JP2000190105A - Cutting tool made of surface coating cemented carbide having hard coating layer exhibiting good chipping resistance - Google Patents
Cutting tool made of surface coating cemented carbide having hard coating layer exhibiting good chipping resistanceInfo
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- JP2000190105A JP2000190105A JP10371997A JP37199798A JP2000190105A JP 2000190105 A JP2000190105 A JP 2000190105A JP 10371997 A JP10371997 A JP 10371997A JP 37199798 A JP37199798 A JP 37199798A JP 2000190105 A JP2000190105 A JP 2000190105A
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- layer thickness
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- hard coating
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Abstract
Description
【０００１】[0001]
【発明の属する技術分野】この発明は、硬質被覆層を構
成する縦長成長結晶組織の炭窒化チタン層（以下、ｌ−
ＴｉＣＮで示す）が一段とすぐれた耐チッピング性を有
し、特に鋼や鋳鉄などの断続切削を高速で、かつ高切り
込みや高送りなどの重切削条件で行った場合にも、切刃
にチッピング（微小欠け）などの発生なく、すぐれた切
削性能を長期に亘って発揮する表面被覆超硬合金製切削
工具（以下、被覆超硬工具という）に関するものであ
る。The present invention relates to a vertically-grown titanium carbonitride layer (hereinafter referred to as l-type) constituting a hard coating layer.
(Shown by TiCN) has a much better chipping resistance. Even when intermittent cutting of steel or cast iron is performed at high speed and under heavy cutting conditions such as high cutting and high feed, chipping ( The present invention relates to a cutting tool made of a surface-coated cemented carbide (hereinafter referred to as a coated cemented carbide tool) that exhibits excellent cutting performance over a long period of time without occurrence of minute chipping or the like.
【０００２】[0002]
【従来の技術】従来、一般に、炭化タングステン基超硬
合金基体（以下、超硬基体という）の表面に、（ａ）
いずれも０．１〜５μｍの平均層厚および粒状結晶組織
を有する、炭化チタン（以下、ＴｉＣで示す）層、窒化
チタン（以下、同じくＴｉＮで示す）層、炭窒化チタン
（以下、ＴｉＣＮで示す）層、炭酸化チタン（以下、Ｔ
ｉＣＯで示す）層、窒酸化チタン（以下、ＴｉＮＯで示
す）層、および炭窒酸化チタン（以下、ＴｉＣＮＯで示
す）層のうちの１層または２層以上からなるＴｉ化合物
層と、（ｂ） ２〜１５μｍの平均層厚のｌ−ＴｉＣＮ
層と、（ｃ） ０．５〜８μｍの平均層厚および粒状結
晶組織を有し、かつ原子比に基づく組成式でＡｌ2 Ｏ3
を満足する酸化アルミニウム（以下、Ａｌ2 Ｏ3 で示
す）層と、で構成された硬質被覆層を３〜２５μｍの全
体平均層厚で化学蒸着および／または物理蒸着してなる
被覆超硬工具が知られており、またこの被覆超硬工具が
鋼や鋳鉄などの連続切削や断続切削に用いられることも
知られている。また、一般に上記の被覆超硬工具の硬質
被覆層を構成するＡｌ2 Ｏ3 層として、α型結晶構造を
もつものやκ型結晶構造をもつものなどが広く実用に供
されることも良く知られており、さらに上記ｌ−ＴｉＣ
Ｎ層は、例えば特開平６−８０１０号公報や特開平７−
３２８８０８号公報などにより公知であり、通常の化学
蒸着装置にて、反応ガスとして有機炭窒化物を含む混合
ガスを使用し、７００〜９５０℃の中温温度域で化学蒸
着することにより形成されるものである。なお、上記の
硬質被覆層を構成するＴｉ化合物層およびｌ−ＴｉＣＮ
層は、いずれもＴｉと非金属成分（Ｃ、Ｎ、およびＯ成
分）との相対原子比が１：１、同じく非金属成分である
ＣとＮ、ＣとＯ、およびＮとＯの相対原子比も１：１、
さらに同じくＣとＮとＯの相対原子比も１：１：１であ
り、したがってＴｉＣＮ層、ＴｉＣＯ層、ＴｉＮＯ層、
およびＴｉＣＮＯ層は、それぞれＴｉ（Ｃ0.5 Ｎ
0. 5 ）、Ｔｉ（Ｃ0.5 Ｏ0.5 ）、Ｔｉ（Ｎ0.5 Ｏ
0.5 ）、およびＴｉ（Ｃ0.33Ｃ0. 33Ｎ0.33）の組成をも
つものであり、かつ層厚全体に亘って均一な組成をもつ
ものである。2. Description of the Related Art Conventionally, a tungsten carbide-based cemented carbide substrate (hereinafter referred to as a cemented carbide substrate) generally has (a)
Each of which has an average layer thickness of 0.1 to 5 μm and a granular crystal structure, a titanium carbide (hereinafter referred to as TiC) layer, a titanium nitride (hereinafter also referred to as TiN) layer, and a titanium carbonitride (hereinafter referred to as TiCN). ) Layer, titanium carbonate (hereinafter, T
a Ti compound layer comprising one or more layers of an iCO) layer, a titanium oxynitride (hereinafter, shown as TiNO) layer, and a titanium carbonitride (hereinafter, shown as TiCNO) layer; L-TiCN with an average layer thickness of 2 to 15 μm
And (c) Al 2 O 3 having an average layer thickness of 0.5 to 8 μm and a granular crystal structure, and having a composition formula based on an atomic ratio.
An aluminum oxide (hereinafter, referred to as Al 2 O 3 ) layer satisfying the following conditions, and a coated hard carbide tool obtained by chemical vapor deposition and / or physical vapor deposition of a hard coating layer composed of 3 to 25 μm with a total average layer thickness of 3 to 25 μm. It is known that this coated carbide tool is used for continuous cutting and interrupted cutting of steel, cast iron, and the like. It is also well known that, generally, those having an α-type crystal structure, those having a κ-type crystal structure, and the like are widely and practically used as the Al 2 O 3 layer constituting the hard coating layer of the coated carbide tool. And the above-mentioned l-TiC
The N layer is formed, for example, in Japanese Patent Application Laid-Open No.
It is known from, for example, 328808, and is formed by performing chemical vapor deposition in a normal chemical vapor deposition apparatus at a medium temperature range of 700 to 950 ° C. using a mixed gas containing an organic carbonitride as a reaction gas. It is. Note that the Ti compound layer and l-TiCN constituting the hard coating layer
Each layer has a relative atomic ratio of Ti to a nonmetallic component (C, N, and O components) of 1: 1 and relative atoms of C and N, C and O, and N and O, which are also nonmetallic components. The ratio is also 1: 1,
Furthermore, the relative atomic ratios of C, N and O are also 1: 1: 1 and therefore, the TiCN layer, TiCO layer, TiNO layer,
And the TiCNO layer are made of Ti (C 0.5 N
0. 5), Ti (C 0.5 O 0.5), Ti (N 0.5 O
0.5), and are those having a composition of Ti (C 0.33 C 0. 33 N 0.33), and those having a uniform composition throughout the layer thickness.
【０００３】[0003]
【発明が解決しようとする課題】一方、近年の切削加工
に対する省力化および省エネ化の要求は強く、これに伴
い、切削加工は高速化し、かつ高切り込みや高送りなど
の重切削化の傾向にあるが、上記の従来被覆超硬工具に
おいては、これの硬質被覆層を構成するｌ−ＴｉＣＮ層
が相対的に良好な靭性を具備することから、これによっ
て硬質被覆層も良好な靭性をもつようになり、高速切削
では切刃にチッピングなどの発生なく、すぐれた切削性
能を発揮するものであるが、切削条件が一段と苛酷にな
る、断続切削を高速で、かつ高切り込みや高送りなどの
重切削条件で行った場合には、未だ十分な靭性を具備す
るものでないために、切刃にチッピングが発生するのが
避けられず、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, there has been a strong demand for labor saving and energy saving for cutting work, and with this, cutting work has been accelerated and heavy cutting such as high cutting and high feed has been performed. However, in the above-mentioned conventional coated cemented carbide tool, the l-TiCN layer constituting the hard coating layer has relatively good toughness, so that the hard coating layer also has good toughness. In high-speed cutting, chipping does not occur on the cutting edge and excellent cutting performance is exhibited.However, cutting conditions become more severe, and intermittent cutting is performed at high speed and heavy cutting such as high cutting and high feed. When cutting is performed under cutting conditions, chipping does not yet have sufficient toughness, so that it is inevitable that chipping will occur on the cutting blade, and the service life will be reached in a relatively short time 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工具の硬質
被覆層を構成するｌ−ＴｉＣＮ層に着目し、これのもつ
耐摩耗性を損なうことなく、より一層の靭性向上を図る
べく研究を行った結果、ｌ−ＴｉＣＮ層の蒸着形成に際
して、まず下面部においてはＮ成分の濃度を相対的に高
くし（当然Ｃ成分の濃度は低くなる）、この状態から反
応ガス中の成分、例えばＣＨ3 ＣＮおよび／またはＣＨ
4 の含有割合を経時的に連続的あるいは段階的に変化さ
せて、前記下面部から層厚中間部にかけてＣ成分の濃度
を高くして行き（この結果Ｎ成分の濃度は相対的に低く
なる）、前記層厚中間部から前記上面部に向けては反対
にＣ成分の濃度を同じく反応ガス中のＣＨ3 ＣＮやＣＨ
4などの成分の含有割合を経時的に連続的あるいは段階
的に変化させて、漸次低減し、Ｎ成分が高くなる濃度勾
配を付与し、前記上面部では上記下面部におけると同様
にＮ成分がＣ成分に比して高い濃度をもつようにし、し
かもこの場合、上記上面部、上記層厚中間部、および上
記下面部が、原子比に基づく組成式：Ｔｉ（Ｃ1-x Ｎ
x ）で現した場合、上記上面部および上記下面部は、
ｘ：０．６５〜０．９５、上記層厚中間部は、ｘ：０．
０５〜０．３５、を満足する組成をもつものとすると、
この結果のｌ−ＴｉＣＮ層（以下、本発明ｌ−ＴｉＣＮ
層と云う）は、下面部から上面部までＣおよびＮ成分に
濃度変化のない一様な従来ｌ−ＴｉＣＮ層に比して、一
段とすぐれた靭性を具備するようになり、したがって前
記本発明ｌ−ＴｉＣＮ層が硬質被覆層を構成する被覆超
硬工具は、前記本発明ｌ−ＴｉＣＮ層によって前記硬質
被覆層自体がこれのもつ耐摩耗性が損なわれることな
く、一段とすぐれた靭性を具備するようになることか
ら、断続切削を高速で、かつ重切削で行うという、きわ
めて苛酷な切削条件でも切刃にチッピングの発生なく、
すぐれた切削性能を発揮するようになるという研究結果
を得たのである。Means for Solving the Problems Accordingly, the present inventors have
In view of the above, attention has been paid to the l-TiCN layer constituting the hard coating layer of the conventional coated carbide tool, and research has been conducted to further improve the toughness without impairing the wear resistance of the tool. As a result, when the l-TiCN layer is formed by vapor deposition, first, the concentration of the N component is relatively increased in the lower surface portion (the concentration of the C component is naturally reduced). 3 CN and / or CH
By changing the content ratio of 4 continuously or stepwise over time, the concentration of the C component is increased from the lower surface portion to the middle portion of the layer thickness (the concentration of the N component is relatively reduced). Conversely, the concentration of the C component is similarly changed from the intermediate portion of the layer thickness toward the upper surface portion to CH 3 CN or CH 3 in the reaction gas.
By changing the content ratio of the component such as 4 continuously or stepwise over time, the concentration is gradually reduced, and a concentration gradient in which the N component is increased is given. In this case, the upper surface portion, the intermediate layer thickness portion, and the lower surface portion have a composition formula based on an atomic ratio: Ti (C 1 -xN
x ), the upper surface and the lower surface are
x: 0.65 to 0.95;
Assuming that the composition satisfies the range of 0.5 to 0.35,
The resulting l-TiCN layer (hereinafter referred to as the present l-TiCN layer)
The layer of the present invention has much higher toughness than a conventional l-TiCN layer in which the concentration of C and N components does not change from the lower surface to the upper surface. -The coated carbide tool in which the TiCN layer constitutes the hard coating layer is such that the hard coating layer itself has more excellent toughness without the wear resistance of the hard coating layer itself being impaired by the l-TiCN layer of the present invention. Therefore, even under extremely severe cutting conditions of interrupted cutting at high speed and heavy cutting, chipping does not occur on the cutting edge,
The research results show that they will exhibit excellent cutting performance.
【０００５】この発明は、上記の研究結果に基づいてな
されたものであって、超硬基体の表面に、（ａ） いず
れも０．１〜５μｍの平均層厚および粒状結晶組織を有
する、ＴｉＣ層、ＴｉＮ層、ＴｉＣＮ層、ＴｉＣＯ層、
ＴｉＮＯ層、およびＴｉＣＮＯ層のうちの１種または２
種以上からなるＴｉ化合物層と、（ｂ） ２〜１５μｍ
の平均層厚のｌ−ＴｉＣＮ層と、（ｃ） ０．５〜８μ
ｍの平均層厚および粒状結晶組織を有するＡｌ2 Ｏ3 層
と、で構成された硬質被覆層を３〜２５μｍの全体平均
層厚で化学蒸着および／または物理蒸着してなる被覆超
硬工具において、上記硬質被覆層を構成するｌ−ＴｉＣ
Ｎ層を、これの上面部、層厚中間部、および下面部が、
原子比に基づく組成式：Ｔｉ（Ｃ1-x Ｎx ）で現した場
合、上記上面部および上記下面部は、ｘ：０．６５〜
０．９５、上記層厚中間部は、ｘ：０．０５〜０．３
５、を満足する組成を有し、かつＣおよびＮ成分濃度
が、上記下面部組成から上記層厚中間部組成に、また前
記層厚中間部組成から上記上面部組成に連続的および／
または段階的に変化する本発明ｌ−ＴｉＣＮ層で構成し
てなる、硬質被覆層がすぐれた耐チッピング性を発揮す
る被覆超硬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, and is based on the following facts: (a) TiC having an average layer thickness of 0.1 to 5 μm and a granular crystal structure Layer, TiN layer, TiCN layer, TiCO layer,
One or two of a TiNO layer and a TiCNO layer
A Ti compound layer comprising at least one species, and (b) 2 to 15 μm
(C) 0.5 to 8 μm
a hard coating layer composed of an Al 2 O 3 layer having an average layer thickness of m and a granular crystal structure, and a chemical vapor deposition and / or physical vapor deposition with a total average layer thickness of 3 to 25 μm. , L-TiC constituting the hard coating layer
The N layer has an upper surface portion, an intermediate layer thickness portion, and a lower surface portion,
When expressed by a composition formula based on an atomic ratio: Ti (C 1-x N x ), the upper surface portion and the lower surface portion have x: 0.65 to 0.65.
0.95, x: 0.05 to 0.3
And the C and N component concentrations are continuously and / or continuously from the lower surface composition to the intermediate layer thickness composition and from the intermediate layer thickness composition to the upper surface composition.
Alternatively, the present invention is characterized by a coated carbide tool having a hard coating layer, which is formed of a stepwise-varying l-TiCN layer of the present invention and exhibits excellent chipping resistance.
【０００６】なお、この発明の被覆超硬工具の硬質被覆
層を構成する本発明ｌ−ＴｉＣＮ層の組成式：Ｔｉ（Ｃ
1-x Ｎx ）におけるｘ値は、経験的に定めたものであっ
て、上記上面部および下面部のｘ値を０．６５〜０．９
５、望ましくは０．７０〜０．８５、上記上記層厚中間
部のｘ値を０．０５〜０．３５、望ましくは０．１５〜
０．３０としたのは、前記上面部および下面部のｘ値が
０．６５未満になったり、前記層厚中間部のｘ値が０．
３５を越えたりすると、層厚方向のＣおよびＮの濃度変
化が小さくなって一段の靭性向上効果が得られず、この
結果硬質被覆層に所望のすぐれた耐チッピング性を確保
することができず、一方前記上面部および下面部のｘ値
が０．９５を越えたり、前記層厚中間部のｘ値が０．０
５未満になったりすると、反対にＣおよびＮの濃度変化
が大きくなり過ぎて、縦長成長結晶組織を確保するのが
困難になり、靭性の著しい低下が避けられず、この結果
チッピングが発生し易くなるという理由に基ずくもので
ある。The composition formula of the 1-TiCN layer of the present invention constituting the hard coating layer of the coated carbide tool of the present invention: Ti (C
The x value in 1-xN x ) is empirically determined, and the x value of the upper surface portion and the lower surface portion is 0.65 to 0.9.
5, desirably 0.70 to 0.85, and the x value of the intermediate portion of the layer thickness is 0.05 to 0.35, desirably 0.15 to
The reason for setting the value to 0.30 is that the x value of the upper surface portion and the lower surface portion is less than 0.65, or the x value of the intermediate portion of the layer thickness is 0.1.
If it exceeds 35, the change in the concentration of C and N in the layer thickness direction becomes small, and a further improvement in toughness cannot be obtained. As a result, a desired excellent chipping resistance cannot be secured in the hard coating layer. On the other hand, the x value of the upper surface portion and the lower surface portion exceeds 0.95, or the x value of the intermediate layer thickness is 0.0
If it is less than 5, on the contrary, the change in the concentration of C and N becomes too large, and it becomes difficult to secure a vertically-grown crystal structure, and a remarkable decrease in toughness cannot be avoided. As a result, chipping tends to occur. It is based on the reason that it becomes.
【０００７】同じく硬質被覆層を構成するＴｉ化合物層
のそれぞれには、構成層相互間の層間密着性を向上させ
る作用があり、したがってその平均層厚が０．１μｍ未
満では、所望のすぐれた層間密着性を確保することがで
きず、一方その平均層厚が５μｍを越えると硬質被覆層
の摩耗進行が促進されるようになることから、その平均
層厚を０．１〜５μｍと定めた。同じくＡｌ2 Ｏ3 層に
は、硬質被覆層の耐摩耗性を向上させる作用があるが、
その平均層厚が０．５μｍ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８
μｍを越えると切刃にチッピングが発生し易くなること
から、その平均層厚を０．５〜８μｍと定めた。さらに
同じく本発明ｌ−ＴｉＣＮ層には、上記の通り硬質被覆
層の耐チッピング性を一段と向上させる作用があるが、
その平均層厚が２μｍ未満では、耐チッピング性に所望
の向上効果が得られず、一方その平均層厚が１５μｍを
越えると耐摩耗性が急激に低下するようになることか
ら、その平均層厚を２〜１５μｍと定めた。また、硬質
被覆層の全体平均層厚を３〜２５μｍとしたのは、その
平均層厚が３μｍ未満では、所望の耐摩耗性を確保する
ことができず、一方その平均層厚が２５μｍを越える
と、切刃に欠けやチッピングが発生し易くなるという理
由からである。Similarly, each of the Ti compound layers constituting the hard coating layer has an effect of improving interlayer adhesion between the constituent layers. Therefore, if the average layer thickness is less than 0.1 μm, a desired excellent interlayer thickness is obtained. Since the adhesion cannot be ensured, and if the average layer thickness exceeds 5 μm, the progress of wear of the hard coating layer is promoted, so the average layer thickness is set to 0.1 to 5 μm. Similarly, the Al 2 O 3 layer has an effect of improving the wear resistance of the hard coating layer,
If the average layer thickness is less than 0.5 μm, the desired excellent wear resistance cannot be secured, while the average layer thickness is 8 μm.
If the thickness exceeds μm, chipping is likely to occur on the cutting edge. Therefore, the average layer thickness is set to 0.5 to 8 μm. Furthermore, the l-TiCN layer of the present invention also has the effect of further improving the chipping resistance of the hard coating layer as described above,
If the average layer thickness is less than 2 μm, the desired effect of improving the chipping resistance cannot be obtained. On the other hand, if the average layer thickness exceeds 15 μm, the wear resistance rapidly decreases. Was determined to be 2 to 15 μm. In addition, the reason why the total average layer thickness of the hard coating layer is set to 3 to 25 μm is that if the average layer thickness is less than 3 μm, desired wear resistance cannot be secured, while the average layer thickness exceeds 25 μm. This is because the chipping and chipping of the cutting edge are likely to occur.
【０００８】[0008]
【発明の実施の形態】つぎに、この発明の被覆超硬工具
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：１．５μｍ有するＷＣ粉末、同１．２μｍの
（Ｔｉ，Ｗ）ＣＮ（重量比で、以下同じ、ＴｉＣ／Ｔｉ
Ｎ／ＷＣ＝２４／２０／５６）粉末、同１．３μｍの
（Ｔａ，Ｎｂ）Ｃ（ＴａＣ／ＮｂＣ＝９０／１０）粉
末、同１μｍのＣｒ3 Ｃ2 粉末、同１．２μｍのＶＣ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、この混合粉末をＩ
ＳＯ規格ＳＮＭＧ１２０４０８に則した形状の圧粉体に
プレス成形し、この圧粉体を１０-3ｔｏｒｒの真空雰囲
気中、１４００〜１４６０℃の範囲内の所定の温度に１
時間保持の条件で真空焼結することにより超硬基体Ａ〜
Ｆをそれぞれ製造した。DETAILED DESCRIPTION OF THE PREFERRED EMBODIMENTS Next, the coated carbide tool of the present invention will be specifically described with reference to examples. As raw material powder, WC powder having an average particle diameter of 1.5 μm, (Ti, W) CN of the same 1.2 μm (the same in weight ratio, hereinafter TiC / Ti
N / WC = 24/20/56) powder, 1.3 μm (Ta, Nb) C (TaC / NbC = 90/10) powder, 1 μm Cr 3 C 2 powder, 1.2 μm VC powder , And 1.2 μm of the same Co powder were prepared, and these raw material powders were mixed in the compounding composition shown in Table 1, wet-mixed in a ball mill for 72 hours, and dried.
The green compact is press-formed into a green compact having a shape conforming to SO standard SNMG120408, and the green compact is heated to a predetermined temperature within a range of 1400 to 1460 ° C. in a vacuum atmosphere of 10 −3 torr.
Carbide substrate A ~
F were each manufactured.
【０００９】ついで、これらの超硬基体Ａ〜Ｆの表面
に、ホーニング加工を施した状態で、通常の化学蒸着装
置を用い、表２、３（表２に示される硬質被覆層の構成
層は、いずれも層の下面部から上面部まで構成成分に濃
度変化のない一様な組成をもつものであり、またｌ−Ｔ
ｉＣＮ層以外はいずれも粒状結晶組織を有するものであ
る）に示される条件にて、表４〜６に示される目標組成
および目標層厚（切刃の逃げ面）の硬質被覆層を形成す
ることにより本発明被覆超硬工具１〜１０および従来被
覆超硬工具１〜１０をそれぞれ製造した。なお、表５に
おいて、例えば本発明ｌ−ＴｉＣＮ（ａ）は、下面部、
層厚中間部、および上面部の目標組成をそれぞれＴｉ
（Ｃ1-0.70Ｎ0.70）、Ｔｉ（Ｃ1-0. 05Ｎ0.05）、および
Ｔｉ（Ｃ1-0.75Ｎ0.75）と設定し、これらの目標組成の
形成を表３に示される条件で行い、一方前記下面部から
層厚：２．２μｍの位置の前記層厚中間部まで、さらに
前記層厚中間部から前記上面部までの組成変化はいずれ
も反応ガス中のＣＨ3 ＣＮおよび／またはＣＨ4 の含有
割合を経時的に連続的に変化させて行い、かつ全体目標
層厚を３．８μｍとする条件で形成することを示すもの
である。この結果得られた本発明被覆超硬工具１〜１０
の硬質被覆層を構成する本発明ｌ−ＴｉＣＮ層（ａ）〜
（ｊ）のそれぞれについて、下面部、層厚中間部、およ
び上面部の組成ｘ値を、下面部および上面部はそれぞれ
の表面から０．２μｍ内側を、また層厚中間部は該当箇
所をオージェ分光分析器を用いて測定したところ、表５
に示される目標値に相当する値を示した。また、本発明
被覆超硬工具１〜１０および従来被覆超硬工具１〜１０
の硬質被覆層の構成層のそれぞれの平均層厚を測定した
ところ、目標層厚と実質的に同じ値を示した。Then, the surfaces of these super-hard substrates A to F are subjected to honing processing, and a conventional chemical vapor deposition apparatus is used. Have a uniform composition with no change in the concentration of the constituent components from the lower surface to the upper surface of the layer.
The hard coating layer having the target composition and the target layer thickness (the flank of the cutting edge) shown in Tables 4 to 6 is formed under the conditions shown in Tables 4 to 6 except for the iCN layer. Produced coated carbide tools 1 to 10 of the present invention and conventional coated carbide tools 1 to 10 respectively. In Table 5, for example, 1-TiCN (a) of the present invention has a lower surface portion,
The target composition of the middle part of the layer
(C 1-0.70 N 0.70), Ti (C 1-0. 05 N 0.05), and set the Ti (C 1-0.75 N 0.75), performed in the formation of these target composition under the conditions shown in Table 3 On the other hand, the composition change from the lower surface portion to the intermediate layer thickness at a position of the layer thickness: 2.2 μm, and further from the intermediate layer thickness to the upper surface portion, is CH 3 CN and / or CH 3 This shows that the formation is performed by changing the content ratio of 4 continuously with time, and that the total target layer thickness is 3.8 μm. The coated carbide tools 1 to 10 of the present invention obtained as a result
1-TiCN layer (a) of the present invention constituting a hard coating layer of
For each of (j), the composition x value of the lower surface portion, the intermediate layer thickness portion, and the upper surface portion, the lower surface portion and the upper surface portion are 0.2 μm inward from the respective surfaces, and the intermediate layer thickness portion is the Auger. Table 5 shows the results of measurement using a spectrometer.
The values corresponding to the target values shown in FIG. Further, the coated carbide tools 1 to 10 of the present invention and the conventionally coated carbide tools 1 to 10
The average layer thickness of each of the constituent layers of the hard coating layer was measured and found to be substantially the same as the target layer thickness.
【００１０】つぎに、上記本発明被覆超硬工具１〜１０
および従来被覆超硬工具１〜１０について、 被削材：ＣＮＣＭ４３９の長さ方向等間隔４本縦溝入り
丸棒、 切削速度：３００ｍ／ｍｉｎ．、 切り込み：５．０ｍｍ、 送り：０．３ｍｍ／ｒｅｖ．、 切削時間：１５分、 の条件での合金鋼の乾式高速高切り込み断続切削試験、
並びに、 被削材：ＣＮＣＭ４３９の長さ方向等間隔４本縦溝入り
丸棒、 切削速度：３００ｍ／ｍｉｎ．、 切り込み：１．５ｍｍ、 送り：０．６ｍｍ／ｒｅｖ．、 切削時間：１０分、 の条件での合金鋼の乾式高速高送り断続切削試験行い、
いずれの切削試験でも切刃の最大逃げ面摩耗幅を測定し
た。この測定結果を表７に示した。Next, the coated carbide tools 1 to 10 according to the present invention will be described.
And conventional coated carbide tools 1 to 10, Work material: CNCM439, lengthwise round bar with four longitudinal grooves, Cutting speed: 300 m / min. Infeed: 5.0 mm Feed: 0.3 mm / rev. , Cutting time: 15 minutes, Dry high-speed high-cut intermittent cutting test of alloy steel under the following conditions:
Work material: CNCM439 lengthwise round bar with four equally spaced longitudinal grooves, Cutting speed: 300 m / min. Infeed: 1.5 mm Feed: 0.6 mm / rev. , Cutting time: 10 minutes, Dry high-speed high feed intermittent cutting test of alloy steel under the conditions of
In each cutting test, the maximum flank wear width of the cutting edge was measured. Table 7 shows the measurement results.
【００１１】[0011]
【表１】 [Table 1]
【００１２】[0012]
【表２】 [Table 2]
【００１３】[0013]
【表３】 [Table 3]
【００１４】[0014]
【表４】 [Table 4]
【００１５】[0015]
【表５】 [Table 5]
【００１６】[0016]
【表６】 [Table 6]
【００１７】[0017]
【表７】 [Table 7]
【００１８】[0018]
【発明の効果】表４〜７に示される結果から、硬質被覆
層中に層厚方向にそってＣおよびＮ成分が濃度変化する
本発明ｌ−ＴｉＣＮ層が存在する本発明被覆超硬工具１
〜１０は、いずれも前記本発明ｌ−ＴｉＣＮ層によって
硬質被覆層がすぐれた靭性を具備するようになることか
ら、鋼の断続切削を高速で、しかも高切り込みおよび高
送りの重切削条件で行うというきわめて苛酷な切削条件
下でも切刃にチッピングの発生なく、すぐれた切削性能
を発揮するのに対して、硬質被覆層を構成するｌ−Ｔｉ
ＣＮ層のＣおよびＮ成分に層厚方向の濃度変化がない従
来被覆超硬工具１〜１０においては、上記の苛酷な切削
条件では硬質被覆層の靭性不足が原因で切刃にチッピン
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工具は、
これを構成する硬質被覆層がすぐた耐チッピング性を有
するので、例えば鋼や鋳鉄などの通常の条件での連続切
削や断続切削は勿論のこと、特にこ断続切削を高速で、
かつ重切削条件下で行うというきわめて苛酷な条件での
切削でも、長期に亘ってすぐれた切削性能を発揮するも
のであるから、切削加工の省力化および省エネ化に十分
満足に対応できるものである。From the results shown in Tables 4 to 7, it can be seen from the results shown in Tables 4 to 7 that the coated carbide tool of the present invention 1 in which the l-TiCN layer of the present invention in which the concentration of C and N components changes in the thickness of the hard coating layer exists
In Nos. 10 to 10, since the hard coating layer has excellent toughness due to the l-TiCN layer of the present invention, intermittent cutting of steel is performed at a high speed, and at high cutting and high feed under heavy cutting conditions. Under extremely severe cutting conditions, the cutting edge does not generate chipping and exhibits excellent cutting performance, whereas l-Ti constituting the hard coating layer
In the conventional coated carbide tools 1 to 10 in which the C and N components of the CN layer do not have a concentration change in the layer thickness direction, chipping occurs on the cutting edge due to insufficient toughness of the hard coating layer under the above severe cutting conditions. It is clear that the service life can be reached in a relatively short time. As described above, the coated carbide tool of the present invention
Since the hard coating layer that constitutes it has excellent chipping resistance, it can be used not only for continuous cutting and interrupted cutting under normal conditions such as steel or cast iron, but also especially for interrupted cutting at high speed.
In addition, even when cutting under extremely severe conditions, such as under heavy cutting conditions, it exhibits excellent cutting performance over a long period of time, so it can sufficiently respond to labor saving and energy saving in cutting work. .
───────────────────────────────────────────────────── フロントページの続き (72)発明者 見市 昌之 茨城県結城郡石下町大字古間木1511番地 三菱マテリアル株式会社筑波製作所内 Ｆターム(参考） 3C046 FF03 FF10 FF16 FF19 FF22 FF25 FF32 FF40 FF42 4K029 BA41 BA44 BA54 BA56 BA60 BB02 BB07 BC00 BD05 EA01 4K030 BA35 BA36 BA38 BA41 BA43 BB01 BB12 CA03 JA01 LA01 LA22 ────────────────────────────────────────────────── ─── Continued on the front page (72) Inventor Masayuki Miichi 1511 Furamagi, Ishishita-cho, Yuki-gun, Ibaraki Pref. BA44 BA54 BA56 BA60 BB02 BB07 BC00 BD05 EA01 4K030 BA35 BA36 BA38 BA41 BA43 BB01 BB12 CA03 JA01 LA01 LA22
Claims (1)
に、 いずれも０．１〜５μｍの平均層厚および粒状結晶組織
を有する、炭化チタン層、窒化チタン層、炭窒化チタン
層、炭酸化チタン層、窒酸化チタン層、および炭窒酸化
チタン層のうちの１種または２種以上からなるＴｉ化合
物層と、 ２〜１５μｍの平均層厚および縦長成長結晶組織を有す
る炭窒化チタン層と、 ０．５〜８μｍの平均層厚および粒状結晶組織を有する
を有する酸化アルミニウム層と、で構成された硬質被覆
層を３〜２５μｍの全体平均層厚で化学蒸着および／ま
たは物理蒸着してなる、表面被覆超硬合金製切削工具に
おいて、 上記硬質被覆層を構成する縦長成長結晶組織の炭窒化チ
タン層を、これの上面部、層厚中間部、および下面部
が、原子比に基づく組成式：Ｔｉ（Ｃ1-x Ｎx ）で現し
た場合、 上記上面部および上記下面部は、ｘ：０．６５〜０．９
５、 上記層厚中間部は、ｘ：０．０５〜０．３５、を満足す
る組成を有し、かつＣおよびＮ成分濃度が、上記下面部
組成から上記層厚中間部組成に、また前記層厚中間部組
成から上記上面部組成に連続的および／または段階的に
変化する縦長成長結晶組織の炭窒化チタン層で構成した
ことを特徴とする硬質被覆層がすぐれた耐チッピング性
を発揮する表面被覆超硬合金製切削工具。1. A titanium carbide layer, a titanium nitride layer, a titanium carbonitride layer, and a titanium carbonate, each having an average layer thickness of 0.1 to 5 μm and a granular crystal structure on the surface of a tungsten carbide-based cemented carbide substrate. A Ti compound layer comprising one or more of a titanium nitride layer, a titanium oxynitride layer, and a titanium carbonitride layer; a titanium carbonitride layer having an average layer thickness of 2 to 15 μm and a vertically elongated crystal structure; An aluminum oxide layer having an average layer thickness and a granular crystal structure of 0.5 to 8 μm, and a hard coating layer formed by chemical vapor deposition and / or physical vapor deposition with a total average layer thickness of 3 to 25 μm. In a coated cemented carbide cutting tool, a titanium carbonitride layer having a vertically-grown crystal structure constituting the hard coating layer is formed such that an upper surface portion, an intermediate layer thickness portion, and a lower surface portion have a composition formula based on an atomic ratio: Ti When expressed as (C 1-x N x ), the upper surface portion and the lower surface portion are x: 0.65 to 0.9.
5. The intermediate layer thickness has a composition that satisfies x: 0.05 to 0.35, and the C and N component concentrations are changed from the lower surface composition to the intermediate layer thickness composition. The hard coating layer, which is composed of a titanium carbonitride layer having a vertically-grown crystal structure that changes continuously and / or stepwise from the composition in the middle of the layer thickness to the composition in the upper surface, exhibits excellent chipping resistance. Surface coated cemented carbide cutting tool.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP10371997A JP2000190105A (en) | 1998-12-28 | 1998-12-28 | Cutting tool made of surface coating cemented carbide having hard coating layer exhibiting good chipping resistance |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP10371997A JP2000190105A (en) | 1998-12-28 | 1998-12-28 | Cutting tool made of surface coating cemented carbide having hard coating layer exhibiting good chipping resistance |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| JP2000190105A true JP2000190105A (en) | 2000-07-11 |
Family
ID=18499668
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP10371997A Withdrawn JP2000190105A (en) | 1998-12-28 | 1998-12-28 | Cutting tool made of surface coating cemented carbide having hard coating layer exhibiting good chipping resistance |
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| Country | Link |
|---|---|
| JP (1) | JP2000190105A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2002154001A (en) * | 2000-09-07 | 2002-05-28 | Ngk Spark Plug Co Ltd | Cutting tool |
-
1998
- 1998-12-28 JP JP10371997A patent/JP2000190105A/en not_active Withdrawn
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2002154001A (en) * | 2000-09-07 | 2002-05-28 | Ngk Spark Plug Co Ltd | Cutting tool |
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