JP2014091169A - Surface-coated cutting tool - Google Patents
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Abstract
Description
本発明は、表面被覆切削工具（以下、被覆工具という）に関し、さらに詳しくは、例えば、軟鋼、一般鋼、高硬度鋼等を、高熱発生を伴うとともに切刃部に対して大きな機械的負荷がかかる高速条件で切削加工した場合に、硬質被覆層がすぐれた耐欠損性と耐摩耗性を発揮する被覆工具に関するものである。 The present invention relates to a surface-coated cutting tool (hereinafter referred to as a coated tool). More specifically, for example, mild steel, general steel, high-hardness steel, and the like are accompanied by high heat generation and a large mechanical load is applied to the cutting edge portion. The present invention relates to a coated tool that exhibits excellent chipping resistance and wear resistance when a hard coating layer is cut under such high-speed conditions.
一般に、被覆工具には、各種の鋼や鋳鉄などの被削材の旋削加工や平削り加工にバイトの先端部に着脱自在に取り付けて用いられるインサート、被削材の穴あけ切削加工などに用いられるドリルやミニチュアドリル、さらに被削材の面削加工や溝加工、肩加工などに用いられるソリッドタイプのエンドミルなどがあり、またインサートを着脱自在に取り付けてソリッドタイプのエンドミルと同様に切削加工を行うインサート式エンドミル工具などが知られている。 In general, coated tools are used for turning and planing of work materials such as various types of steel and cast iron, inserts that can be used detachably attached to the tip of a cutting tool, drilling processing of work materials, etc. There are drills, miniature drills, solid type end mills used for chamfering, grooving, shoulder processing, etc. of the work material, etc. Also, inserts are detachably attached and cutting is performed in the same way as solid type end mills Insert type end mill tools are known.
近年、金属材料の切削加工においては高能率化の要求が高く、切削速度を高速化させることが求められている。このため、切削工具の工具基体表面を被覆する被膜に対して耐摩耗性や耐欠損性を向上させることが要求されている。
したがって、このような要求を満足するべく前記被膜の開発が種々行なわれている。例えば、特許文献１は、そのような被膜としてＡｌとＣｒとを含む特定組成の化合物を用いること（所謂ＡｌＣｒ系被膜）を提案している。
In recent years, there is a high demand for higher efficiency in cutting metal materials, and it is required to increase the cutting speed. For this reason, it is requested | required that a wear resistance and a fracture | rupture resistance should be improved with respect to the film which coat | covers the tool base | substrate surface of a cutting tool.
Therefore, various developments of the coating have been made to satisfy such requirements. For example, Patent Document 1 proposes to use a compound having a specific composition containing Al and Cr as such a coating (so-called AlCr-based coating).
また、特許文献２は、表面被覆切削工具の工具基体上に被膜を形成するものであって、この被膜が、第１超多層膜と第２超多層膜とを各々１以上交互に積層させてなる複合超多層膜を含み、前記第１超多層膜が、Ａ１層とＢ層とを各々１層以上交互に積層することにより構成され、前記第２超多層膜が、Ａ２層とＣ層とを各々１層以上交互に積層することにより構成され、前記Ａ１層とＡ２層が、各々ＴｉＮ、ＴｉＣＮ、ＴｉＡｌＮまたはＴｉＡｌＣＮのいずれかにより構成され、前記Ｂ層が、ＴｉＳｉＮまたはＴｉＳｉＣＮにより構成され、前記Ｃ層が、ＡｌＣｒＮまたはＡｌＣｒＣＮにより構成されることにより、耐熱性と耐摩耗性を維持しつつ、脆性の問題を低減した被膜を有する表面被覆切削工具を提供することを開示している。 Further, Patent Document 2 forms a film on a tool base of a surface-coated cutting tool, and the film is formed by alternately laminating one or more first super multi-layer films and second super multi-layer films. The first super multi-layer film is formed by alternately laminating one or more layers of A1 and B layers, and the second super multi-layer film is composed of an A2 layer and a C layer. Are alternately stacked, each of the A1 layer and the A2 layer is composed of any one of TiN, TiCN, TiAlN, or TiAlCN, and the B layer is composed of TiSiN or TiSiCN, It discloses that the C layer is composed of AlCrN or AlCrCN, thereby providing a surface-coated cutting tool having a coating with reduced brittleness problems while maintaining heat resistance and wear resistance.
さらに、別の従来被覆工具として、例えば、図２に概略説明図で示される物理蒸着装置の１種であるアークイオンプレーティング装置に工具基体を装入し、ヒーターで工具基体を、４５０℃の温度に加熱した状態で、アノード電極と所定組成を有するＡｌ−Ｃｒ合金がセットされたカソード電極（蒸発源）との間に、電流：１００Ａの条件でアーク放電を発生させ、同時に装置内に反応ガスとして窒素ガスを導入して窒素雰囲気とし、一方、前記工具基体には、例えば、−２００Ｖのバイアス電圧を印加した条件で、工具基体の表面に蒸発した粒子を蒸着させることにより（Ａｌ，Ｃｒ）Ｎ層からなる硬質被覆層が形成されることも知られている（例えば、特許文献３参照）。 Further, as another conventional coated tool, for example, an arc ion plating apparatus, which is one of physical vapor deposition apparatuses shown schematically in FIG. 2, is loaded with a tool base, and the tool base is heated to 450 ° C. with a heater. While being heated to a temperature, an arc discharge is generated between the anode electrode and a cathode electrode (evaporation source) on which an Al—Cr alloy having a predetermined composition is set under the condition of current: 100 A and simultaneously reacts in the apparatus. Nitrogen gas is introduced as a gas to form a nitrogen atmosphere. On the other hand, by evaporating evaporated particles on the surface of the tool base under the condition that a bias voltage of −200 V is applied (Al, Cr, for example) ) It is also known that a hard coating layer composed of an N layer is formed (see, for example, Patent Document 3).
ところが、近年の切削加工装置の自動化はめざましく、一方で切削加工に対する省力化および省エネ化、さらには低コスト化の要求は強く、これに伴い、切削工具には被削材の材種できるだけ影響を受けない汎用性、すなわち、できるだけ多くの材種の切削加工が可能な切削工具が求められる傾向にあるが、（Ａｌ，Ｃｒ）Ｎ層からなる被覆層を用いた従来被覆工具においては、これを、鋼や鋳鉄などの被削材の通常切削速度での切削加工に用いた場合には問題ないが、軟鋼、一般鋼、高硬度鋼等を、高い発熱を伴うとともに、切刃部への衝撃性および溶着性が著しい高速切削条件で切削した場合には、（Ａｌ，Ｃｒ）Ｎ層は高硬度な皮膜であるが、その硬度や高い残留応力のため、皮膜自体が崩壊したり、剥離したりする問題があり、この結果、切刃部における欠損（微少欠け）の発生が急激に増加し、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。 However, the automation of cutting machines in recent years has been remarkable. On the other hand, there is a strong demand for labor saving, energy saving, and cost reduction for cutting, and as a result, cutting tools have as much influence as possible on the type of work material. There is a tendency to find a versatile tool that does not receive, that is, a cutting tool capable of cutting as many grades as possible. However, in a conventional coated tool using a coating layer composed of an (Al, Cr) N layer, this is not the case. Although there is no problem when used for cutting materials such as steel and cast iron at the normal cutting speed, mild steel, general steel, high hardness steel, etc. are accompanied by high heat generation and impact on the cutting edge. (Al, Cr) N layer is a high hardness film when it is cut under high-speed cutting conditions that have remarkable properties and weldability. However, due to its hardness and high residual stress, the film itself may collapse or peel off. Or this problem Fruit, occurs rapidly increased in defects in the cutting edge (small chipping), which is at present, leading to a relatively short time service life due.
例えば、特許文献１によれば、耐摩耗性と耐欠損性をある程度向上させることは可能であるが、このようなＡｌＣｒ系被膜固有の問題として脆性を示すことから切削時の衝撃等により被膜自体が破壊したり剥離したりするという問題があった。
また、特許文献２による提案によっても、過酷な切削条件下においては被膜自体の破壊や剥離を十分に防止することができない場合があった。
そこで、本発明が解決しようとする技術的課題、すなわち、本発明の目的は、軟鋼、一般鋼、高硬度鋼等を、高熱発生を伴う高速切削条件で切削した場合においてもすぐれた耐摩耗性および耐欠損性を発揮する被覆工具を提供することである。
For example, according to Patent Document 1, although it is possible to improve the wear resistance and fracture resistance to some extent, since the problem inherent to such an AlCr-based film shows brittleness, the film itself due to impact during cutting or the like. There was a problem of breaking or peeling.
Further, even according to the proposal in Patent Document 2, there are cases where the coating itself cannot be sufficiently prevented from being broken or peeled off under severe cutting conditions.
Therefore, the technical problem to be solved by the present invention, that is, the object of the present invention is to provide excellent wear resistance even when mild steel, general steel, high hardness steel, etc. are cut under high-speed cutting conditions with high heat generation. And providing a coated tool exhibiting fracture resistance.
そこで、本発明者らは、前述のような観点から、特に軟鋼、一般鋼、高硬度鋼等の切削加工を、高速切削条件で切削加工した場合に、硬質被覆層がすぐれた耐摩耗性および耐欠損性を併せ持つ被覆工具を開発すべく、鋭意研究を行った。
その結果、
（１）（Ａｌ，Ｃｒ）Ｎ層は、高硬度な皮膜であり、硬質被覆層に適した材質ではあるが、従来の成膜方法で形成した場合、ヤング率が高くなり、これが原因で、皮膜の靭性が低下し、欠損の発生が増加する。
（２）本発明者らは、（Ａｌ，Ｃｒ）Ｎ層のヤング率は、膜形成時のバイアス電圧と反応雰囲気圧を調整することにより再現性よく、コントロールすることができることを見出したが、（Ａｌ，Ｃｒ）Ｎ層をすべてヤング率が高い層として形成すると、高硬度ではあるが、皮膜靭性の低下による耐欠損性が低下し、皮膜の崩壊や剥離が起こりやすくなってしまう。
（３）そこで、本発明者らは、硬質被覆層を高ヤング率の（Ａｌ，Ｃｒ）Ｎ層からなる薄層Ｂと耐欠損性および密着性にすぐれた（Ａｌ，Ｔｉ）Ｎ層からなる薄層Ａとを交互積層させることにより、高ヤング率の（Ａｌ，Ｃｒ）Ｎ層が有する欠点を（Ａｌ，Ｔｉ）Ｎ層との交互積層により補完し合い、従来被覆層にないすぐれた切削性能を有する硬質被覆層を得ることができるという全く新規な知見を得た。
本発明は、このような知見に基づき、薄層Ａ、薄層Ｂの組成、層厚、ヤング率、総層厚などと切削性能との関係を詳しく解析した結果得られたものであって、具体的には、以下のような構成からなる。
工具基体の表面に、ＡｌとＴｉとの合量に占めるＴｉの含有割合が２５〜５５原子％となるようにＴｉ成分を含有させたＡｌとＴｉの複合窒化物層（以下、（Ａｌ，Ｔｉ）Ｎ層と示す）であってヤング率ａが４００ＧＰａ≦ａ≦５５０ＧＰａである（Ａｌ，Ｔｉ）Ｎ層を薄層Ａとして０．１〜１．０μｍの平均層厚で形成し、硬質被覆層としてＡｌとＣｒとの合量に占めるＣｒの含有割合が２５〜５０原子％となるようにＣｒ成分を含有させたＡｌとＣｒの複合窒化物層であってヤング率ｂが５００ＧＰａ≦ｂ≦８００ＧＰａである高ヤング率層（以下、高ヤング率（Ａｌ，Ｃｒ）Ｎ層と示す）を薄層Ｂとして０．１〜１．０μｍの平均層厚で形成し、この上に、さらにその上に薄層Ａ、薄層Ｂを順次形成し、総平均層厚が１．０〜１０μｍである交互積層構造を有する層を形成する。この結果、薄層Ａを構成する（Ａｌ，Ｔｉ）Ｎ層が、すぐれた密着性、耐欠損性を示し、薄層Ｂの高ヤング率（Ａｌ，Ｃｒ）Ｎ層が、すぐれた耐摩耗性、耐熱性を示すと共に、（Ａｌ，Ｔｉ）Ｎ層と高ヤング率（Ａｌ，Ｃｒ）Ｎ層のそれぞれ組成の異なる層を交互積層として形成することにより、それぞれの層の粒子の成長の粗大化が防止され、粒子の微細化が図られ、膜強度が向上するとともに、この積層構造によってクラックの伝播・進展が防止されることで耐欠損性、耐チッピング性が向上する。これらの相乗効果により、すぐれた耐欠損性、耐摩耗性、耐熱性が発揮されるという新規な知見を得て、かかる知見に基づき、本発明を完成するに至った。
In view of the above, the inventors of the present invention have excellent wear resistance and a hard coating layer, particularly when cutting of mild steel, general steel, high hardness steel and the like under high-speed cutting conditions. In order to develop a coated tool that has both fracture resistance, we conducted intensive research.
as a result,
(1) The (Al, Cr) N layer is a high-hardness film and is a material suitable for the hard coating layer. However, when formed by a conventional film formation method, the Young's modulus increases, and this is the cause. The toughness of the film decreases and the occurrence of defects increases.
(2) The present inventors have found that the Young's modulus of the (Al, Cr) N layer can be controlled with good reproducibility by adjusting the bias voltage and reaction atmosphere pressure during film formation. When all the (Al, Cr) N layers are formed as layers having a high Young's modulus, although the hardness is high, the fracture resistance due to the decrease in the film toughness decreases, and the film tends to collapse or peel off.
(3) Therefore, the inventors of the present invention have a hard coating layer composed of a thin layer B composed of an (Al, Cr) N layer having a high Young's modulus and an (Al, Ti) N layer excellent in fracture resistance and adhesion. By alternately laminating the thin layer A, the defects of the high Young's modulus (Al, Cr) N layer are complemented by the alternate laminating with the (Al, Ti) N layer, and excellent cutting that the conventional coating layer does not have. A completely new finding was obtained that a hard coating layer having performance can be obtained.
Based on such knowledge, the present invention was obtained as a result of detailed analysis of the relationship between the thin layer A, the composition of the thin layer B, the layer thickness, the Young's modulus, the total layer thickness and the cutting performance, Specifically, the configuration is as follows.
An Al and Ti composite nitride layer (hereinafter referred to as (Al, Ti) containing a Ti component so that the Ti content in the total amount of Al and Ti is 25 to 55 atomic% on the surface of the tool base. A hard coating layer formed by forming an (Al, Ti) N layer having a Young's modulus a of 400 GPa ≦ a ≦ 550 GPa as a thin layer A with an average layer thickness of 0.1 to 1.0 μm. As a composite nitride layer of Al and Cr containing a Cr component so that the Cr content in the total amount of Al and Cr is 25 to 50 atomic%, the Young's modulus b is 500 GPa ≦ b ≦ 800 GPa A high Young's modulus layer (hereinafter referred to as a high Young's modulus (Al, Cr) N layer) is formed as a thin layer B with an average layer thickness of 0.1 to 1.0 μm. A thin layer A and a thin layer B are formed in order, and the total average layer thickness is Forming a layer having alternating layered structure that. As a result, the (Al, Ti) N layer constituting the thin layer A exhibits excellent adhesion and fracture resistance, and the high Young's modulus (Al, Cr) N layer of the thin layer B exhibits excellent wear resistance. In addition to exhibiting heat resistance, the layers of different composition of the (Al, Ti) N layer and the high Young's modulus (Al, Cr) N layer are formed as alternating layers, thereby coarsening the particle growth of each layer Is prevented, particles are miniaturized, film strength is improved, and crack propagation and progress are prevented by this laminated structure, thereby improving chipping resistance and chipping resistance. By these synergistic effects, the inventors have obtained new knowledge that excellent chipping resistance, wear resistance, and heat resistance are exhibited, and based on such knowledge, the present invention has been completed.
本発明は、前記研究結果に基づいてなされたものであって、
「（１） 炭化タングステン基超硬合金または炭窒化チタン基サーメットで構成された工具基体の表面に硬質被覆層を形成してなる表面被覆切削工具において、
前記硬質被覆層が、
（ａ）０．１〜１．０μｍの平均層厚を有し、かつ、
組成式：（Ａｌ１−ｙＴｉｙ）Ｎ（ここで、ｙはＡｌとＴｉの合量に占めるＴｉの含有割合を示し、原子比で、０．２５≦ｙ≦０．５５である）を満足し、ヤング率ａが４００ＧＰａ≦ａ≦５５０ＧＰａであるＡｌとＴｉとの複合窒化物からなる薄層Ａ、
（ｂ）０．１〜１．０μｍの平均層厚を有し、かつ、
組成式：（Ａｌ１−ｘＣｒｘ）Ｎ（ここで、ｘはＡｌとＣｒの合量に占めるＣｒの含有割合を示し、原子比で、０．２５≦ｘ≦０．５０である）を満足し、ヤング率ｂが５００ＧＰａ≦ｂ≦８００ＧＰａであり、且つ、前記薄層Ａのヤング率よりも１００ＧＰａ以上大きいＡｌとＣｒとの複合窒化物層からなる薄層Ｂと、
（ｃ）工具基体直上が薄層Ａであり、薄層Ａと薄層Ｂとの交互積層構造を有し、総平均層厚が１．０〜１０μｍである、
前記（ａ）〜（ｃ）の条件を満たすことを特徴とする表面被覆切削工具。」
を特徴とする。
The present invention has been made based on the research results,
“(1) In a surface-coated cutting tool in which a hard coating layer is formed on the surface of a tool base composed of tungsten carbide-based cemented carbide or titanium carbonitride-based cermet,
The hard coating layer is
(A) having an average layer thickness of 0.1 to 1.0 μm, and
Composition formula: (Al 1-y Ti y ) N (where y represents the content ratio of Ti in the total amount of Al and Ti, and the atomic ratio is 0.25 ≦ y ≦ 0.55) Satisfactory, thin layer A composed of a composite nitride of Al and Ti with Young's modulus a of 400 GPa ≦ a ≦ 550 GPa,
(B) having an average layer thickness of 0.1 to 1.0 μm, and
Composition formula: (Al 1-x Cr x ) N (where x represents the content ratio of Cr in the total amount of Al and Cr, and the atomic ratio is 0.25 ≦ x ≦ 0.50) Satisfied, a thin layer B composed of a composite nitride layer of Al and Cr having a Young's modulus b of 500 GPa ≦ b ≦ 800 GPa and greater than the Young's modulus of the thin layer A by 100 GPa,
(C) Immediately above the tool substrate is the thin layer A, and has an alternate laminated structure of the thin layer A and the thin layer B, and the total average layer thickness is 1.0 to 10 μm.
A surface-coated cutting tool characterized by satisfying the conditions (a) to (c). "
It is characterized by.
次に、本発明の被覆工具の硬質被覆層の構成層に関し、前記の通りに数値限定した理由を説明する。 Next, the reason why the numerical values of the constituent layers of the hard coating layer of the coated tool of the present invention are limited as described above will be described.
（ａ）薄層Ｂを構成する（Ａｌ，Ｃｒ）Ｎ層の組成およびヤング率：
交互積層構造の１層である薄層Ｂを構成する（Ａｌ，Ｃｒ）Ｎ層の構成成分であるＡｌ成分には硬質被覆層における高温硬さを向上させ、同Ｃｒ成分には高温強度を向上させる作用があるが、Ａｌとの合量に占めるＣｒの含有割合を示すｘ値（原子比、以下同じ）が０．２５未満になると、相対的にＡｌの含有割合が増加することによって、結晶構造が立方晶から六方晶へ変化し、皮膜硬さが低下するので、少なくとも所定の皮膜硬さを保持するためには、Ａｌとの合量に占めるＣｒの含有割合を示すｘ値が０．２５以上とする必要がある。一方、Ｃｒの含有割合を示すｘ値が同０．５０を越えると、相対的にＡｌの含有割合が減少し、高速切削加工で必要とされる高温硬さを確保することができず、チッピングの発生を防止することが困難になることからｘ値を０．２５〜０．５０と定めた。
(A) Composition and Young's modulus of (Al, Cr) N layer constituting thin layer B:
The Al component, which is a component of the (Al, Cr) N layer that constitutes the thin layer B, which is one layer of the alternately laminated structure, improves the high temperature hardness of the hard coating layer, and the Cr component improves the high temperature strength. However, when the x value (atomic ratio, the same applies hereinafter) indicating the Cr content in the total amount with Al is less than 0.25, the Al content is relatively increased, so that Since the structure changes from cubic to hexagonal and the film hardness decreases, in order to maintain at least the predetermined film hardness, the x value indicating the Cr content in the total amount with Al is 0. It needs to be 25 or more. On the other hand, when the x value indicating the Cr content ratio exceeds 0.50, the Al content ratio is relatively reduced, and the high temperature hardness required for high-speed cutting cannot be ensured. The x value was determined to be 0.25 to 0.50 because it would be difficult to prevent the occurrence of.
また、薄層Ｂを構成する（Ａｌ，Ｃｒ）Ｎ層のヤング率が５００〜８００ＧＰａである高ヤング率とすることで外部応力が加わった際の皮膜の変形量が増加し、クラック等の発生を阻止するため、耐欠損性を向上させることができる。ここで、前記ヤング率を５００〜８００ＧＰａに限定した理由は、ヤング率を５００ＧＰａよりも下げることは、耐摩耗性の低下が著しいため好ましくなく、一方、８００ＧＰａより大きくなると皮膜靭性の低下による耐欠損性が低下してしまうため、皮膜の崩壊や剥離が起こりやすくなる。したがって、交互積層構造の奏する機能をより効果的に発揮させるために、ヤング率を５００〜８００ＧＰａに限定した。さらに、薄層Ｂを構成する（Ａｌ，Ｃｒ）Ｎ層のヤング率が、薄層Ａを構成する（Ａｌ，Ｔｉ）Ｎ層のヤング率よりも１００ＧＰａ以上大きいときに、切削時に交互積層構造中に発生したクラックに対し、薄層Ａと薄層Ｂの境界部において優れた耐クラック進展性を持つことを見出した。 In addition, by making the Young's modulus of the (Al, Cr) N layer constituting the thin layer B high Young's modulus of 500 to 800 GPa, the amount of deformation of the film when external stress is applied increases, and cracks and the like are generated. Therefore, the chipping resistance can be improved. Here, the reason why the Young's modulus is limited to 500 to 800 GPa is that lowering the Young's modulus to less than 500 GPa is not preferable because the wear resistance is remarkably lowered. Since the properties are reduced, the coating is likely to collapse or peel off. Therefore, the Young's modulus is limited to 500 to 800 GPa in order to more effectively exert the function exhibited by the alternately laminated structure. Further, when the Young's modulus of the (Al, Cr) N layer constituting the thin layer B is 100 GPa or more larger than the Young's modulus of the (Al, Ti) N layer constituting the thin layer A, the alternating layered structure is formed during cutting. The present inventors have found that the cracks generated at the boundary between the thin layer A and the thin layer B have excellent crack resistance.
（ｂ）薄層Ａ層を構成する（Ａｌ，Ｔｉ）Ｎ層の組成およびヤング率：
薄層Ｂと共に交互積層構造を構成する薄層Ａの（Ａｌ，Ｔｉ）Ｎ層は、層全体に亘って均質な高温硬さと耐熱性および靭性を示すが、その構成成分であるＴｉ成分によって、すぐれた高温強度を備えるようになり、また、Ａｌ成分によって、高温硬さと耐熱性を補完する。そのため、高温切削条件下でも低摩擦係数が維持され、すぐれた耐熱性を発揮するようになるが、Ａｌとの合量に占めるＴｉの含有割合を示すｙ値（原子比、以下同じ）が０．２５未満になると、高温強度を確保することができないために刃先の境界部分において異常損傷を生じ欠損を発生しやすくなるため長寿命を期待することはできず、一方、Ａｌとの合量に占めるＴｉの含有割合を示すｙ値が０．５５を越えると、相対的にＡｌの含有割合が減少し、高速切削加工で必要とされる高温硬さ確保することができないばかりか、耐摩耗性も低下し、チッピング発生を防止することが困難になることから、ｙ値を０．２５〜０．５５と定めた。
(B) Composition and Young's modulus of the (Al, Ti) N layer constituting the thin layer A layer:
The (Al, Ti) N layer of the thin layer A that constitutes an alternate laminated structure together with the thin layer B exhibits uniform high-temperature hardness and heat resistance and toughness throughout the layer, but by the Ti component that is a constituent component thereof, It has excellent high-temperature strength, and the Al component complements high-temperature hardness and heat resistance. Therefore, a low friction coefficient is maintained even under high-temperature cutting conditions, and excellent heat resistance is exhibited, but the y value (atomic ratio, the same applies hereinafter) indicating the Ti content in the total amount with Al is 0. If it is less than .25, high temperature strength cannot be secured, and abnormal damage is caused at the boundary portion of the cutting edge and defects are likely to occur, so a long life cannot be expected. If the y value indicating the Ti content ratio exceeds 0.55, the Al content ratio is relatively decreased, and not only the high-temperature hardness required for high-speed cutting cannot be secured, but also wear resistance. The y value was determined to be 0.25 to 0.55 because it is difficult to prevent the occurrence of chipping.
また、薄層Ａを構成する（Ａｌ，Ｔｉ）Ｎ層については、期待される耐欠損性、耐摩耗性、耐熱性を十分に発揮させるためには、被削材や切削条件に限らず、ヤング率が４００〜５５０ＧＰａであるとき（Ａｌ，Ｔｉ）Ｎ層の有する耐摩耗性、耐熱性、耐欠損性がより有効に発揮される。そのため、本発明においては、薄層Ａの（Ａｌ，Ｔｉ）Ｎ層のヤング率は４００〜５５０ＧＰａと定めた。 In addition, the (Al, Ti) N layer constituting the thin layer A is not limited to the work material and cutting conditions in order to sufficiently exhibit the expected fracture resistance, wear resistance, and heat resistance. When the Young's modulus is 400 to 550 GPa, the wear resistance, heat resistance, and fracture resistance of the (Al, Ti) N layer are more effectively exhibited. Therefore, in the present invention, the Young's modulus of the (Al, Ti) N layer of the thin layer A is set to 400 to 550 GPa.
（ｃ）薄層Ａおよび薄層Ｂの平均層厚ならびに硬質被覆層の総平均層厚：
本発明の硬質被覆層は、それぞれの組成の異なる薄層Ａと薄層Ｂとを交互に積層して構成した交互積層構造とすることで、それぞれの層の粒子の成長の粗大化が防止され、粒子の微細化が図られ、膜強度が向上するとともに、この積層構造によってクラックの伝播・進展が防止されることで耐欠損性、耐チッピング性が向上するが、薄層Ａおよび薄層Ｂの平均層厚が０．１μｍ未満になると、各薄層を所定組成のものとして明確に形成することが困難であるばかりか、各薄層の有する前記のすぐれた特性を発揮することができない。一方、それぞれの平均層厚が１．０μｍを超えると、粒子の粗大化による膜強度の低下により、耐欠損性、耐チッピング性が低下することから、薄層Ａ、薄層Ｂのそれぞれの平均層厚を、０．１〜１．０μｍと定めた。
また、硬質被覆層の総平均層厚が、１．０μｍ未満では、前述した交互積層構造の備えるすぐれた耐欠損性、耐チッピング性を十分に発揮することができず、一方、１０μｍを超えると、反対に、チッピング、欠損を発生しやすくなるので、硬質被覆層の総平均層厚は、１．０〜１０μｍと定めた。
(C) The average layer thickness of the thin layers A and B and the total average layer thickness of the hard coating layer:
The hard coating layer of the present invention has an alternate laminated structure in which thin layers A and thin layers B having different compositions are alternately laminated, thereby preventing the growth of particles in each layer from being coarsened. In addition to reducing the size of the particles and improving the film strength, the lamination structure prevents crack propagation and progress, thereby improving the chipping resistance and chipping resistance. When the average layer thickness is less than 0.1 μm, it is difficult to clearly form each thin layer as having a predetermined composition, and the above-mentioned excellent characteristics possessed by each thin layer cannot be exhibited. On the other hand, if the average layer thickness exceeds 1.0 μm, the chip strength and chipping resistance decrease due to the decrease in film strength due to the coarsening of the particles. The layer thickness was set to 0.1 to 1.0 μm.
In addition, when the total average layer thickness of the hard coating layer is less than 1.0 μm, the excellent chipping resistance and chipping resistance provided by the above-described alternate laminated structure cannot be sufficiently exhibited, while when it exceeds 10 μm. On the contrary, since chipping and defects are likely to occur, the total average layer thickness of the hard coating layer was determined to be 1.0 to 10 μm.
加えて特に限定するわけではないが、薄層Ｂを構成する（Ａｌ，Ｃｒ）Ｎ層の結晶構造と薄層Ａを構成する（Ａｌ，Ｔｉ）Ｎ層の結晶構造をと同じ立方晶とすることにより、層間の密着性が向上し、層間剥離による寿命劣化の問題が解消されるため好ましい。 In addition, although not particularly limited, the crystal structure of the (Al, Cr) N layer constituting the thin layer B and the crystal structure of the (Al, Ti) N layer constituting the thin layer A are the same cubic crystal. This improves the adhesion between the layers and solves the problem of life deterioration due to delamination, which is preferable.
なお、本発明の硬質被覆層を構成する薄層Ｂを構成する（Ａｌ，Ｃｒ）Ｎ層および薄層Ａを構成する（Ａｌ，Ｔｉ）Ｎ層は、例えば、図１に概略説明図で示される物理蒸着装置の１種であるアークイオンプレーティング装置に工具基体を装入し、ヒーターで装置内を、例えば、５００℃の温度に加熱した状態で、
（ａ）アノード電極とカソード電極（蒸発源）としてのＡｌ−Ｔｉ合金との間に、例えば、電流：１１０Ａの条件でアーク放電を発生させ、同時に装置内に反応ガスとして窒素ガスを導入して、例えば、３．０Ｐａの反応雰囲気とし、工具基体には、例えば、−１００Ｖのバイアス電圧を印加した条件で所定時間蒸着することにより、工具基体表面に、所定の目標層厚の薄層Ａである（Ａｌ，Ｔｉ）Ｎ層が形成される。
（ｂ）ついで、装置内に所定組成のＡｌ−Ｃｒ合金からなるカソード電極（蒸発源）を配置し、アノード電極とカソード電極（蒸発源）としてのＡｌ−Ｃｒ合金との間に、例えば、電流：１１０Ａの条件でアーク放電を発生させ、同時に装置内に反応ガスとして窒素ガスを導入して、例えば、５．０Ｐａの反応雰囲気とし、一方、工具基体には、例えば、−１００Ｖのバイアス電圧を印加した条件で所定時間蒸着することにより、前記薄層Ａ上に所定の目標層厚、ヤング率の薄層Ｂを構成する（Ａｌ，Ｃｒ）層が形成される。
前記（ａ）、（ｂ）を所定の総目標層厚になるまで、交互に繰り返すことにより、本発明の硬質被覆層を蒸着形成することができる。すなわち、反応雰囲気圧と工具基体に印加するバイアス電圧を調整することで、薄層Ｂを構成する（Ａｌ，Ｃｒ）Ｎ層のヤング率をコントロールすることができる。
The (Al, Cr) N layer constituting the thin layer B constituting the hard coating layer of the present invention and the (Al, Ti) N layer constituting the thin layer A are shown schematically in FIG. 1, for example. In a state where a tool base is loaded into an arc ion plating apparatus which is a kind of physical vapor deposition apparatus, and the inside of the apparatus is heated to a temperature of, for example, 500 ° C. with a heater.
(A) For example, arc discharge is generated between the anode electrode and the Al—Ti alloy as the cathode electrode (evaporation source) under the condition of current: 110 A, and simultaneously, nitrogen gas is introduced into the apparatus as a reaction gas. For example, the reaction atmosphere is set to 3.0 Pa, and the tool base is vapor-deposited for a predetermined time under the condition that a bias voltage of −100 V is applied, for example, so that a thin layer A having a predetermined target layer thickness is formed on the tool base surface. A certain (Al, Ti) N layer is formed.
(B) Next, a cathode electrode (evaporation source) made of an Al—Cr alloy having a predetermined composition is arranged in the apparatus, and, for example, an electric current is provided between the anode electrode and the Al—Cr alloy as the cathode electrode (evaporation source). : Arc discharge is generated under the condition of 110 A, and nitrogen gas is introduced as a reaction gas into the apparatus at the same time to obtain a reaction atmosphere of, for example, 5.0 Pa, while a bias voltage of, for example, −100 V is applied to the tool base. By depositing for a predetermined time under the applied conditions, an (Al, Cr) layer constituting a thin layer B having a predetermined target layer thickness and Young's modulus is formed on the thin layer A.
By repeating the steps (a) and (b) alternately until a predetermined total target layer thickness is obtained, the hard coating layer of the present invention can be formed by vapor deposition. That is, the Young's modulus of the (Al, Cr) N layer constituting the thin layer B can be controlled by adjusting the reaction atmospheric pressure and the bias voltage applied to the tool base.
本発明の被覆工具の一態様によれば、硬質被覆層が（Ａｌ，Ｔｉ）Ｎ層からなる薄層Ａと高ヤング率（Ａｌ，Ｃｒ）Ｎ層からなる薄層Ｂとの交互積層構造であることによって、薄層Ａが奏するすぐれた耐欠損性および密着性と、薄層Ｂが奏するすぐれた高温硬さと耐熱性および靭性との相乗効果によって、硬質被覆層は、すぐれた高温硬さ、耐熱性、高温強度、耐摩耗性、潤滑性、耐衝撃性、耐欠損性、耐チッピング性を有することから、その結果、特に、軟鋼、一般鋼、高硬度鋼等の大きな発熱を伴い、かつ、高負荷のかかる高速切削加工であっても、長期に亘ってすぐれた耐摩耗性、耐欠損性を発揮するものである。 According to one aspect of the coated tool of the present invention, the hard coating layer has an alternately laminated structure of a thin layer A composed of an (Al, Ti) N layer and a thin layer B composed of a high Young's modulus (Al, Cr) N layer. By virtue of the synergistic effect of the excellent fracture resistance and adhesion exhibited by the thin layer A and the excellent high temperature hardness and heat resistance and toughness exhibited by the thin layer B, the hard coating layer has excellent high temperature hardness, Because it has heat resistance, high temperature strength, wear resistance, lubricity, impact resistance, chipping resistance, chipping resistance, as a result, it is accompanied by large heat generation, especially mild steel, general steel, high hardness steel, etc. Even in high-speed cutting with a high load, it exhibits excellent wear resistance and fracture resistance over a long period of time.
つぎに、本発明の被覆工具を実施例により具体的に説明する。 Next, the coated tool of the present invention will be specifically described with reference to examples.
原料粉末として、いずれも１〜３μｍの平均粒径を有するＷＣ粉末、ＴｉＣ粉末、ＺｒＣ粉末、ＶＣ粉末、ＴａＣ粉末、ＮｂＣ粉末、Ｃｒ３Ｃ２粉末、ＴｉＮ粉末、ＴａＮ粉末、および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、１００ＭＰａの圧力で圧粉体にプレス成形し、この圧粉体を６Ｐａの真空中、温度：１４００℃に１時間保持の条件で焼結し、焼結後、ＩＳＯ規格・ＣＮＭＧ１２０４０８のインサート形状をもったＷＣ基超硬合金製の工具基体Ａ−１〜Ａ−１０を形成した。 WC powder, TiC powder, ZrC powder, VC powder, TaC powder, NbC powder, Cr 3 C 2 powder, TiN powder, TaN powder, and Co powder all having an average particle diameter of 1 to 3 μm are prepared as raw material powders. These raw material powders are blended into the composition shown in Table 1, wet mixed by a ball mill for 72 hours, dried, and then pressed into a green compact at a pressure of 100 MPa. Medium, sintered at 1400 ° C. for 1 hour, and after sintering, tool bases A-1 to A-10 made of WC-base cemented carbide having an ISO standard / CNMG120408 insert shape were formed. .
また、原料粉末として、いずれも０．５〜２μｍの平均粒径を有するＴｉＣＮ（質量比で、ＴｉＣ／ＴｉＮ＝５０／５０）粉末、Ｍｏ２Ｃ粉末、ＺｒＣ粉末、ＮｂＣ粉末、ＴａＣ粉末、ＷＣ粉末、Ｃｏ粉末、およびＮｉ粉末を用意し、これら原料粉末を、表２に示される配合組成に配合し、ボールミルで２４時間湿式混合し、乾燥した後、１００ＭＰａの圧力で圧粉体にプレス成形し、この圧粉体を２ｋＰａの窒素雰囲気中、温度：１５００℃に１時間保持の条件で焼結し、焼結後、ＩＳＯ規格・ＣＮＭＧ１２０４０８のインサート形状をもったＴｉＣＮ基サーメット製の工具基体Ｂ−１〜Ｂ−６を形成した。 In addition, as raw material powders, TiCN (mass ratio, TiC / TiN = 50/50) powder, Mo 2 C powder, ZrC powder, NbC powder, TaC powder, WC, all having an average particle diameter of 0.5 to 2 μm. Prepare powder, Co powder, and Ni powder, mix these raw material powders into the composition shown in Table 2, wet mix for 24 hours with a ball mill, dry, and press-mold into green compact at 100 MPa pressure Then, this green compact was sintered in a nitrogen atmosphere of 2 kPa at a temperature of 1500 ° C. for 1 hour, and after sintering, a tool substrate B made of TiCN base cermet having an ISO standard / CNMG120408 insert shape was used. -1 to B-6 were formed.
（ａ）ついで、前記工具基体Ａ−１〜Ａ−１０およびＢ−１〜Ｂ−６のそれぞれを、アセトン中で超音波洗浄し、乾燥した状態で、図１に示されるアークイオンプレーティング装置内の回転テーブル上の中心軸から半径方向に所定距離離れた位置に外周部に沿って装着し、前記回転テーブルを挟んで対向する２つのカソード電極（蒸発源）を配置し、第１の電極として、薄層Ａ形成用の所定組成を有するＡｌ−Ｔｉ合金、第２の電極として、薄層Ｂ形成用の所定組成を有するＡｌ−Ｃｒ合金を配置し、
（ｂ）まず、装置内を排気して０．１ Ｐａ以下の真空に保持しながら、ヒーターで装置内を５００℃に加熱した後、回転テーブル上で自転しながら回転する工具基体に−１０００Ｖの直流バイアス電圧を印加し、かつＡｌ−Ｃｒ合金（カソード電極）とアノード電極との間に１００Ａの電流を流してアーク放電を発生させ、もって工具基体表面をボンバード洗浄し、
（ｃ）次に装置内雰囲気を０．５〜９．０Ｐａの窒素雰囲気に保持して、回転テーブル上で自転しながら回転する工具基体に−２０〜−１５０Ｖの直流バイアス電圧を印加し、カソード電極（蒸発源）であるＡｌ−Ｔｉ合金電極とアノード電極との間に１２０Ａの電流を流してアーク放電を発生させて、表３に示される目標組成、目標層厚の薄層Ａとしての（Ａｌ，Ｔｉ）Ｎ層を蒸着形成した。
（ｄ）引き続いて、装置内に反応ガスとして窒素ガスを導入して３．０〜９．０Ｐａの反応雰囲気とすると共に、回転テーブル上で自転しながら回転する工具基体に−５０〜−１５０Ｖの直流バイアス電圧を印加し、かつ、カソード電極の前記Ａｌ−Ｃｒ合金とアノード電極との間に１２０Ａの電流を流してアーク放電を発生させ、前記薄層Ａの上に、表３に示される目標組成、目標層厚の薄層Ｂとしての（Ａｌ，Ｃｒ）Ｎ層を蒸着形成した後、カソード電極（蒸発源）とアノード電極との間のアーク放電を停止し、
前記（ｃ）、（ｄ）を交互に繰り返して、表３に示される総目標層厚の交互積層構造の硬質被覆層を工具基体上に蒸着形成し、本発明被覆工具としての表面被覆インサート（以下、本発明被覆インサートと云う）１〜１６をそれぞれ製造した。
薄層Ｂのヤング率の制御は、前述のようにバイアス電圧と窒素分圧を制御することにより行った。すなわち、高バイアス電圧、高窒素分圧とすることで、薄層Ｂの（Ａｌ，Ｃｒ）Ｎ層のヤング率を高ヤング率に制御することができる。また、薄層Ａの（Ａｌ，Ｔｉ）Ｎ層のヤング率の制御は、前述のようにバイアス電圧と窒素分圧を制御することにより行った。すなわち、−２０〜１５０Ｖ、かつ０．５〜９．０Ｐａの範囲で成膜することで４００〜５５０ＧＰａに制御することができる。薄層Ａおよび薄層Ｂの形成条件（バイアス電圧、窒素分圧）、ヤング率を同じく表３に示す。
また、ヤング率の測定は、ナノインデンター（ＭＴＳシステムズ社の商標）を用いてナノインデンテーション法による測定を行った。さらに本発明被覆インサート１〜１６の薄層Ａおよび薄層Ｂについて、Ｘ線回折装置を用いて、その結晶構造を特定した。それらの結果を同じく表３に示した。
(A) Next, each of the tool bases A-1 to A-10 and B-1 to B-6 is ultrasonically cleaned in acetone and dried, and then the arc ion plating apparatus shown in FIG. A first electrode is provided with two cathode electrodes (evaporation sources) that are mounted along the outer peripheral portion at a predetermined distance in the radial direction from the central axis on the inner rotary table, and that face each other across the rotary table. An Al—Ti alloy having a predetermined composition for forming the thin layer A, and an Al—Cr alloy having a predetermined composition for forming the thin layer B as the second electrode,
(B) First, the inside of the apparatus is evacuated and kept at a vacuum of 0.1 Pa or less, and the inside of the apparatus is heated to 500 ° C. with a heater, and then rotated to a tool base that rotates while rotating on a rotary table. A DC bias voltage is applied, and an arc discharge is generated by flowing a current of 100 A between the Al—Cr alloy (cathode electrode) and the anode electrode, and the tool base surface is bombard washed.
(C) Next, the atmosphere in the apparatus is maintained in a nitrogen atmosphere of 0.5 to 9.0 Pa, and a DC bias voltage of -20 to -150 V is applied to the rotating tool base while rotating on the rotary table, and the cathode An arc discharge is generated by flowing a current of 120 A between an Al—Ti alloy electrode, which is an electrode (evaporation source), and an anode electrode, and a thin layer A having a target composition and a target layer thickness shown in Table 3 ( An Al, Ti) N layer was deposited.
(D) Subsequently, nitrogen gas is introduced as a reaction gas into the apparatus to obtain a reaction atmosphere of 3.0 to 9.0 Pa, and a tool base that rotates while rotating on a rotary table is set to −50 to −150 V. A direct current bias voltage is applied and a current of 120 A is passed between the Al—Cr alloy of the cathode electrode and the anode electrode to generate an arc discharge, and the target shown in Table 3 is formed on the thin layer A. After the vapor deposition of the (Al, Cr) N layer as the thin layer B having the composition and target layer thickness, the arc discharge between the cathode electrode (evaporation source) and the anode electrode is stopped,
By alternately repeating the steps (c) and (d), a hard coating layer having an alternate laminated structure having a total target layer thickness shown in Table 3 is formed on the tool substrate by vapor deposition, and the surface coating insert ( Hereinafter, the present invention coated inserts) 1 to 16 were produced.
The Young's modulus of the thin layer B was controlled by controlling the bias voltage and the nitrogen partial pressure as described above. That is, by setting a high bias voltage and a high nitrogen partial pressure, the Young's modulus of the (Al, Cr) N layer of the thin layer B can be controlled to a high Young's modulus. Further, the Young's modulus of the (Al, Ti) N layer of the thin layer A was controlled by controlling the bias voltage and the nitrogen partial pressure as described above. That is, it can control to 400-550 GPa by forming into a film in the range of -20-150V and 0.5-9.0Pa. The conditions for forming the thin layer A and the thin layer B (bias voltage, nitrogen partial pressure) and Young's modulus are also shown in Table 3.
The Young's modulus was measured by a nanoindentation method using a nanoindenter (trademark of MTS Systems). Furthermore, about the thin layer A and the thin layer B of this invention covering insert 1-16, the crystal structure was specified using the X-ray-diffraction apparatus. The results are also shown in Table 3.
また、比較の目的で、
（ａ）前記工具基体Ａ−１〜Ａ−１０およびＢ−１〜Ｂ−６のそれぞれを、アセトン中で超音波洗浄し、乾燥した状態で、図１に示されるアークイオンプレーティング装置内の回転テーブル上の中心軸から半径方向に所定距離離れた位置に外周部に沿って装着し、前記回転テーブルを挟んで対向する２つのカソード電極（蒸発源）を配置し、第１の電極として、薄層Ａ形成用の所定組成を有するＡｌ−Ｔｉ合金、第２の電極として、薄層Ｂ形成用の所定組成を有するＡｌ−Ｃｒ合金を配置し、
（ｂ）まず、装置内を排気して０．１ Ｐａ以下の真空に保持しながら、ヒーターで装置内を５００℃に加熱した後、回転テーブル上で自転しながら回転する工具基体に−１０００Ｖの直流バイアス電圧を印加し、かつＡｌ−Ｃｒ合金（カソード電極）とアノード電極との間に１００Ａの電流を流してアーク放電を発生させ、もって工具基体表面をボンバード洗浄し、
（ｃ）次に装置内雰囲気を０．５〜９．０Ｐａの窒素雰囲気に保持して、回転テーブル上で自転しながら回転する工具基体に−２０〜−１５０Ｖの直流バイアス電圧を印加し、カソード電極（蒸発源）であるＡｌ−Ｔｉ合金電極とアノード電極との間に１２０Ａの電流を流してアーク放電を発生させて、表４に示される目標組成、目標層厚の薄層Ａとしての（Ａｌ，Ｔｉ）Ｎ層を蒸着形成した。
（ｄ）引き続いて、装置内に反応ガスとして窒素ガスを導入して０．５〜９．０Ｐａの反応雰囲気とすると共に、回転テーブル上で自転しながら回転する工具基体に−２０〜−５００Ｖの直流バイアス電圧を印加し、かつ、カソード電極の前記Ａｌ−Ｃｒ合金とアノード電極との間に１２０Ａの電流を流してアーク放電を発生させ、工具基体の表面に、表４に示される目標組成、目標層厚の薄層Ｂとしての（Ａｌ，Ｃｒ）Ｎ層を蒸着形成した後、カソード電極（蒸発源）とアノード電極との間のアーク放電を停止し、
前記（ｃ）、（ｄ）を交互に繰り返して、表４に示される総目標層厚の交互積層構造の硬質被覆層を工具基体上に蒸着形成し、比較被覆工具としての表面被覆インサート（以下、本発明被覆インサートと云う）１〜８をそれぞれ製造した。各層の形成条件（バイアス電圧、窒素分圧）を同じく表４に示す。さらに、比較被覆インサート１〜８について、前記と同様の方法によりヤング率および結晶構造を測定した。それらの結果を同じく表４に示した。
For comparison purposes,
(A) Each of the tool bases A-1 to A-10 and B-1 to B-6 is ultrasonically cleaned in acetone and dried, and then in the arc ion plating apparatus shown in FIG. Attached along the outer periphery at a predetermined distance in the radial direction from the central axis on the rotary table, two cathode electrodes (evaporation sources) facing each other across the rotary table are arranged, and the first electrode is An Al—Ti alloy having a predetermined composition for forming the thin layer A and an Al—Cr alloy having a predetermined composition for forming the thin layer B are disposed as the second electrode,
(B) First, the inside of the apparatus is evacuated and kept at a vacuum of 0.1 Pa or less, and the inside of the apparatus is heated to 500 ° C. with a heater, and then rotated to a tool base that rotates while rotating on a rotary table. A DC bias voltage is applied, and an arc discharge is generated by flowing a current of 100 A between the Al—Cr alloy (cathode electrode) and the anode electrode, and the tool base surface is bombard washed.
(C) Next, the atmosphere in the apparatus is maintained in a nitrogen atmosphere of 0.5 to 9.0 Pa, and a DC bias voltage of -20 to -150 V is applied to the rotating tool base while rotating on the rotary table, and the cathode A current of 120 A is passed between the Al—Ti alloy electrode, which is an electrode (evaporation source), and the anode electrode to generate an arc discharge, and the target composition and the thin layer A having the target layer thickness shown in Table 4 ( An Al, Ti) N layer was deposited.
(D) Subsequently, nitrogen gas is introduced into the apparatus as a reaction gas to obtain a reaction atmosphere of 0.5 to 9.0 Pa, and a tool base that rotates while rotating on a rotary table is set to −20 to −500 V. A direct current bias voltage was applied, and a current of 120 A was passed between the Al—Cr alloy of the cathode electrode and the anode electrode to generate an arc discharge, and the target composition shown in Table 4 was formed on the surface of the tool base. After vapor-depositing the (Al, Cr) N layer as the thin layer B of the target layer thickness, the arc discharge between the cathode electrode (evaporation source) and the anode electrode is stopped,
By alternately repeating the steps (c) and (d), a hard coating layer having an alternate laminated structure having a total target layer thickness shown in Table 4 is formed on the tool substrate by vapor deposition. (Referred to as a coated insert of the present invention) 1 to 8 were produced. The formation conditions (bias voltage, nitrogen partial pressure) of each layer are also shown in Table 4. Furthermore, the Young's modulus and crystal structure of the comparative coated inserts 1 to 8 were measured by the same method as described above. The results are also shown in Table 4.
被削材：ＪＩＳ・Ｓ１０Ｃ（ＨＢ２００）の丸棒、
切削速度： ３２０ｍ／ｍｉｎ．、
切り込み： ２．５ｍｍ、
送り： ０．４５ｍｍ／ｒｅｖ．、
切削時間： １５分、
の条件（切削条件Ａ）での炭素鋼の乾式高速高送り切削加工試験（通常の切削速度および送りは、それぞれ、２００ｍ／ｍｉｎ．、０．２５ｍｍ／ｒｅｖ．）、
被削材：ＪＩＳ・ＳＣＭ４１５（ＨＢ２８０）の丸棒、
切削速度： ３００ｍ／ｍｉｎ．、
切り込み： ３．５ ｍｍ、
送り： ０．３ｍｍ／ｒｅｖ．、
切削時間： １２分、
の条件（切削条件Ｂ）での合金鋼の乾式高速高切込切削加工試験（通常の切削速度および切込は、それぞれ、１９０ｍ／ｍｉｎ．、２．０ｍｍ．）、
被削材：ＪＩＳ・ＳＣＭ４２０Ｈ（ＨＲＣ６１）の丸棒、
切削速度： １２０ｍ／ｍｉｎ．、
切り込み： ０．４ｍｍ、
送り： ０．２５ｍｍ／ｒｅｖ．、
切削時間： ８分、
の条件（切削条件Ｃ）での焼入鋼の乾式高速高切込・高送り切削加工試験（通常の切削速度、切込および送りは、それぞれ、６０ ｍ／ｍｉｎ．、０．２ｍｍ．、０．１ｍｍ／ｒｅｖ．）、
を行い、いずれの高速切削加工試験でも切刃の逃げ面摩耗幅を測定した。この測定結果を表５、表６に示した。
Work material: JIS S10C (HB200) round bar,
Cutting speed: 320 m / min. ,
Cutting depth: 2.5mm,
Feed: 0.45 mm / rev. ,
Cutting time: 15 minutes,
Of carbon steel under the above conditions (cutting conditions A) (normal cutting speed and feed are 200 m / min. And 0.25 mm / rev., Respectively),
Work material: JIS / SCM415 (HB280) round bar,
Cutting speed: 300 m / min. ,
Cutting depth: 3.5 mm,
Feed: 0.3 mm / rev. ,
Cutting time: 12 minutes,
Dry high-speed high-cut cutting test of alloy steel under the following conditions (cutting condition B) (normal cutting speed and cutting are 190 m / min. And 2.0 mm., Respectively),
Work material: JIS / SCM420H (HRC61) round bar,
Cutting speed: 120 m / min. ,
Cutting depth: 0.4mm,
Feed: 0.25 mm / rev. ,
Cutting time: 8 minutes,
(High cutting speed, cutting and feed are 60 m / min., 0.2 mm., 0 respectively) .1 mm / rev.),
The flank wear width of the cutting edge was measured in any high-speed cutting test. The measurement results are shown in Tables 5 and 6.
実施例１と同様、いずれも１〜３μｍの平均粒径を有するＷＣ粉末、ＴｉＣ粉末、ＺｒＣ粉末、ＶＣ粉末、ＴａＣ粉末、ＮｂＣ粉末、Ｃｒ３Ｃ２粉末、ＴｉＮ粉末、ＴａＮ粉末、およびＣｏ粉末からなる原料粉末を、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、１００ＭＰａの圧力で圧粉体にプレス成形し、この圧粉体を６Ｐａの真空中、温度：１４００℃に１時間保持の条件で焼結し、直径が１３ｍｍの工具基体形成用丸棒焼結体を形成し、さらに前記の丸棒焼結体から、研削加工にて、切刃部の直径×長さが１０ｍｍ×２２ｍｍの寸法、並びにねじれ角３０度の４枚刃スクエア形状をもったＷＣ基超硬合金製の工具基体（エンドミル）Ａ−１〜Ａ−１０をそれぞれ製造した。 As in Example 1, all of WC powder, TiC powder, ZrC powder, VC powder, TaC powder, NbC powder, Cr 3 C 2 powder, TiN powder, TaN powder, and Co powder having an average particle diameter of 1 to 3 μm. The raw material powder consisting of the above is blended in the composition shown in Table 1, wet mixed for 72 hours with a ball mill, dried, and then pressed into a green compact at a pressure of 100 MPa. , Temperature: Sintered at 1400 ° C. for 1 hour to form a round tool sintered body for forming a tool base having a diameter of 13 mm. WC-base cemented carbide tool bases (end mills) A-1 to A-10 having a four-blade square shape with a diameter x length of 10 mm x 22 mm and a twist angle of 30 degrees were manufactured, respectively. .
ついで、これらの工具基体（エンドミル）Ａ−１〜Ａ−１０の表面をアセトン中で超音波洗浄し、乾燥した状態で、同じく図１に示されるアークイオンプレーティング装置に装入し、実施例１と同一の条件で、表７に示される目標組成、目標層厚、ヤング率、結晶構造の（Ａｌ，Ｔｉ）Ｎ層からなる薄層Ａと、表７に示される目標組成、目標層厚、ヤング率、結晶構造の（Ａｌ，Ｃｒ）Ｎ層からなる薄層Ｂとの交互積層構造からなる表７に示される目標総層厚の硬質被覆層を蒸着形成することにより、本発明被覆工具としての本発明表面被覆超硬製エンドミル（以下、本発明被覆エンドミルと云う）１〜１０をそれぞれ製造した。 Then, the surfaces of these tool bases (end mills) A-1 to A-10 were ultrasonically cleaned in acetone and dried, and then charged into the arc ion plating apparatus shown in FIG. 1, the target composition, target layer thickness, Young's modulus, thin layer A composed of (Al, Ti) N layer of crystal structure shown in Table 7, and target composition, target layer thickness shown in Table 7 The coated tool of the present invention is formed by vapor-depositing a hard coating layer having a target total layer thickness shown in Table 7 consisting of an alternately laminated structure with a thin layer B consisting of an (Al, Cr) N layer having a Young's modulus and crystal structure The present invention surface-coated carbide end mills (hereinafter referred to as the present invention-coated end mills) 1 to 10 were produced.
また、比較の目的で、前記工具基体（エンドミル）Ａ−１〜Ａ−５の表面をアセトン中で超音波洗浄し、乾燥した状態で、同じく図１に示されるアークイオンプレーティング装置に装入し、実施例１と同様工程で、表８に示される形成条件（バイアス電圧、窒素分圧）を用いて、表８に示される目標組成、目標層厚、ヤング率、結晶構造の（Ａｌ，Ｔｉ）Ｎ層からなる薄層Ａと、表８に示される目標組成、目標層厚、ヤング率、結晶構造の（Ａｌ，Ｃｒ）Ｎ層からなる薄層Ｂとの交互積層構造からなる表８に示される目標総層厚の硬質被覆層を蒸着形成することにより、比較被覆工具としての表面被覆超硬製エンドミル（以下、比較被覆エンドミルと云う）１〜５をそれぞれ製造した。
つぎに、本発明被覆エンドミル１〜１０および比較被覆エンドミル１〜５について、
被削材−平面寸法：１００ ｍｍ×２５０ ｍｍ、厚さ：５０ ｍｍのＪＩＳ・Ｓ１０Ｃ（ＨＢ２００）の板材、
切削速度： ３２０ｍ／ｍｉｎ．、
溝深さ（切り込み）：５．０ｍｍ、
テーブル送り： ２２００ｍｍ／ｍｉｎ．、
の条件（切削条件Ｄ）での炭素鋼の乾式高速溝切削加工試験（通常の切削速度およびテーブル送りは、それぞれ、２００ｍ／ｍｉｎ．、１４００ｍｍ／ｍｉｎ．）、
被削材−平面寸法：１００ｍｍ×２５０ ｍｍ、厚さ：５０ｍｍのＪＩＳ・ＳＣＭ４１５（ＨＢ２８０）の板材、
切削速度： ２７０ｍ／ｍｉｎ．、
溝深さ（切り込み）：３．０ｍｍ、
テーブル送り： ２０００ｍｍ／ｍｉｎ．、
の条件（切削条件Ｅ）での合金鋼の乾式高速溝切削加工試験（通常の切削速度およびテーブル送りは、それぞれ、１５０ｍ／ｍｉｎ．、１４００ｍｍ／ｍｉｎ．）、
被削材−平面寸法：１００ｍｍ×２５０ｍｍ、厚さ：５０ｍｍのＪＩＳ・ＳＣＭ４２０Ｈ（ＨＲＣ６１）の板材、
切削速度： １２０ｍ／ｍｉｎ．、
溝深さ（切り込み）：１．０ｍｍ、
テーブル送り： ３２０ｍｍ／ｍｉｎ．、
の条件（切削条件Ｆ）での焼入鋼の乾式高速溝切削加工試験（通常の切削速度およびテーブル送りは、それぞれ、５０ｍ／ｍｉｎ．、２１０ｍｍ／ｍｉｎ．）、
をそれぞれ行い、いずれの高速溝切削加工試験でも切刃部の外周刃の逃げ面摩耗幅が使用寿命の目安とされる０．１ｍｍに至るまでの切削溝長を測定した。この測定結果を同じく表７、表８にそれぞれ示した。
For comparison purposes, the surfaces of the tool bases (end mills) A-1 to A-5 are ultrasonically cleaned in acetone and dried, and then loaded into the arc ion plating apparatus shown in FIG. In the same process as in Example 1, using the formation conditions (bias voltage, nitrogen partial pressure) shown in Table 8, the target composition, target layer thickness, Young's modulus, crystal structure (Al, Table 8 consisting of an alternating layered structure of a thin layer A consisting of Ti) N layers and a thin layer B consisting of (Al, Cr) N layers of the target composition, target layer thickness, Young's modulus and crystal structure shown in Table 8. Surface-coated carbide end mills (hereinafter referred to as comparative coated end mills) 1 to 5 as comparative coated tools were produced by vapor-depositing a hard coating layer having a target total layer thickness shown in FIG.
Next, for the present invention coated end mills 1-10 and comparative coated end mills 1-5,
Work material-planar dimensions: 100 mm × 250 mm, thickness: 50 mm JIS / S10C (HB200) plate material,
Cutting speed: 320 m / min. ,
Groove depth (cut): 5.0 mm,
Table feed: 2200 mm / min. ,
Carbon steel dry high-speed grooving test under normal conditions (cutting conditions D) (normal cutting speed and table feed are 200 m / min. And 1400 mm / min., Respectively),
Work material-planar dimensions: 100 mm × 250 mm, thickness: 50 mm JIS / SCM415 (HB280) plate material,
Cutting speed: 270 m / min. ,
Groove depth (cut): 3.0 mm,
Table feed: 2000 mm / min. ,
(High cutting speed and table feed are 150 m / min. And 1400 mm / min., Respectively)
Work material-planar dimensions: 100 mm × 250 mm, thickness: 50 mm JIS / SCM420H (HRC61) plate material,
Cutting speed: 120 m / min. ,
Groove depth (cut): 1.0 mm,
Table feed: 320 mm / min. ,
(High cutting speed and table feed are 50 m / min and 210 mm / min, respectively)
In each high-speed groove cutting test, the cutting groove length was measured until the flank wear width of the outer peripheral edge of the cutting edge reached 0.1 mm, which is a guide for the service life. The measurement results are shown in Table 7 and Table 8, respectively.
実施例２で製造した直径が１３ｍｍの丸棒焼結体を用い、この丸棒焼結体から、研削加工にて、溝形成部の直径×長さがそれぞれ８ｍｍ×２２ｍｍの寸法、並びにねじれ角３０度の２枚刃形状をもったＷＣ基超硬合金製の工具基体（ドリル）Ａ−１〜Ａ−１０をそれぞれ製造した。 The round bar sintered body with a diameter of 13 mm manufactured in Example 2 was used, and from this round bar sintered body, the dimensions of the groove forming part diameter × length were 8 mm × 22 mm and the twist angle by grinding. WC-base cemented carbide tool bases (drills) A-1 to A-10 having a 30-degree two-blade shape were produced, respectively.
ついで、これらの工具基体（ドリル）Ａ−１〜Ａ−１０の切刃に、ホーニングを施し、アセトン中で超音波洗浄し、乾燥した状態で、同じく図１に示されるアークイオンプレーティング装置に装入し、実施例１と同一の条件で、表９に示される目標組成、目標層厚およびヤング率の（Ａｌ，Ｔｉ）Ｎ層からなる薄層Ａと、同じく表９に示される目標組成、目標層厚およびヤング率の（Ａｌ，Ｃｒ）Ｎ層からなる薄層Ｂとの交互積層構造からなる同じく表９に示される目標総層厚の硬質被覆層を蒸着形成することにより、本発明被覆工具としての本発明表面被覆超硬製ドリル（以下、本発明被覆ドリルと云う）１〜１０をそれぞれ製造した。 Next, the cutting edges of these tool bases (drills) A-1 to A-10 are subjected to honing, ultrasonically cleaned in acetone, and dried to the arc ion plating apparatus shown in FIG. Under the same conditions as in Example 1, the target composition, the target layer thickness and the thin layer A composed of the (Al, Ti) N layer having the target layer thickness and Young's modulus shown in Table 9, and the target composition also shown in Table 9 are used. The present invention is achieved by vapor-depositing a hard coating layer having a target total layer thickness shown in Table 9 and having an alternately laminated structure with a thin layer B made of an (Al, Cr) N layer having a target layer thickness and Young's modulus. The surface-coated carbide drills of the present invention (hereinafter referred to as the present invention-coated drills) 1 to 10 as coated tools were produced, respectively.
また、比較の目的で、前記工具基体（ドリル）Ａ−１〜Ａ−５の表面に、ホーニングを施し、アセトン中で超音波洗浄し、乾燥した状態で、同じく図１に示されるアークイオンプレーティング装置に装入し、実施例１と同様工程で、表１０に示される形成条件（バイアス電圧、窒素分圧）を用いて、表１０に示される目標組成、目標層厚、ヤング率、結晶構造の（Ａｌ，Ｔｉ）Ｎ層からなる薄層Ａと、表１０に示される目標組成、目標層厚、ヤング率、結晶構造の（Ａｌ，Ｃｒ）Ｎ層からなる薄層Ｂとの交互積層構造からなる表１０に示される目標総層厚の硬質被覆層を蒸着形成することにより、比較被覆工具としての表面被覆超硬製ドリル（以下、比較被覆ドリルと云う）１〜５をそれぞれ製造した。 For comparison purposes, the surfaces of the tool bases (drills) A-1 to A-5 are subjected to honing, ultrasonically cleaned in acetone and dried, and the arc ion plate shown in FIG. The target composition, target layer thickness, Young's modulus, and crystal shown in Table 10 were charged in the same process as in Example 1 using the formation conditions (bias voltage and nitrogen partial pressure) shown in Table 10 in the same process as Example 1. Alternating lamination of thin layer A composed of (Al, Ti) N layers having a structure and thin layer B composed of (Al, Cr) N layers having a target composition, target layer thickness, Young's modulus and crystal structure shown in Table 10 Surface-coated carbide drills (hereinafter referred to as comparative coated drills) 1 to 5 as comparative coated tools were manufactured by vapor-depositing a hard coated layer having a target total layer thickness shown in Table 10 having a structure. .
つぎに、本発明被覆ドリル１〜１０および比較被覆ドリル１〜５について、
被削材−平面寸法：１００ｍｍ×２５０ｍｍ、厚さ：５０ｍｍのＪＩＳ・Ｓ１０Ｃ（ＨＢ２００）の板材、
切削速度： １９０ｍ／ｍｉｎ．、
送り： ０．４５ｍｍ／ｒｅｖ．、
穴深さ： ６ｍｍ、
の条件（切削条件Ｇ）での炭素鋼の乾式高速穴あけ加工試験（通常の切削速度および送りは、それぞれ、１００ｍ／ｍｉｎ．、０．３ｍｍ／ｒｅｖ．）、
被削材−平面寸法：１００ｍｍ×２５０ｍｍ、厚さ：５０ｍｍのＪＩＳ・ＳＣＭ４１５（ＨＢ２８０）の板材、
切削速度： １５０ｍ／ｍｉｎ．、
送り： ０．４０ｍｍ／ｒｅｖ．、
穴深さ： ６ｍｍ、
の条件（切削条件Ｈ）での合金鋼の乾式高速穴あけ加工試験（通常の切削速度および送りは、それぞれ、８０ｍ／ｍｉｎ．、０．２５ｍｍ／ｒｅｖ．）、
被削材−平面寸法：１００ｍｍ×２５０ｍｍ、厚さ：５０ｍｍのＪＩＳ・ＳＣＭ４２０Ｈ（ＨＲＣ６１）の板材、
切削速度： ６５ｍ／ｍｉｎ．、
送り： ０．２５ｍｍ／ｒｅｖ．、
穴深さ： ６ｍｍ、
の条件（切削条件Ｉ）での焼入鋼の乾式高速穴あけ加工試験（通常の切削速度および送りは、それぞれ、３０ｍ／ｍｉｎ．、０．１２ｍｍ／ｒｅｖ．）、
をそれぞれ行い、いずれの乾式高速穴あけ加工試験でも先端切刃面の逃げ面摩耗幅が０．３ｍｍに至るまでの穴あけ加工数を測定した。この測定結果を同じく表９、表１０にそれぞれ示した。
Next, for the present invention coated drills 1-10 and comparative coated drills 1-5,
Work material-Plane dimension: 100 mm x 250 mm, thickness: 50 mm JIS S10C (HB200) plate material,
Cutting speed: 190 m / min. ,
Feed: 0.45 mm / rev. ,
Hole depth: 6mm,
Carbon steel dry high speed drilling test under normal conditions (cutting condition G) (normal cutting speed and feed are 100 m / min. And 0.3 mm / rev., Respectively),
Work material-Plane dimension: 100 mm x 250 mm, thickness: 50 mm JIS / SCM415 (HB280) plate material,
Cutting speed: 150 m / min. ,
Feed: 0.40 mm / rev. ,
Hole depth: 6mm,
(High cutting speed and feed are 80 m / min. And 0.25 mm / rev., Respectively)
Work material-planar dimensions: 100 mm × 250 mm, thickness: 50 mm JIS / SCM420H (HRC61) plate material,
Cutting speed: 65 m / min. ,
Feed: 0.25 mm / rev. ,
Hole depth: 6mm,
(High cutting speed and feed rate are 30 m / min. And 0.12 mm / rev., Respectively)
In each dry high-speed drilling test, the number of drilling processes until the flank wear width of the tip cutting edge surface reached 0.3 mm was measured. The measurement results are also shown in Table 9 and Table 10, respectively.
この結果得られた本発明被覆工具としての本発明被覆インサート１〜１６、本発明被覆エンドミル１〜１０、および本発明被覆ドリル１〜１０の硬質被覆層を構成する薄層Ａである（Ａｌ，Ｔｉ）Ｎ層と薄層Ｂである（Ａｌ，Ｃｒ）Ｎ層の組成、並びに、比較被覆工具としての比較被覆インサート１〜８、比較被覆エンドミル１〜５、および比較被覆ドリル１〜５の硬質被覆層を構成する薄層Ａである（Ａｌ，Ｔｉ）Ｎ層と薄層Ｂである（Ａｌ，Ｃｒ）Ｎ層の組成を、透過型電子顕微鏡を用いてのエネルギー分散Ｘ線分析法により測定したところ、それぞれ目標組成と実質的に同じ組成を示した。 As a result of this, it is a thin layer A constituting the hard coating layer of the present invention coated inserts 1-16 as the present invention coated tool, the present coated end mill 1-10, and the present coated drill 1-10 (Al, Composition of Ti) N layer and (Al, Cr) N layer as thin layer B, and comparative coated inserts 1-8 as comparative coated tools, comparative coated end mills 1-5, and comparative coated drills 1-5 hard The composition of the (Al, Ti) N layer, which is a thin layer A and the (Al, Cr) N layer, which is a thin layer B constituting the coating layer, is measured by energy dispersive X-ray analysis using a transmission electron microscope. As a result, each showed substantially the same composition as the target composition.
また、前記硬質被覆層を構成する各層の平均層厚を走査型電子顕微鏡を用いて断面測定したところ、いずれも目標層厚と実質的に等しい平均層厚（５ヶ所の平均値）を示した。 Moreover, when the average layer thickness of each layer which comprises the said hard coating layer was cross-sectional measured using the scanning electron microscope, all showed the average layer thickness (average value of five places) substantially equal to target layer thickness. .
表３〜１０に示される結果から、本発明被覆工具は、所定の組成、目標層厚、ヤング率の薄層Ａと、所定の組成、目標層厚の薄層Ｂとからなる交互積層構造を有する硬質被覆層を形成した結果、薄層Ａである（Ａｌ，Ｔｉ）Ｎ層によって、工具基体表面に強固に密着接合した状態で、耐欠損性、高温硬さ、高温強度が向上し、薄層Ｂである高ヤング率の（Ａｌ，Ｃｒ）Ｎ層がすぐれた耐熱性および耐摩耗性を有するとともに、組成が異なる薄層Ａと薄層Ｂとの交互積層による相乗効果によって、耐衝撃性、耐チッピング性、耐クラック進展性を向上させる結果、軟鋼、一般鋼、高硬度鋼等の高速切削加工でも、すぐれた耐欠損性が確保され、チッピングの発生なく、長期に亘ってすぐれた耐摩耗性を発揮する。これに対して、硬質被覆層として、組成が異なる薄層Ａと薄層Ｂとの交互積層構造を有するものの、薄層Ｂの（Ａｌ，Ｃｒ）Ｎ層のヤング率が制御されていないか、各層の組成、目標層厚が本発明で規定する範囲を逸脱する比較被覆工具においては、いずれも軟鋼、一般鋼、高硬度鋼等の高速切削加工では、耐摩耗性が十分でなく、かつ皮膜の靭性が低下するために、切刃部にチッピングが発生するようになり、比較的短時間で使用寿命に至ることが明らかである。 From the results shown in Tables 3 to 10, the coated tool of the present invention has an alternately laminated structure including a thin layer A having a predetermined composition, a target layer thickness, and a Young's modulus, and a thin layer B having a predetermined composition and a target layer thickness. As a result of forming the hard coating layer having the above, the (Al, Ti) N layer, which is the thin layer A, improves the chipping resistance, high-temperature hardness, and high-temperature strength in a tightly bonded state to the surface of the tool substrate. The high Young's modulus (Al, Cr) N layer, which is layer B, has excellent heat resistance and wear resistance, and also has impact resistance due to the synergistic effect of alternately laminating thin layers A and B having different compositions. As a result of improving chipping resistance and crack progress resistance, excellent chipping resistance is ensured even in high-speed cutting such as mild steel, general steel, and high hardness steel, and chipping does not occur and excellent long-term resistance. Exhibits abrasion. On the other hand, as a hard coating layer, although it has an alternating layered structure of thin layers A and thin layers B having different compositions, the Young's modulus of the (Al, Cr) N layer of the thin layer B is not controlled, In the comparative coated tool whose composition of each layer and target layer thickness deviate from the range specified in the present invention, the wear resistance is not sufficient in high-speed cutting such as mild steel, general steel, high hardness steel, etc. It is clear that chipping occurs at the cutting edge due to the lowering of the toughness, and the service life is reached in a relatively short time.
前述のように、本発明の被覆工具は、一般的な被削材の切削加工は勿論のこと、特に、軟鋼、一般鋼、高硬度鋼等の高速切削加工でもすぐれた耐摩耗性と耐欠損性を発揮し、長期に亘ってすぐれた切削性能を示すものであるから、切削加工装置の自動化、並びに切削加工の省力化および省エネ化、さらに低コスト化に十分満足に対応できるものである。 As described above, the coated tool of the present invention is excellent in wear resistance and fracture resistance not only in cutting of general work materials, but also in high-speed cutting of soft steel, general steel, hard steel, etc. Since it exhibits excellent cutting performance and exhibits excellent cutting performance over a long period of time, it can satisfactorily respond to automation of the cutting apparatus, labor saving and energy saving of cutting, and cost reduction.
Claims (1)
前記硬質被覆層が、
（ａ）０．１〜１．０μｍの平均層厚を有し、かつ、
組成式：（Ａｌ１−ｙＴｉｙ）Ｎ（ここで、ｙはＡｌとＴｉの合量に占めるＴｉの含有割合を示し、原子比で、０．２５≦ｙ≦０．５５である）を満足し、ヤング率ａが４００ＧＰａ≦ａ≦５５０ＧＰａであるＡｌとＴｉとの複合窒化物層からなる薄層Ａと、
（ｂ）０．１〜１．０μｍの平均層厚を有し、かつ、
組成式：（Ａｌ１−ｘＣｒｘ）Ｎ（ここで、ｘはＡｌとＣｒの合量に占めるＣｒの含有割合を示し、原子比で、０．２５≦ｘ≦０．５０である）を満足し、ヤング率ｂが５００ＧＰａ≦ｂ≦８００ＧＰａであり、且つ、前記薄層Ａのヤング率よりも１００ＧＰａ以上大きいＡｌとＣｒとの複合窒化物層からなる薄層Ｂと、
（ｃ）工具基体直上が薄層Ａであり、薄層Ａと薄層Ｂとの交互積層構造を有し、総平均層厚が１．０〜１０μｍである、
前記（ａ）〜（ｃ）の条件を満たすことを特徴とする表面被覆切削工具。
In a surface-coated cutting tool formed by forming a hard coating layer on the surface of a tool base composed of tungsten carbide-based cemented carbide or titanium carbonitride-based cermet,
The hard coating layer is
(A) having an average layer thickness of 0.1 to 1.0 μm, and
Composition formula: (Al 1-y Ti y ) N (where y represents the content ratio of Ti in the total amount of Al and Ti, and the atomic ratio is 0.25 ≦ y ≦ 0.55) Satisfied, a thin layer A composed of a composite nitride layer of Al and Ti having a Young's modulus a of 400 GPa ≦ a ≦ 550 GPa,
(B) having an average layer thickness of 0.1 to 1.0 μm, and
Composition formula: (Al 1-x Cr x ) N (where x represents the content ratio of Cr in the total amount of Al and Cr, and the atomic ratio is 0.25 ≦ x ≦ 0.50) Satisfied, a thin layer B composed of a composite nitride layer of Al and Cr having a Young's modulus b of 500 GPa ≦ b ≦ 800 GPa and greater than the Young's modulus of the thin layer A by 100 GPa,
(C) Immediately above the tool substrate is the thin layer A, and has an alternate laminated structure of the thin layer A and the thin layer B, and the total average layer thickness is 1.0 to 10 μm.
A surface-coated cutting tool characterized by satisfying the conditions (a) to (c).
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| EP3842170A4 (en) * | 2018-08-24 | 2021-12-15 | Sumitomo Electric Hardmetal Corp. | Cutting tool |
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