the first to third layers,
At least W of the components constituting the cemented carbide substrate
It is characterized by the inclusion of Co and Co, and by the above (a) and (b), the coated cemented carbide cutting tool having the hard coating layer with excellent interlayer adhesion.
【０００６】なお、この発明の被覆超硬切削工具を構成
する硬質被覆層のうちの第２層の縦長結晶組織を有する
ＴｉＣＮ層は、例えば特開平６−８０１０号公報に記載
される通り、 （ア） 反応ガス組成、容量％で、ＴｉＣｌ4 ：１〜４
％、 ＣＨ3 ＣＮ：０．１〜５％、Ｎ2 ：０〜３５
％、 Ｈ2 ：残り、 （イ） 反応温度：８５０〜９５０℃、 （ウ） 雰囲気圧力：３０〜２００torr、 の条件で形成するのが望ましい。一方、粒状結晶組織を
有するＴｉＣＮ層は、通常、 （ア） 反応ガス組成、容量％で、ＴｉＣｌ4 ：１〜５
％、 ＣＨ4 ：２〜７％、Ｎ2 ：１５〜３０％、
Ｈ2 ：残り、 （イ） 反応温度：９５０〜１０５０℃、 （ウ） 雰囲気圧力：３０〜２００torr、 の条件で形成される。また、カッパー型結晶を主体とす
る組織を有するＡｌ2 Ｏ3 層は、 （ア） 反応ガス組成、容量％で、初期段階の１〜１２
０分を、ＡｌＣｌ3 ：１〜２０％、 Ｈ2 ：残り、ま
たは、ＡｌＣｌ3 ：１〜２０％、ＨＣｌ：１〜２０％お
よび／またはＨ2 Ｓ：０．０５〜５％、Ｈ2 ：残り、と
し、以後、ＡｌＣｌ3 ：１〜２０％、 ＣＯ2 ：０．
５〜３０％、Ｈ2 ：残り、または、ＡｌＣｌ3 ：１〜２
０％、 ＣＯ2 ：０．５〜３０％、ＨＣｌ：１〜２０
％および／またはＨ2 Ｓ：０．０５〜５％、Ｈ2 ：残
り、 （イ） 反応温度：８５０〜１０００℃、 （ウ） 雰囲気圧力：３０〜２００torr、 の条件で形成される。The TiCN layer having the longitudinal crystal structure of the second layer of the hard coating layers constituting the coated cemented carbide cutting tool of the present invention is as described in, for example, JP-A-6-8010. A) the reaction gas composition, in volume%, TiCl 4: 1 to 4
%, CH 3 CN: 0.1~5% , N 2: 0~35
%, H 2 : Remaining, (a) Reaction temperature: 850 to 950 ° C., (c) Atmospheric pressure: 30 to 200 torr. On the other hand, a TiCN layer having a granular crystal structure is usually (a) with a reaction gas composition and a volume percentage of TiCl 4 : 1 to 5
%, CH 4: 2~7%, N 2: 15~30%,
H 2 : remaining, (a) reaction temperature: 950 to 1050 ° C., (c) atmosphere pressure: 30 to 200 torr. Further, the Al 2 O 3 layer having a structure mainly composed of copper-type crystals has (a) a reaction gas composition and a volume% at an initial stage of 1 to 12
0 minutes, AlCl 3: 1~20%, H 2: remainder, or,, AlCl 3: 1~20%, HCl: 1~20% and / or H 2 S: 0.05~5%, H 2: and the rest, and, thereafter, AlCl 3: 1~20%, CO 2: 0.
5 to 30%, H 2 : remaining, or AlCl 3 : 1 to 2
0%, CO 2: 0.5~30% , HCl: 1~20
% And / or H 2 S: 0.05 to 5%, H 2 : remaining, (a) reaction temperature: 850 to 1000 ° C., (c) atmosphere pressure: 30 to 200 torr.
【０００７】また、この発明の被覆超硬切削工具を構成
する硬質被覆層は、化学蒸着法および／または物理蒸着
法にて、上記の条件および通常の条件で、超硬合金基体
の表面に、まず第１層のＴｉＮ層を蒸着し、ついで第２
層のＴｉＣＮ層から第４層のＡｌ2 Ｏ3 層まで、さらに
必要に応じて第５層のＴｉＮ層を順次蒸着することによ
って形成されるが、前記第２層以降の形成に際して、前
記第１層のＴｉＮ層中に前記超硬合金基体中のＣ成分が
拡散固溶する場合があるが、この場合は前記第１層の一
部あるいは全体がＴｉＣＮとなる。Further, the hard coating layer constituting the coated cemented carbide cutting tool of the present invention is formed on the surface of the cemented carbide substrate by the chemical vapor deposition method and / or the physical vapor deposition method under the above-mentioned conditions and ordinary conditions. First, the first TiN layer is vapor-deposited, then the second
The TiCN layer of the fourth layer to the Al 2 O 3 layer of the fourth layer are further formed by sequentially vapor-depositing the TiN layer of the fifth layer, if necessary. In some cases, the C component in the cemented carbide substrate may diffuse and form a solid solution in the TiN layer of the layer. In this case, part or all of the first layer becomes TiCN.
【０００８】さらに、上記硬質被覆層の平均層厚を３〜
３０μｍと定めたのは、その平均層厚が３μｍ未満では
所望のすぐれた耐摩耗性を確保することができず、一方
その平均層厚が３０μｍを越えると耐欠損性が急激に低
下するようになるという理由によるものであり、また第
１層のＴｉＮ層の平均層厚は０．１〜５μｍ、第２層の
ＴｉＣＮ層のそれは３〜２０μｍ、第３層のＴｉＣ層は
１〜１０μｍ、第４層のＡｌ2 Ｏ3 層は０．１〜１５μ
ｍ、さらに第５層のＴｉＮ層は０．１〜５μｍの平均層
厚とするのが望ましい。Further, the average layer thickness of the hard coating layer is 3 to
The value of 30 μm is set so that the desired excellent wear resistance cannot be ensured when the average layer thickness is less than 3 μm, while the fracture resistance sharply decreases when the average layer thickness exceeds 30 μm. The average layer thickness of the TiN layer of the first layer is 0.1 to 5 μm, that of the TiCN layer of the second layer is 3 to 20 μm, and that of the TiC layer of the third layer is 1 to 10 μm. Four layers of Al 2 O 3 are 0.1-15μ
m, and the TiN layer of the fifth layer preferably has an average layer thickness of 0.1 to 5 μm.
【０００９】[0009]
【実施例】つぎに、この発明の被覆超硬切削工具を実施
例により具体的に説明する。原料粉末として、平均粒
径：３μｍを有する中粒ＷＣ粉末、同５μｍの粗粒ＷＣ
粉末、同１．５μｍの（Ｔｉ，Ｗ）Ｃ（重量比で、以下
同じ、ＴｉＣ／ＷＣ＝３０／７０）粉末、同１．２μｍ
の（Ｔｉ，Ｗ）ＣＮ（ＴｉＣ／ＴｉＮ／ＷＣ＝２４／２
０／５６）粉末、および同１．２μｍのＣｏ粉末を用意
し、これら原料粉末を表１に示される配合組成に配合
し、ボールミルで７２時間湿式混合し、乾燥した後、Ｉ
ＳＯ・ＣＮＭＧ１２０４０８（超硬合金基体Ａ〜Ｄ用）
および同ＳＥＥＮ４２ＡＦＴＮ１（超硬合金基体Ｅ用）
に定める形状の圧粉体にプレス成形し、この圧粉体を同
じく表１に示される条件で真空焼結することにより超硬
合金基体Ａ〜Ｅをそれぞれ製造した。さらに、上記超硬
合金基体Ｂに対して、１００torrのＣＨ4 ガス雰囲気
中、温度：１４００℃に１時間保持後、徐冷の浸炭処理
を施し、処理後、基体表面に付着するカーボンとＣｏを
酸およびバレル研磨で除去することにより、表面から１
０μｍの位置で最大Ｃｏ含有量：１５重量％、深さ：４
０μｍのＣｏ富化帯域を基体表面部に形成した。また、
上記超硬合金基体ＡおよびＤには、焼結したままで、表
面部に表面から１５μｍの位置で最大Ｃｏ含有量：９重
量％、深さ：２０μｍのＣｏ富化帯域が形成されてお
り、残りの超硬合金基体ＣおよびＥには、前記Ｃｏ富化
帯域の形成がなく、全体的に均質な組織をもつものであ
った。さらに、表１には上記超硬合金基体Ａ〜Ｅの内部
硬さ（ロックウェル硬さＡスケール）をそれぞれ示し
た。Next, the coated carbide cutting tool of the present invention will be described in detail with reference to examples. As the raw material powder, a medium-grain WC powder having an average particle diameter of 3 μm and a coarse-grain WC having the same particle diameter of 5 μm
Powder, 1.5 μm (Ti, W) C (weight ratio, same below, TiC / WC = 30/70) powder, 1.2 μm
(Ti, W) CN (TiC / TiN / WC = 24/2)
0/56) powder and Co powder of 1.2 μm were prepared, these raw material powders were compounded to the compounding composition shown in Table 1, wet-mixed for 72 hours with a ball mill, dried, and then I
SO / CNMG120408 (for cemented carbide substrates A to D)
And SEEN42AFTN1 (for cemented carbide substrate E)
Cemented carbide base bodies A to E were manufactured by press-molding into a green compact having the shape defined in 1. and vacuum sintering the green compact under the conditions shown in Table 1. Further, the above cemented carbide substrate B was kept at a temperature of 1400 ° C. for 1 hour in a CH 4 gas atmosphere of 100 torr and then subjected to carburizing treatment by slow cooling. After the treatment, carbon and Co attached to the substrate surface were removed. 1 from the surface by removing with acid and barrel polishing
Maximum Co content at 0 μm: 15% by weight, depth: 4
A Co enriched zone of 0 μm was formed on the substrate surface. Also,
In the cemented carbide substrates A and D, as-sintered, a Co-enriched zone having a maximum Co content of 9 wt% and a depth of 20 μm was formed on the surface at a position of 15 μm from the surface, The remaining cemented carbide substrates C and E did not have the Co-enriched zone formed and had an overall homogeneous structure. Further, Table 1 shows the internal hardness (Rockwell hardness A scale) of each of the cemented carbide substrates AE.
【００１０】ついで、これらの超硬合金基体Ａ〜Ｅの表
面に、ホーニングを施した状態で、通常の化学蒸着装置
を用い、表２に示される条件で、表３〜６に示される組
成および結晶組織、並びに平均層厚の硬質被覆層を形成
し、この間第２層形成後に３５torrの水素雰囲気中、温
度：１０５０℃に１〜５時間の範囲内の所定時間保持の
条件で加熱処理を施すことにより本発明被覆超硬切削工
具１〜７を製造すると共に、前記加熱処理を行なわずに
従来被覆超硬切削工具１〜７をそれぞれ製造した。この
結果得られた各種の被覆超硬切削工具を構成する硬質被
覆層の第１，２層について、それぞれの層を透過電子顕
微鏡（ＴＥＭ）で観察して各層毎適宜５ヶ所の粒界を特
定し、この特定粒界のＷおよびＣｏ含有量をエネルギー
分散型Ｘ線測定装置で定量分析した。これらの結果を表
３〜６に平均値で示した。Then, the surfaces of these cemented carbide substrates A to E were subjected to honing, using a conventional chemical vapor deposition apparatus, under the conditions shown in Table 2 under the conditions shown in Table 2 and the compositions shown in Tables 3 to 6 A crystalline structure and a hard coating layer having an average layer thickness are formed, and after that, a heat treatment is performed in a hydrogen atmosphere of 35 torr at a temperature of 1050 ° C. for a predetermined time within a range of 1 to 5 hours after forming the second layer. Thus, the coated carbide cutting tools 1 to 7 of the present invention were manufactured, and the conventional coated carbide cutting tools 1 to 7 were manufactured without performing the heat treatment. Regarding the first and second hard coating layers constituting the various coated carbide cutting tools obtained as a result, each layer is observed with a transmission electron microscope (TEM), and 5 grain boundaries are appropriately specified for each layer. Then, the W and Co contents of this specific grain boundary were quantitatively analyzed by an energy dispersive X-ray measuring device. The results are shown in Tables 3 to 6 as average values.
【００１１】また、上記本発明被覆超硬切削工具１〜５
および従来被覆超硬切削工具１〜５について、 被削材：軟鋼の丸棒、 切削速度：３３５ｍ／min.、 送り：０．２６mm／rev.、 切込み：２mm、 切削時間：２０分、 の条件での軟鋼の連続切削試験、および、 被削材：軟鋼の角材、 切削速度：３０５ｍ／min.、 送り：０．２６mm／rev.、 切込み：１．５mm、 切削時間：２５分、 の条件での軟鋼の断続切削試験を行ない、いずれの切削
試験でも切刃の逃げ面摩耗幅を測定した。これらの測定
結果を表４，６に示した。さらに、上記本発明被覆超硬
切削工具６，７および従来被覆超硬切削工具６，７につ
いて、 被削材：軟鋼の角材、 切削速度：３０５ｍ／min.、 送り：０．３６mm／刃、 切込み：２．５mm、 切削時間：３０分、 の条件で軟鋼のフライス切削を行ない、切刃の逃げ面摩
耗幅を測定した。この測定結果も表４，６に示した。Further, the above coated carbide cutting tools 1 to 5 of the present invention.
For the conventional coated carbide cutting tools 1 to 5, the conditions of work material: round bar of mild steel, cutting speed: 335 m / min., Feed: 0.26 mm / rev., Depth of cut: 2 mm, cutting time: 20 minutes Continuous cutting test of mild steel at, and work material: square bar of mild steel, cutting speed: 305 m / min., Feed: 0.26 mm / rev., Depth of cut: 1.5 mm, cutting time: 25 minutes The mild steel was subjected to an intermittent cutting test, and the flank wear width of the cutting edge was measured in each cutting test. The results of these measurements are shown in Tables 4 and 6. Further, regarding the coated carbide cutting tools 6 and 7 of the present invention and the conventional coated carbide cutting tools 6 and 7, the work material: square bar of mild steel, cutting speed: 305 m / min., Feed: 0.36 mm / blade, cutting Milling of mild steel was performed under the following conditions: 2.5 mm, cutting time: 30 minutes, and the flank wear width of the cutting edge was measured. The measurement results are also shown in Tables 4 and 6.
【００１２】[0012]
【表１】 [Table 1]
【００１３】[0013]
【表２】 [Table 2]
【００１４】[0014]
【表３】 [Table 3]
【００１５】[0015]
【表４】 [Table 4]
【００１６】[0016]
【表５】 [Table 5]
【００１７】[0017]
【表６】 [Table 6]
【００１８】[0018]
【発明の効果】表３〜６に示される結果から、本発明被
覆超硬切削工具１〜７は、いずれも切削抵抗の高い軟鋼
の切削にもかかわらず、硬質被覆層に層間剥離やチッピ
ングの発生なく、すぐれた耐摩耗性を示すのに対して、
従来被覆超硬切削工具１〜７は、硬質被覆層における層
間密着性が不十分なために、軟鋼の切削では層間剥離や
チッピングが発生し、比較的短時間で使用寿命に至るこ
とが明らかである。上述のように、この発明の被覆超硬
切削工具は、これを構成する硬質被覆層がすぐれた層間
密着性を有するので、合金鋼や鋳鉄などの切削は勿論の
こと、切削抵抗の高い軟鋼などの切削に用いた場合にも
長期に亘ってすぐれた切削性能を発揮するのである。From the results shown in Tables 3 to 6, the coated carbide cutting tools 1 to 7 of the present invention are not susceptible to delamination or chipping of the hard coating layer despite the cutting of mild steel having high cutting resistance. While it does not occur and shows excellent wear resistance,
Conventionally, the coated carbide cutting tools 1 to 7 clearly show that the interlayer adhesion in the hard coating layer is insufficient, and delamination and chipping occur in the cutting of mild steel, resulting in a relatively short service life. is there. As described above, the coated cemented carbide cutting tool according to the present invention has a hard coating layer having excellent interlayer adhesion, so that it can cut not only alloy steel and cast iron, but also mild steel having a high cutting resistance. Even when used for cutting, excellent cutting performance is exhibited over a long period of time.
───────────────────────────────────────────────────── 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 16/36 16/40 ─────────────────────────────────────────────────── ─── Continuation of the front page (51) Int.Cl. 6 Identification code Internal reference number FI technical display location C23C 16/36 16/40
Claims (2)
合金基体、または表面部に結合相富化帯域を有する炭化
タングステン基超硬合金基体の表面に、窒化チタンの第
１層、炭窒化チタンの第２層、炭化チタンの第３層、お
よび酸化アルミニウムの第４層からなる硬質被覆層を３
〜３０μｍの平均層厚で形成してなる表面被覆炭化タン
グステン基超硬合金製切削工具において、 （ａ） 上記第１層および第３層を粒状結晶組織、上記
第２層を縦長成長結晶組織、上記第４層をカッパー型結
晶を主体とした組織とすると共に、 （ｂ） 上記第１，２層または上記第１〜３層の結晶粒
界に、上記基体を構成する成分のうちの少なくともＷと
Ｃｏが拡散含有すること、を特徴とする硬質被覆層がす
ぐれた層間密着性を有する表面被覆炭化タングステン基
超硬合金製切削工具。1. A first layer of titanium nitride, titanium carbonitride, on the surface of a wholly homogeneous tungsten carbide-based cemented carbide substrate or a tungsten carbide-based cemented carbide substrate having a binder phase enriched zone on its surface. A hard coating layer consisting of a second layer of titanium, a third layer of titanium carbide, and a fourth layer of aluminum oxide.
A surface-coated tungsten carbide based cemented carbide cutting tool formed with an average layer thickness of ˜30 μm, wherein (a) the first layer and the third layer have a granular crystal structure, the second layer has a vertically elongated crystal structure, The fourth layer has a structure mainly composed of kappa-type crystals, and (b) at least W of the components constituting the substrate is present at the crystal grain boundaries of the first and second layers or the first to third layers. A surface-coated tungsten carbide-based cemented carbide cutting tool having excellent interlayer adhesion with a hard coating layer characterized by containing and diffusing Co and Co.
合金基体、または表面部に結合相富化帯域を有する炭化
タングステン基超硬合金基体の表面に、窒化チタンの第
１層、炭窒化チタンの第２層、炭化チタンの第３層、お
よび酸化アルミニウムの第４層、さらに窒化チタンの第
５層からなる硬質被覆層を３〜３０μｍの平均層厚で形
成してなる表面被覆炭化タングステン基超硬合金製切削
工具において、 （ａ） 上記第１層、上記第３層、および第５層を粒状
結晶組織、上記第２層を縦長成長結晶組織、上記第４層
をカッパー型結晶を主体とした組織とすると共に、 （ｂ） 上記第１，２層または上記第１〜３層の結晶粒
界に、上記基体を構成する成分のうちの少なくともＷと
Ｃｏが拡散含有すること。を特徴とする硬質被覆層がす
ぐれた層間密着性を有する表面被覆炭化タングステン基
超硬合金製切削工具。2. A titanium nitride first layer, titanium carbonitride, on the surface of an entirely homogeneous tungsten carbide based cemented carbide substrate or a tungsten carbide based cemented carbide substrate having a binder phase enriched zone on the surface. Surface-coated tungsten carbide base formed by forming a hard coating layer having an average layer thickness of 3 to 30 μm, the hard coating layer including a second layer, a third layer of titanium carbide, a fourth layer of aluminum oxide, and a fifth layer of titanium nitride. In a cemented carbide cutting tool, (a) the first layer, the third layer, and the fifth layer are mainly composed of a granular crystal structure, the second layer is composed of a vertically elongated crystal structure, and the fourth layer is composed mainly of a kappa-type crystal. (B) At least W and Co of the components constituting the substrate are diffused and contained in the crystal grain boundaries of the first and second layers or the first to third layers. A surface-coated tungsten carbide-based cemented carbide cutting tool having excellent hard coating layer interlayer adhesion.
Priority Applications (5)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP34005894A JP3269305B2 (en) | 1994-12-28 | 1994-12-28 | Surface coated tungsten carbide based cemented carbide cutting tool with excellent interlayer adhesion with hard coating layer |
| US08/541,088 US5652045A (en) | 1994-10-20 | 1995-10-11 | Coated tungsten carbide-based cemented carbide blade member |
| EP95116113A EP0709484B2 (en) | 1994-10-20 | 1995-10-12 | Coated tungsten carbide-based cemented carbide blade member |
| DE69509035T DE69509035T3 (en) | 1994-10-20 | 1995-10-12 | Coated cemented tungsten carbide-based blade |
| KR1019950036041A KR100187369B1 (en) | 1994-10-20 | 1995-10-18 | Coated tungsten carbide-based cemented carbide blade member |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP34005894A JP3269305B2 (en) | 1994-12-28 | 1994-12-28 | Surface coated tungsten carbide based cemented carbide cutting tool with excellent interlayer adhesion with hard coating layer |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH08187605A true JPH08187605A (en) | 1996-07-23 |
| JP3269305B2 JP3269305B2 (en) | 2002-03-25 |
Family
ID=18333324
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP34005894A Expired - Fee Related JP3269305B2 (en) | 1994-10-20 | 1994-12-28 | Surface coated tungsten carbide based cemented carbide cutting tool with excellent interlayer adhesion with hard coating layer |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP3269305B2 (en) |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH10219451A (en) * | 1997-02-04 | 1998-08-18 | Hitachi Tool Eng Co Ltd | Multilayer-coated cemented carbide |
| JPH10219452A (en) * | 1997-02-04 | 1998-08-18 | Hitachi Tool Eng Co Ltd | Multilayer-coated cemented carbide |
| US6589602B2 (en) | 2001-04-17 | 2003-07-08 | Toshiba Tungaloy Co., Ltd. | Highly adhesive surface-coated cemented carbide and method for producing the same |
| JP2004506525A (en) * | 2000-08-11 | 2004-03-04 | ケンナメタル インコーポレイテッド | Chromium-containing cemented tungsten carbide |
| US6723389B2 (en) | 2000-07-21 | 2004-04-20 | Toshiba Tungaloy Co., Ltd. | Process for producing coated cemented carbide excellent in peel strength |
| US7172807B2 (en) | 2003-02-17 | 2007-02-06 | Kyocera Corporation | Surface-coated member |
Families Citing this family (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| SE530756C2 (en) | 2006-09-15 | 2008-09-02 | Sandvik Intellectual Property | Methods of Manufacturing a Coated Cement Cutting Tool, a Coated Cutting Tool and a Coated Rotating Cutting Tool |
-
1994
- 1994-12-28 JP JP34005894A patent/JP3269305B2/en not_active Expired - Fee Related
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH10219451A (en) * | 1997-02-04 | 1998-08-18 | Hitachi Tool Eng Co Ltd | Multilayer-coated cemented carbide |
| JPH10219452A (en) * | 1997-02-04 | 1998-08-18 | Hitachi Tool Eng Co Ltd | Multilayer-coated cemented carbide |
| US6723389B2 (en) | 2000-07-21 | 2004-04-20 | Toshiba Tungaloy Co., Ltd. | Process for producing coated cemented carbide excellent in peel strength |
| JP2004506525A (en) * | 2000-08-11 | 2004-03-04 | ケンナメタル インコーポレイテッド | Chromium-containing cemented tungsten carbide |
| US6589602B2 (en) | 2001-04-17 | 2003-07-08 | Toshiba Tungaloy Co., Ltd. | Highly adhesive surface-coated cemented carbide and method for producing the same |
| US7172807B2 (en) | 2003-02-17 | 2007-02-06 | Kyocera Corporation | Surface-coated member |
Also Published As
| Publication number | Publication date |
|---|---|
| JP3269305B2 (en) | 2002-03-25 |
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