JPH081409A - Cutting tool made of surface-covered tungsten carbide base cemented carbide having excellent in-layer adhesion of hard covered layer - Google Patents
Cutting tool made of surface-covered tungsten carbide base cemented carbide having excellent in-layer adhesion of hard covered layerInfo
- Publication number
- JPH081409A JPH081409A JP6156843A JP15684394A JPH081409A JP H081409 A JPH081409 A JP H081409A JP 6156843 A JP6156843 A JP 6156843A JP 15684394 A JP15684394 A JP 15684394A JP H081409 A JPH081409 A JP H081409A
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- Prior art keywords
- layer
- cemented carbide
- titanium
- carbide
- crystal structure
- Prior art date
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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）からなる第１層、炭窒化チタン
（以下、ＴｉＣＮで示す）からなる第２層、炭化チタン
（以下、ＴｉＣで示す）からなる第３層、および酸化ア
ルミニウム（以下、Ａｌ2 Ｏ3 で示す）からなる第４
層、さらに必要に応じてＴｉＮからなる第５層で構成さ
れた硬質被覆層を３〜３０μｍの範囲内の所定の平均層
厚で形成してなる被覆超硬切削工具が、主に合金鋼や鋳
鉄の旋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 or physical vapor deposition, the first layer of titanium nitride (hereinafter, TiN), the second layer of titanium carbonitride (hereinafter, TiCN), titanium carbide. A third layer made of (hereinafter referred to as TiC) and a fourth layer made of aluminum oxide (hereinafter referred to as Al 2 O 3 )
Layer, and if necessary, a hard coating layer composed of a fifth layer made of TiN with a predetermined average layer thickness within a range of 3 to 30 μm is mainly used for alloy steel or alloy steel. It is well known that it is used for turning and milling cast iron.
【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
の密着性に問題はないが、前記第１層と第２層のＴｉＣ
Ｎ層、前記第２層と第３層のＴｉＣ層、および前記第３
層と第４層のＡｌ2 Ｏ3 層、さらに前記第４層と第５層
のＴｉＮ層の層間密着性がいずれも低く、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、および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こと。 （ｃ） 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２層のＴｉＣＮ層を縦長成長結晶組織
とし、かつ第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、または実質的にカッパー型結晶からなる組織）とす
ると、この結果の硬質被覆層はいずれの層間密着性も著
しく向上したものになり、したがって切削抵抗の高い被
削材の切削にも層間剥離のチッピングの発生がなく、す
ぐれた切削性能を長期に亘って発揮すること。 （ｄ） 上記（ｃ）の硬質被覆層の第２層を構成する縦
長成長結晶組織を有するＴｉＣＮ層を１層または２層以
上の粒状結晶組織を有するＴｉＮ層で複数層に分割す
る、すなわち前記ＴｉＮ分割層の上下両面側に前記Ｔｉ
ＣＮ区分層が存在する構造をもつものにすると、特に高
送り切削や高切込み切削などの重切削での切刃の耐欠損
性が著しく向上するようになること。 以上（ａ）〜（ｄ）に示される研究結果を得たのであ
る。Therefore, the present inventors have
From the above-mentioned viewpoint, the above-mentioned conventional coated carbide cutting tool was focused on, and a study was conducted to improve the interlayer adhesion of the hard coating layer constituting the cutting tool. In the hard coating layer constituting the cutting tool, there is no problem in the adhesion of the first TiN layer to the cemented carbide substrate, but the TiC of the first layer and the second layer
The N layer, the second and third TiC layers, and the third layer
The interlayer adhesion between the first layer and the fourth Al 2 O 3 layer, and further between the fourth and fifth TiN layers, is low, which easily causes 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 layer, the TiC layer of the third layer, and the TiN layer of the fifth layer formed as necessary all have a granular crystal structure, and
The Al 2 O 3 layer of the layer has an alpha-type crystal structure. (C) In the hard coating layer constituting the above conventional coated carbide cutting tool, the second TiCN layer has a vertically elongated crystal structure, and the fourth Al 2 O 3 layer mainly has a copper crystal. Assuming that the structure has a structure (preferably, a structure in which a copper type crystal occupies 50% by volume or more, and the balance is an alpha type crystal, or a structure in which a copper type crystal is substantially formed), the resulting hard coating layer has any layer structure. Adhesion is also significantly improved, so even when cutting a work material with high cutting resistance, delamination chipping does not occur and excellent cutting performance is exhibited over a long period of time. (D) The TiCN layer having a vertically elongated crystal structure that constitutes the second layer of the hard coating layer of (c) is divided into a plurality of layers by one or more TiN layers having a granular crystal structure, that is, The Ti is formed on both the upper and lower sides of the TiN dividing layer.
When the structure having the CN division layer is present, the fracture resistance of the cutting edge is remarkably improved particularly in heavy cutting such as high feed cutting and high depth cutting. The research results shown in (a) to (d) 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、粒状結
晶組織を有するＴｉＮからなる第１層、同じく粒状結晶
組織を有するＴｉＣＮからなる第２層、同じく粒状結晶
組織を有するＴｉＣからなる第３層、およびアルファ型
結晶組織を有するＡｌ2 Ｏ3 からなる第４層、さらに必
要に応じて形成される粒状結晶組織を有するＴｉＮから
なる第５層で構成された硬質被覆層を、通常の化学蒸着
法および／または物理蒸着法を用い、３〜３０μｍの範
囲内の所定の平均層厚で形成してなる被覆超硬切削工具
において、上記第２層を、粒状結晶組織を有する１層ま
たは２層以上のＴｉＮ分割層で区分された複数の縦長成
長結晶組織を有するＴｉＣＮ区分層からなるもののＴｉ
ＣＮ層を縦長成長結晶組織とし、かつ第４層のＡｌ2 Ｏ
3 層をカッパ型結晶を主体とした組織とすることにより
硬質被覆層の層間密着性を向上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, and comprises a first layer of TiN having a granular crystal structure on the surface of a cemented carbide substrate, and TiCN also having a granular crystal structure. A second layer, a third layer made of TiC which also has a granular crystal structure, a fourth layer made of Al 2 O 3 having an alpha type crystal structure, and TiN having a granular crystal structure formed as necessary. In a coated carbide cutting tool formed by forming a hard coating layer composed of a fifth layer by a normal chemical vapor deposition method and / or physical vapor deposition method to a predetermined average layer thickness within a range of 3 to 30 μm, The second layer is composed of a TiCN partition layer having a plurality of vertically elongated crystal structures partitioned by one or more TiN partition layers having a granular crystal structure.
The CN layer has a vertically elongated crystal structure and the fourth layer of Al 2 O
A characteristic feature of the coated carbide cutting tool is that the three layers have a structure mainly composed of kappa-type crystals to improve the interlayer adhesion of the hard coating layer.
【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層を構成する縦長成長結晶
組織を有するＴｉＣＮ区分層は、例えば特開平６−８０
１０号公報に記載される通り、 反応ガス組成：容量％で、ＴｉＣｌ4 ：１〜１０％、Ｃ
Ｈ3 ＣＮ：０．１〜５％、Ｎ2 ：０〜３５％、Ｈ2 ：残
り、 反応温度：８５０〜９５０℃、 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、 反応ガス組成：容量％で、ＴｉＣｌ4 ：１〜５％、ＣＨ
4 ：２〜７％、Ｎ2 ：１５〜３５％、Ｈ2 ：残り、 反応温度：９５０〜１０５０℃、 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、 反応ガス：容量％で、初期段階の１〜１２０分を、Ａｌ
Ｃｌ3 ：１〜２０％、必要に応じて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％、必要に応じてＨＣｌ：１〜２０％および／ま
たはＨ2 Ｓ：０．０５〜５％、Ｈ2 ：残り、 反応温度：８５０〜１０００℃、 雰囲気圧力：３０〜２００torr、 の条件で形成される。A TiCN partition layer having a vertically elongated crystal structure, which constitutes the second layer of the hard coating layers constituting the coated cemented carbide cutting tool of the present invention, is disclosed in, for example, JP-A-6-80.
As described in Japanese Patent Publication No. 10, the reaction gas composition: volume%, TiCl 4 : 1 to 10%, C
H 3 CN: 0.1 to 5%, N 2 : 0 to 35%, H 2 : residual, reaction temperature: 850 to 950 ° C., atmospheric pressure: 30 to 200 torr. On the other hand, a TiCN layer having a granular crystal structure usually has a reaction gas composition: volume%, TiCl 4 : 1 to 5%, CH
4: 2~7%, N 2: 15~35%, H 2: remainder, reaction temperature: 950 to 1050 ° C., atmospheric pressure: 30～200Torr, is formed by the conditions. Further, the Al 2 O 3 layer having a structure mainly composed of a copper-type crystal is composed of a reaction gas: volume% and an Al phase of 1 to 120 minutes in the initial stage.
Cl 3: 1-20%, HCl if necessary: 1-20%
And / or H 2 S: 0.05~5%, H 2: remainder,
Thereafter, AlCl 3 : 1 to 20%, CO 2 : 0.5
-30%, if necessary HCl: 1-20% and / or H 2 S: 0.05-5%, H 2 : remaining, reaction temperature: 850-1000 ° C., atmospheric pressure: 30-200 torr, conditions Is formed by.
【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、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区分層と
ＴｉＮ区分層、第３層のＴｉＣ層、および第４層のＡｌ
2 Ｏ3 層、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り、この場合の
第１層は硬質被覆層形成後ＴｉＣＮ層として存在するこ
とになる。In the hard coating layer constituting the coated cemented carbide cutting tool of the present invention, the TiN layer of the first layer is first deposited on the surface of the cemented carbide substrate, and then the TiCN section layer of the second layer and the TiN layer. Partition layer, third layer TiC layer, and fourth layer Al
It is formed by sequentially depositing a 2 O 3 layer and, if necessary, a TiN layer of a fifth layer. When forming the second and subsequent layers, the cemented carbide substrate is added to the TiN layer of the first layer. In some cases, the C component therein may be solid-dissolved as a solid solution, and in this case, the first layer exists as a TiCN layer after the hard coating layer is formed.
【０００８】さらに、上記硬質被覆層の平均層厚は３〜
３０μｍとするのがよく、これは、その平均層厚が３μ
ｍ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０．１〜５μ
ｍ、第２層のＴｉＣＮ区分層およびＴｉＮ分割層のそれ
は３〜２０μｍおよび０．１〜５μｍ、第３層のＴｉＣ
層は１〜１０μｍ、第４層のＡｌ2 Ｏ3 層は０．１〜１
５μｍ、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 hard coating layer has an average layer thickness of 3 to 3.
Preferably, the average layer thickness is 3 μm.
If the average layer thickness is less than 30 μm, the chipping resistance will rapidly decrease, and if the average layer thickness exceeds 30 μm, the first layer will not be able to secure desired wear resistance. The average thickness of the TiN layer is 0.1 to 5 μm.
m of the second TiCN partition layer and that of the TiN partition layer are 3 to 20 μm and 0.1 to 5 μm, and the third layer of TiC.
The layer is 1 to 10 μm, and the fourth Al 2 O 3 layer is 0.1 to 1
The average thickness of the TiN layer of 5 μm and the fifth layer is preferably 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、同１．３μｍの（Ｔａ，Ｎｂ）Ｃ（Ｔ
ａＣ／ＮｂＣ＝９０／１０）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、ＩＳＯ・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に示される条件に真空焼結する
ことにより超硬合金基体Ａ〜Ｅを製造した。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、徐冷の滲炭
処理を施し、処理後、基体表面に付着するカーボンとＣ
ｏを酸およびバレル研磨で除去することにより、表面か
ら１０μｍの位置で最大Ｃｏ含有量：１５重量％、深
さ：４０μｍのＣｏ富化帯域を基体表層部に形成した。
また、上記超硬合金基体ＡおよびＤには、焼結したまま
で、表層部に表面から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Ｃ
ｏ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（ロックウエル硬さ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, 1.3 μm (Ta, Nb) C (T
aC / NbC = 90/10) powder and 1.2 μm
Are prepared, and these raw material powders are blended in the composition shown in Table 1, and wet-mixed for 72 hours by a ball mill.
After being dried, it is press-molded into a green compact having a shape defined by ISO / CNMG120408 (for cemented carbide base bodies A to D) and SEEN42AFTN1 (for cemented carbide base body E),
Cemented carbide base bodies A to E were manufactured by vacuum-sintering the green compact under the conditions shown in Table 1. Further, the cemented carbide substrate B is kept in a 100 torr CH 4 gas atmosphere at a temperature of 1400 ° C. for 1 hour, and then subjected to a slow cooling carburizing treatment. After the treatment, carbon and carbon adhering to the substrate surface are removed.
By removing o by acid and barrel polishing, a Co-enriched zone having a maximum Co content of 15% by weight and a depth of 40 μm was formed at a position 10 μm from the surface in the surface layer portion of the substrate.
In the cemented carbide substrates A and D, a Co-enriched zone having a maximum Co content of 9% by weight and a depth of 20 μm was formed on the surface layer at a position 15 μm from the surface while being sintered. The remaining cemented carbide substrates C and E have the above C
o There was no formation of enriched zones, and there was an overall homogeneous structure. Further, Table 1 shows that the cemented carbide substrates A to E
Of each sample (Rockwell hardness A scale).
【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３〜７に示される組
成および結晶組織、さらに平均層厚の硬質被覆層を形成
することにより本発明被覆超硬切削工具１〜７および従
来被覆超硬切削工具１〜７をそれぞれ製造した。つぎ
に、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：１８０ｍ／min.、 送り：０．４２mm／rev.、 切込み：２mm、 切削時間：３０min.、 の条件での軟鋼の高送り連続切削試験、および、 被削材：軟鋼の丸棒、 切削速度：１８０ｍ／min.、 送り：０．２７mm／rev.、 切込み：４mm、 切削時間：４０min.、 の条件での軟鋼の高切込み連続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５，７に示した。また、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については、 被削材：軟鋼の角材、 切削速度：２３０ｍ／min.、 送り：０．３７mm／刃、 切込み：３mm、 切削時間：４０min.、 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５，７に示した。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 7 The coated carbide cutting tools 1 to 7 of the present invention and the coated carbide cutting tools 1 to 7 of the related art were manufactured by forming a crystal structure and a hard coating layer having an average layer thickness. Next, regarding the above-mentioned coated carbide cutting tools 1 to 5 of the present invention and conventional coated carbide cutting tools 1 to 5, work material: round bar of mild steel, cutting speed: 180 m / min., Feed: 0.42 mm / rev ., Depth of cut: 2 mm, cutting time: 30 min., High-feed continuous cutting test of mild steel, and work material: round bar of mild steel, cutting speed: 180 m / min., Feed: 0.27 mm / rev ., Depth of cut: 4 mm, cutting time: 40 min.
In each cutting test, the flank wear width of the cutting edge was measured.
The results of these measurements are shown in Tables 5 and 7. Further, regarding the above-mentioned coated carbide cutting tools 6 and 7 of the present invention and conventional coated carbide cutting tools 6 and 7, the work material is a square piece of mild steel, the cutting speed is 230 m / min., The feed is 0.37 mm / blade, Milling of mild steel was performed under the following conditions: depth of cut: 3 mm, cutting time: 40 min, and the flank wear width of the cutting edge was measured. The measurement results are also shown in Tables 5 and 7.
【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３〜７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 7, 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.
Claims (2)
合金基体、または表層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、粒状結晶組織を
有する窒化チタンからなる第１層、同じく粒状結晶組織
を有する炭窒化チタンからなる第２層、同じく粒状結晶
組織を有する炭化チタンからなる第３層、およびアルフ
ァ型結晶組織を有する酸化アルミニウムからなる第４層
で構成された硬質被覆層を３〜３０μｍの範囲内の所定
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、 上記第２層を、粒状結晶組織を有する１層または２層以
上の窒化チタン分割層で区分された複数の縦長成長結晶
組織を有する炭窒化チタン区分層からなるものとし、か
つ上記第４層の酸化アルミニウム層をカッパー型結晶を
主体とした組織と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 titanium carbide-based cemented carbide substrate that is wholly homogeneous, or a titanium carbide-based cemented carbide substrate that has a binder phase enriched zone in the surface layer and is made of titanium nitride having a granular crystal structure. One layer, a second layer made of titanium carbonitride having the same grain structure, a third layer made of titanium carbide having the same grain structure, and a fourth layer made of aluminum oxide having an alpha crystal structure. A surface-coated tungsten carbide-based cemented carbide cutting tool comprising a hard coating layer having a predetermined average layer thickness within the range of 3 to 30 μm, wherein the second layer is one layer or two layers having a granular crystal structure. The titanium carbonitride partition layer having a plurality of vertically elongated crystal structures partitioned by the titanium nitride partition layer is used, and the fourth aluminum oxide layer is a kappa layer. A surface-coated tungsten carbide based cemented carbide cutting tool having an excellent interlaminar adhesion of a hard coating layer, which is characterized by having a structure mainly composed of -type crystals.
合金基体、または表層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、粒状結晶組織を
有する窒化チタンからなる第１層、同じく粒状結晶組織
を有する炭窒化チタンからなる第２層、同じく粒状結晶
組織を有する炭化チタンからなる第３層、アルファ型結
晶組織を有する酸化アルミニウムからなる第４層、およ
び粒状結晶組織を有する窒化チタンからなる第５層で構
成された硬質被覆層を３〜３０μｍの範囲内の所定の平
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、 上記第２層を、粒状結晶組織を有する１層または２層以
上の窒化チタン分割層で区分された複数の縦長成長結晶
組織を有する炭窒化チタン区分層からなるものの炭窒化
チタン層を縦長成長結晶組織とし、かつ上記第４層の酸
化アルミニウム層をカッパー型結晶を主体とした組織と
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 carbide-based cemented carbide substrate that is wholly homogeneous, or a titanium carbide-based cemented carbide substrate that has a binder phase-enriched zone in the surface layer. One layer, a second layer made of titanium carbonitride having the same granular crystal structure, a third layer made of titanium carbide having the same granular crystal structure, a fourth layer made of aluminum oxide having an alpha type crystal structure, and a granular crystal structure. A surface-coated tungsten carbide-based cemented carbide cutting tool comprising a hard coating layer composed of a fifth layer of titanium nitride having a predetermined average layer thickness within the range of 3 to 30 μm. The layer is composed of a titanium carbonitride partition layer having a plurality of vertically elongated crystal structures partitioned by one or more titanium nitride partition layers having a granular crystal structure. A surface-coated carbonized hard coating layer having excellent interlayer adhesion, characterized in that the titanium carbonitride layer has a vertically elongated crystal structure and the fourth aluminum oxide layer has a structure mainly composed of copper crystals. Cutting tool made of tungsten-based cemented carbide.
Priority Applications (7)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP15684394A JP3230373B2 (en) | 1994-06-15 | 1994-06-15 | Surface-coated tungsten carbide-based cemented carbide cutting tool with excellent interlayer adhesion and fracture resistance with a hard coating layer |
| US08/398,533 US5920760A (en) | 1994-05-31 | 1995-03-06 | Coated hard alloy blade member |
| DE69518039T DE69518039T2 (en) | 1994-05-31 | 1995-03-08 | Coated carbide alloy blade |
| EP95103339A EP0685572B1 (en) | 1994-05-31 | 1995-03-08 | Coated hard-alloy blade member |
| KR1019950006333A KR0163654B1 (en) | 1994-05-31 | 1995-03-24 | Coated hard alloy blade member |
| CN95103640A CN1070540C (en) | 1994-05-31 | 1995-04-06 | Coated hard alloy blade member |
| US09/210,460 US6093479A (en) | 1994-05-31 | 1998-12-14 | Coated hard alloy blade member |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP15684394A JP3230373B2 (en) | 1994-06-15 | 1994-06-15 | Surface-coated tungsten carbide-based cemented carbide cutting tool with excellent interlayer adhesion and fracture resistance with a hard coating layer |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPH081409A true JPH081409A (en) | 1996-01-09 |
| JP3230373B2 JP3230373B2 (en) | 2001-11-19 |
Family
ID=15636592
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP15684394A Expired - Lifetime JP3230373B2 (en) | 1994-05-31 | 1994-06-15 | Surface-coated tungsten carbide-based cemented carbide cutting tool with excellent interlayer adhesion and fracture resistance with a hard coating layer |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP3230373B2 (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR20240050371A (en) | 2021-10-15 | 2024-04-18 | 제이에프이 스틸 가부시키가이샤 | Aging treatment method and manufacturing method of grain-oriented electrical steel sheet |
-
1994
- 1994-06-15 JP JP15684394A patent/JP3230373B2/en not_active Expired - Lifetime
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR20240050371A (en) | 2021-10-15 | 2024-04-18 | 제이에프이 스틸 가부시키가이샤 | Aging treatment method and manufacturing method of grain-oriented electrical steel sheet |
Also Published As
| Publication number | Publication date |
|---|---|
| JP3230373B2 (en) | 2001-11-19 |
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