JP5234332B2 - A surface-coated cutting tool that exhibits excellent chipping resistance with a hard coating layer in high-speed, high-feed cutting. - Google Patents
A surface-coated cutting tool that exhibits excellent chipping resistance with a hard coating layer in high-speed, high-feed cutting. Download PDFInfo
- Publication number
- JP5234332B2 JP5234332B2 JP2008139300A JP2008139300A JP5234332B2 JP 5234332 B2 JP5234332 B2 JP 5234332B2 JP 2008139300 A JP2008139300 A JP 2008139300A JP 2008139300 A JP2008139300 A JP 2008139300A JP 5234332 B2 JP5234332 B2 JP 5234332B2
- Authority
- JP
- Japan
- Prior art keywords
- cutting
- tool
- hard coating
- speed
- feed
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Expired - Fee Related
Links
Images
Landscapes
- Drilling Tools (AREA)
- Cutting Tools, Boring Holders, And Turrets (AREA)
- Physical Vapour Deposition (AREA)
Description
この発明は、例えば、合金工具鋼の焼入れ材、高硬度ステンレス鋼などの高硬度被削材を、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高送り条件で切削加工した場合に、硬質被覆層がすぐれた潤滑性と耐チッピング性を発揮する表面被覆切削工具（以下、被覆工具という）に関するものである。 The present invention, for example, cuts high-hardness work materials such as hardened alloy tool steels and high-hardness stainless steel under high-speed and high-feed conditions that generate high heat and place a large mechanical load on the cutting edge. In this case, the present invention relates to a surface-coated cutting tool (hereinafter referred to as a coated tool) in which a hard coating layer exhibits excellent lubricity and chipping resistance.
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スローアウエイチップ、前記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、さらに前記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、また前記スローアウエイチップを着脱自在に取り付けて前記ソリッドタイプのエンドミルと同様に切削加工を行うスローアウエイエンドミル工具などが知られている。 In general, for coated tools, throwaway inserts that are detachably attached to the tip of the cutting tool for turning and planing of various steel and cast iron materials, drilling of the work material, etc. Drills and miniature drills, and solid type end mills used for chamfering, grooving and shouldering of the work material, etc. A slow-away end mill tool that performs cutting work in the same manner as an end mill is known.
また、被覆工具としては、例えば、工具基体表面に、ＴｉとＡｌの複合窒化物（（Ｔｉ，Ａｌ）Ｎ）層、あるいは、これにさらに、Ｓｉ、Ｂ、Ｙ、Ｚｒ、Ｖ等を微量添加含有させたＴｉとＡｌを主成分とする複合窒化物（以下、これらを総称して、（Ｔｉ，Ａｌ，Ｍ）Ｎという）層を設けた被覆工具も知られており、特に、構成成分であるＡｌによって高温硬さと耐熱性、同Ｔｉによって高温強度を具備することから、上記（Ｔｉ，Ａｌ，Ｍ）Ｎ層がすぐれた高温強度、耐欠損性、耐摩耗性を示すことも知られている。 As a coated tool, for example, a Ti and Al composite nitride ((Ti, Al) N) layer or a small amount of Si, B, Y, Zr, V, etc. is added to the tool base surface. A coated tool provided with a composite nitride mainly containing Ti and Al (hereinafter collectively referred to as (Ti, Al, M) N) is also known. It is also known that the above (Ti, Al, M) N layer exhibits excellent high temperature strength, fracture resistance, and wear resistance because it has high temperature hardness and heat resistance with certain Al and high temperature strength with the same Ti. Yes.
さらに、上記の従来被覆工具が、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、装置内を、例えば５００℃の温度に加熱した状態で、硬質被覆層の組成に対応した合金がセットされたカソード電極、例えば、Ｔｉ−Ａｌ−Ｍ合金と、アノード電極との間に、例えば電流：９０Ａ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２Ｐａの反応雰囲気とし、一方、上記工具基体には、例えば−１００Ｖのバイアス電圧を印加した条件で、前記工具基体表面に、（Ｔｉ，Ａｌ，Ｍ）Ｎ層からなる硬質被覆層を蒸着することにより製造されることも知られている。
近年の切削加工装置のＦＡ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に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、上記の従来被覆工具においては、これを、合金工具鋼の焼入れ材、高硬度ステンレス鋼などの高硬度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、これらの被削材を、高い発熱をともなうとともに、切刃部に局部的に高負荷がかかる高速高送り条件で切削した場合には、切削時の発熱によって被削材および切粉は高温に加熱されて粘性が増大し、これに伴って硬質被覆層表面に対する溶着性が一段と増すようになり、この結果切刃部におけるチッピング（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。 In recent years, the use of FA for cutting devices has been remarkable. On the other hand, there is a strong demand for labor saving, energy saving, and cost reduction for cutting processing. As a result, cutting tools are affected as much as possible by the material type of the work material. There is a tendency not to be versatile, that is, there is a tendency to demand a cutting tool capable of cutting as many grades as possible. However, in the above-mentioned conventional coated tools, this is used as a hardened material of alloy tool steel, high hardness stainless steel, etc. There is no problem when using these materials for cutting at high cutting speeds at normal cutting speeds, but these materials have high heat generation and high speed and high local load on the cutting edge. When cutting under feed conditions, the work material and chips are heated to a high temperature due to the heat generated during cutting, and the viscosity increases. With this, the weldability to the surface of the hard coating layer further increases. result Chipping (minute chipping) in the blade portion is rapidly increased, which is at present, leading to a relatively short time service life due.
そこで、本発明者等は、上述のような観点から、特に合金工具鋼の焼入れ材、高硬度ステンレス鋼などの高硬度被削材の切削加工を、高速高送り切削条件で切削加工した場合に、硬質被覆層がすぐれた潤滑性とすぐれた耐チッピング性を発揮する被覆工具を開発すべく、上記の従来被覆工具に着目し、研究を行った結果、
ＷＣ基超硬合金またはＴｉＣＮ基サーメットからなる工具基体の表面に、一層平均層厚０．０１〜０．１μｍの（Ｔｉ，Ａｌ，Ｍ）Ｎ薄層を蒸着形成し、この上に、Ｃｒとの合量に占めるＹの含有割合が１〜１０原子％となるようにＹ成分を含有させたＣｒとＹの複合窒化物層（以下、（Ｃｒ，Ｙ）Ｎ層で示す）からなる一層平均層厚０．０１〜０．１μｍの（Ｃｒ，Ｙ）Ｎ薄層を蒸着形成し、さらに、上記（Ｔｉ，Ａｌ，Ｍ）Ｎ薄層と上記（Ｃｒ，Ｙ）Ｎ薄層とを交互に形成し、交互積層構造からなる硬質被覆層を構成すると、（Ｔｉ，Ａｌ，Ｍ）Ｎ薄層はすぐれた高温硬さ、高温強度、耐熱性を示し、また、これと交互に積層形成される（Ｃｒ，Ｙ）Ｎ薄層はすぐれた潤滑性を示し、特に、（Ｃｒ，Ｙ）Ｎ薄層中に含有されるＹ成分によって、（Ｃｒ，Ｙ）Ｎ薄層の耐熱性が向上することから、高熱発生を伴う切削加工においても、（Ｃｒ，Ｙ）Ｎ薄層のすぐれた潤滑性は維持されることを見出した。
In view of the above, the present inventors, in particular, in the case of cutting high-hardness work materials such as hardened materials of alloy tool steel and high-hardness stainless steel under high-speed high-feed cutting conditions. In order to develop a coated tool that exhibits excellent lubricity and excellent chipping resistance, the hard coating layer focuses on the above-mentioned conventional coated tools, and as a result of research,
A thin (Ti, Al, M) N layer having an average layer thickness of 0.01 to 0.1 μm is vapor-deposited on the surface of a tool base made of a WC-based cemented carbide or TiCN-based cermet, and Cr and One-layer average composed of a composite nitride layer of Cr and Y (hereinafter referred to as (Cr, Y) N layer) containing Y component so that the Y content in the total amount of 1 to 10 atomic% A (Cr, Y) N thin layer having a thickness of 0.01 to 0.1 μm is formed by vapor deposition, and the (Ti, Al, M) N thin layer and the (Cr, Y) N thin layer are alternately formed. When a hard coating layer having an alternating laminated structure is formed, the (Ti, Al, M) N thin layer exhibits excellent high-temperature hardness, high-temperature strength, and heat resistance, and is alternately laminated. The (Cr, Y) N thin layer exhibits excellent lubricity, and in particular, due to the Y component contained in the (Cr, Y) N thin layer. Thus, the heat resistance of the (Cr, Y) N thin layer is improved, and thus it has been found that the excellent lubricity of the (Cr, Y) N thin layer is maintained even in the cutting process with high heat generation.
したがって、工具表面に溶着し易い低中硬度被削材の高速高送り切削加工において、切刃部が高温になったとしても、（Ｔｉ，Ａｌ，Ｍ）Ｎ薄層に不足する潤滑性を、これと交互に積層される（Ｃｒ，Ｙ）Ｎ薄層が補完し、硬質被覆層全体としての被削材との耐溶着性も改善され、その結果、切刃部におけるチッピング（微少欠け）の発生が防止され、長期に亘ってすぐれた耐摩耗性が発揮されることを見出し、本発明に至ったものである。 Therefore, in the high-speed high-feed cutting of a low-medium hardness work material that is easily welded to the tool surface, even if the cutting edge becomes high temperature, the lubricity that is insufficient for the (Ti, Al, M) N thin layer, The (Cr, Y) N thin layers that are alternately stacked complement each other, and the welding resistance to the work material as the entire hard coating layer is improved. As a result, chipping (slight chipping) at the cutting edge portion is improved. The inventors have found that generation is prevented and excellent wear resistance is exhibited over a long period of time, and the present invention has been achieved.
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、
「（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、
（ａ）０．０１〜０．１μｍの一層平均層厚を有し、かつ、
組成式：（Ｔｉ１−αＡｌα）Ｎ（但し、αはＡｌの含有割合を示し、原子比で、０．４５≦α≦０．７５である）を満足するＴｉとＡｌの複合窒化物層からなる（Ｔｉ，Ａｌ）Ｎ薄層、
（ｂ）０．０１〜０．１μｍの一層平均層厚を有し、かつ、
組成式：（Ｃｒ１−γＹγ）Ｎ（但し、γはＹの含有割合を示し、原子比で、０．０１≦γ≦０．１である）を満足するＣｒとＹの複合窒化物層からなる（Ｃｒ，Ｙ）Ｎ薄層、
上記（ａ）、（ｂ）の交互積層からなり、１〜５μｍの合計平均層厚を有する硬質被覆層を形成してなる、高速高送り切削加工で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切削工具。
（２） 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、
（ａ）０．０１〜０．１μｍの一層平均層厚を有し、かつ、
組成式：（Ｃｒ１−α−βＡｌαＭβ）Ｎ（ここで、Ｍは、Ｃｒを除く周期律表４ａ，５ａ，６ａ族の元素、Ｓｉ、Ｂ、Ｙのうちから選ばれた１種又は２種以上の添加成分を示し、また、αはＡｌの含有割合、βはＭの含有割合をそれぞれ示し、原子比で、０．４５≦α≦０．７５、０．０１≦β≦０．２５、α+β＜１．００である）を満足するＣｒとＡｌとＭの複合窒化物層からなる（Ｃｒ，Ａｌ，Ｍ）Ｎ薄層、
（ｂ）０．０１〜０．１μｍの一層平均層厚を有し、かつ、
組成式：（Ｃｒ１−γＹγ）Ｎ（但し、γはＹの含有割合を示し、原子比で、０．０１≦γ≦０．１である）を満足するＣｒとＹの複合窒化物層からなる（Ｃｒ，Ｙ）Ｎ薄層、
上記（ａ）、（ｂ）の交互積層からなり、１〜５μｍの合計平均層厚を有する硬質被覆層を形成してなる、高速高送り切削加工で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切削工具。」
に特徴を有するものである。
This invention was made based on the above research results,
“(1) On the surface of a tool base made of tungsten carbide-based cemented carbide or titanium carbonitride-based cermet,
(A) having an average layer thickness of 0.01 to 0.1 μm, and
Ti and Al composite nitride satisfying the composition formula: (Ti 1-α Al α ) N (where α is the Al content ratio and the atomic ratio is 0.45 ≦ α ≦ 0.75) (Ti, Al) N thin layer consisting of layers,
(B) having an average layer thickness of 0.01 to 0.1 μm, and
Cr and Y composite nitride satisfying the composition formula: (Cr 1-γ Y γ ) N (where γ represents the Y content and the atomic ratio is 0.01 ≦ γ ≦ 0.1) (Cr, Y) N thin layer consisting of layers,
Demonstrating excellent chipping resistance in high-speed, high-feed cutting, consisting of alternating layers (a) and (b) above, and forming a hard coating layer with a total average layer thickness of 1 to 5 μm A surface-coated cutting tool.
(2) On the surface of the tool base made of tungsten carbide-based cemented carbide or titanium carbonitride-based cermet,
(A) having an average layer thickness of 0.01 to 0.1 μm, and
Composition formula: (Cr 1-α-β Al α M β ) N (where M is one selected from elements of groups 4a, 5a, and 6a of the periodic table excluding Cr, Si, B, and Y) Seeds or two or more kinds of additive components, α is a content ratio of Al, β is a content ratio of M, and atomic ratio is 0.45 ≦ α ≦ 0.75, 0.01 ≦ β ≦ (Cr, Al, M) N thin layer comprising a composite nitride layer of Cr, Al and M satisfying 0.25 , α + β <1.00 )
(B) having an average layer thickness of 0.01 to 0.1 μm, and
Cr and Y composite nitride satisfying the composition formula: (Cr 1-γ Y γ ) N (where γ represents the Y content and the atomic ratio is 0.01 ≦ γ ≦ 0.1) (Cr, Y) N thin layer consisting of layers,
Demonstrating excellent chipping resistance in high-speed, high-feed cutting, consisting of alternating layers (a) and (b) above, and forming a hard coating layer with a total average layer thickness of 1 to 5 μm A surface-coated cutting tool. "
It has the characteristics.
つぎに、この発明の被覆工具の硬質被覆層について、詳細に説明する。 Next, the hard coating layer of the coated tool of the present invention will be described in detail.
（ａ）（Ｔｉ，Ａｌ，Ｍ）Ｎ薄層の組成および一層平均層厚
（Ｔｉ，Ａｌ，Ｍ）Ｎ薄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Ｔｉ成分には高温強度を向上させる作用があり、さらに、Ｍ成分のうちの、Ｔｉを除く周期律表４ａ，５ａ，６ａ族の元素、Ｓｉ、Ｂ、には硬質被覆層の耐摩耗性を向上させる作用があり、また、Ｙには硬質被覆層の高温耐酸化性を向上させる作用があるが、Ａｌの割合を示すα値がＴｉとの合量あるいはＴｉとＭの合量に占める割合（原子比、以下同じ）で０．４５未満になると、所定の高温硬さを確保することができず、これが耐摩耗性低下の原因となり、一方Ａｌの割合を示すα値が同０．７５を越えると、相対的にＴｉの含有割合が減少し、高速高送り切削加工で必要とされる高温強度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り、さらに、Ｍ成分の含有割合を示すβ値がＴｉとの合量に占める割合（原子比、以下同じ）で０．０１未満では、Ｍ成分を含有させたことによる耐摩耗性、高温耐酸化性等の特性向上が期待できず、一方同β値が０．２５を超えると、高温強度に低下傾向が現れるようになることから、α値を０．４５〜０．７５、β値を０．０１〜０．２５、かつ、（α+β）の値を１．００未満と定めた。
また、その一層平均層厚が０．０１μｍ未満では、自身のもつすぐれた耐摩耗性を長期に亘って発揮するには不十分であり、一方その一層平均層厚が０．１μｍを越えると、上記の高速高送り切削では、潤滑性の不足が顕在化し、切刃部にチッピングが発生し易くなることから、その一層平均層厚を０．０１〜０．１μｍと定めた。
(A) (Ti, Al, M) N thin layer composition and one layer average layer thickness (Ti, Al, M) Al component which is a constituent of N thin layer improves the high temperature hardness in the hard coating layer, The Ti component has the effect of improving the high-temperature strength. Further, among the M components, the elements of the periodic tables 4a, 5a and 6a excluding Ti, Si and B, wear resistance of the hard coating layer. Y has the effect of improving the high-temperature oxidation resistance of the hard coating layer, but the α value indicating the proportion of Al accounts for the total amount of Ti or the total amount of Ti and M. When the ratio (atomic ratio, the same applies hereinafter) is less than 0.45, the predetermined high-temperature hardness cannot be secured, which causes a decrease in wear resistance, while the α value indicating the Al ratio is the same as that of the same value. If it exceeds 75, the content ratio of Ti is relatively reduced, which is necessary for high-speed high-feed cutting. It is difficult to prevent the occurrence of chipping, and the β value indicating the content ratio of the M component occupies the total amount with Ti (atomic ratio, the same applies hereinafter). If it is less than 0.01, improvement in properties such as wear resistance and high-temperature oxidation resistance due to the inclusion of the M component cannot be expected. On the other hand, if the β value exceeds 0.25, the high-temperature strength tends to decrease. Since it appears, the α value was set to 0.45 to 0.75, the β value was set to 0.01 to 0.25 , and the value of (α + β) was set to less than 1.00 .
Further, if the average layer thickness is less than 0.01 μm, it is insufficient to exhibit its excellent wear resistance over a long period of time, while if the average layer thickness exceeds 0.1 μm, In the high-speed and high-feed cutting described above, insufficient lubricity becomes obvious and chipping is likely to occur at the cutting edge portion. Therefore, the average layer thickness is determined to be 0.01 to 0.1 μm.
（ｂ）（Ｃｒ，Ｙ）Ｎ薄層の組成および一層平均層厚
上記（Ｔｉ，Ａｌ，Ｍ）Ｎ薄層と交互積層構造を構成するＣｒとＹの複合窒化物層（（Ｃｒ，Ｙ）Ｎ層）は、所定の高温硬さ、高温強度、潤滑性を有するとともに、その構成成分であるＹ成分によって、すぐれた耐熱性を備えるようになり、そのため、（Ｔｉ，Ａｌ，Ｍ）Ｎ薄層に不足する潤滑性を補完し、高温切削条件下でも硬質被覆層の低摩擦係数が維持され、すぐれた潤滑性を発揮するようになる。ただ、Ｙの含有割合を示すγ値がＣｒとの合量に占める割合（原子比、以下同じ）で０．０１未満になると、耐熱性を確保することができないために潤滑効果を期待することはできず、一方、Ｙの割合を示すγ値が同０．１０を越えると、相対的にＣｒの含有割合が減少し、溶着性が高い高硬度被削材の高速高送り切削加工で必要とされる高温強度を確保することができないばかりか、潤滑性も低下し、チッピング発生を防止することが困難になることから、γ値を０．０１〜０．１０（原子比、以下同じ）と定めた。
また、交互積層を構成する（Ｃｒ，Ｙ）Ｎ層の一層平均層厚が０．０１μｍ未満では、自身のもつすぐれた耐熱性、潤滑性によって、硬質被覆層の特性を改善するには不十分であり、一方、一層平均層厚が０．１μｍを越えると、相対的な（Ｔｉ，Ａｌ，Ｍ）Ｎ薄層の割合の減少によって、硬質被覆層全体としての高温硬さ、高温強度が低下し、その結果、合金工具鋼の焼入れ材、高硬度ステンレス鋼などの高硬度被削材の高速高送り切削加工では切刃部にチッピングが発生し易くなるとともに摩耗も促進されることから、その一層平均層厚を０．０１〜０．１μｍと定めた。
(B) Composition and single layer average layer thickness of (Cr, Y) N thin layer Cr and Y composite nitride layer ((Cr, Y) constituting the (Ti, Al, M) N thin layer and an alternate laminated structure) N layer) has a predetermined high-temperature hardness, high-temperature strength, and lubricity, and also has excellent heat resistance due to its constituent Y component. Therefore, (Ti, Al, M) N thin Complementing the lack of lubricity of the layer, the low friction coefficient of the hard coating layer is maintained even under high-temperature cutting conditions, and excellent lubricity is exhibited. However, if the γ value indicating the Y content is less than 0.01 in the total amount with Cr (atomic ratio, the same shall apply hereinafter), heat resistance cannot be ensured and a lubricating effect is expected. On the other hand, if the γ value indicating the ratio of Y exceeds 0.10, it is necessary for high-speed high-feed cutting of high-hardness work materials with relatively low Cr content and high weldability. Not only can ensure the high temperature strength, but also the lubricity is lowered and it is difficult to prevent chipping, so the γ value is 0.01 to 0.10 (atomic ratio, the same applies hereinafter). It was determined.
In addition, if the average layer thickness of the (Cr, Y) N layers constituting the alternately laminated layers is less than 0.01 μm, it is insufficient to improve the characteristics of the hard coating layer due to its excellent heat resistance and lubricity. On the other hand, when the average layer thickness exceeds 0.1 μm, the high-temperature hardness and high-temperature strength of the entire hard coating layer decrease due to a decrease in the relative proportion of the (Ti, Al, M) N thin layer. As a result, in high-speed high-feed cutting of hardened materials such as hardened alloy tool steel and high-hardness stainless steel, chipping tends to occur at the cutting edge and wear is also promoted. The average layer thickness was determined to be 0.01 to 0.1 μm.
（ｃ）硬質被覆層の合計平均層厚
（Ｔｉ，Ａｌ，Ｍ）Ｎ薄層と（Ｃｒ，Ｙ）Ｎ薄層の交互積層構造からなる硬質被覆層は、その合計平均層厚が１μｍ未満では、硬質被覆層を構成する（Ｃｒ，Ｙ）Ｎ層の平均層厚が１μｍ未満では、長期の使用にわたって十分な耐摩耗性を発揮することができず、一方、合計平均層厚が５μｍを越えると、合金工具鋼の焼入れ材、高硬度ステンレス鋼などの高硬度被削材の高速高送り切削加工では切刃部にチッピングが発生し易くなることから、その合計平均層厚を１〜５μｍと定めた。
(C) Total average layer thickness of hard coating layer A hard coating layer composed of an alternating laminate structure of (Ti, Al, M) N thin layers and (Cr, Y) N thin layers has a total average layer thickness of less than 1 μm. When the average layer thickness of the (Cr, Y) N layer constituting the hard coating layer is less than 1 μm, sufficient wear resistance cannot be exhibited over a long period of use, while the total average layer thickness exceeds 5 μm. In addition, in the high-speed high-feed cutting of a hard material such as a hardened alloy tool steel or high-hardness stainless steel, chipping is likely to occur at the cutting edge, so the total average layer thickness is 1 to 5 μm. Determined.
（ｄ）そして、上記（Ｔｉ，Ａｌ，Ｍ）Ｎ薄層と（Ｃｒ，Ｙ）Ｎ薄層の交互積層は、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基体を装入し、ヒータで装置内を、例えば５００℃の温度に加熱した状態で、装置内に所定組成のＴｉ−Ａｌ−Ｍ合金からなるカソード電極（蒸発源）と、所定組成のＣｒ−Ｙ合金からなるカソード電極（蒸発源）とを配置し、まず、アノード電極とＴｉ−Ａｌ−Ｍ合金からなるカソード電極（蒸発源）との間に、例えば電流：９０Ａ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２Ｐａの反応雰囲気とし、一方、上記基体には、例えば−１００Ｖのバイアス電圧を印加した条件で、基体表面に（Ｔｉ，Ａｌ，Ｍ）Ｎ薄層を蒸着形成し、アーク放電を停止した後、引き続いて、アノード電極とＣｒ−Ｙ合金からなるカソード電極（蒸発源）との間に、前記と同様にアーク放電を行わせ、基体表面に（Ｃｒ，Ｙ）Ｎ薄層を蒸着形成し、上記操作を繰り返し行うことにより、所定の一層平均層厚の（Ｔｉ，Ａｌ，Ｍ）Ｎ薄層と（Ｃｒ，Ｙ）Ｎ薄層との交互積層構造からなる、所定合計平均層厚の硬質被覆層を蒸着形成することができる。 (D) Then, the alternate lamination of the (Ti, Al, M) N thin layer and the (Cr, Y) N thin layer is, for example, arc ion which is one type of physical vapor deposition apparatus schematically shown in FIG. The substrate is loaded into the plating apparatus, and the inside of the apparatus is heated to a temperature of, for example, 500 ° C. with a heater, and a cathode electrode (evaporation source) made of a Ti—Al—M alloy having a predetermined composition is disposed in the apparatus. A cathode electrode (evaporation source) made of a Cr—Y alloy having a composition is disposed, and first, between the anode electrode and a cathode electrode (evaporation source) made of a Ti—Al—M alloy, for example, at a current of 90 A. At the same time, an arc discharge is generated and nitrogen gas is introduced as a reaction gas into the apparatus to form a reaction atmosphere of, for example, 2 Pa. On the other hand, for example, a bias voltage of −100 V is applied to the substrate surface ( Ti, Al, M After the N thin layer is formed by vapor deposition and the arc discharge is stopped, the arc discharge is subsequently performed between the anode electrode and the cathode electrode (evaporation source) made of the Cr—Y alloy in the same manner as described above, and the substrate surface (Cr, Y) N thin layer is formed by vapor deposition, and the above operation is repeated to obtain a (Ti, Al, M) N thin layer and a (Cr, Y) N thin layer having a predetermined average layer thickness. A hard coating layer having a predetermined total average layer thickness composed of an alternating laminated structure can be formed by vapor deposition.
この発明の被覆工具は、交互積層構造からなる硬質被覆層を（Ｔｉ，Ａｌ，Ｍ）Ｎ薄層が、すぐれた高温硬さ、高温強度を有し、あるいは、さらにすぐれた耐摩耗性、高温耐酸化性を有し、また、（Ｃｒ，Ｙ）Ｎ薄層が、すぐれた潤滑性と耐熱性を兼ね備えていることから、硬質被覆層は全体として、すぐれた高温硬さ、高温強度等に加え、すぐれた潤滑性を備えたものとなり、その結果、特に銅合金、合金工具鋼の焼入れ材、高硬度ステンレス鋼などの高硬度被削材の、大きな発熱を伴い、かつ、切刃に対して高負荷のかかる高速高送り切削加工であっても、すぐれた耐チッピング性を示し、長期に亘ってすぐれた耐摩耗性を発揮するものである。 In the coated tool of the present invention, a hard coating layer having an alternately laminated structure (Ti, Al, M) N thin layer has excellent high-temperature hardness and high-temperature strength, or further excellent wear resistance and high-temperature. Since it has oxidation resistance and the (Cr, Y) N thin layer has excellent lubricity and heat resistance, the hard coating layer as a whole has excellent high temperature hardness, high temperature strength, etc. In addition, it has excellent lubricity, and as a result, it is accompanied by a large amount of heat generated from hard materials such as hardened materials of copper alloys, alloy tool steels, and high-hardness stainless steels. Even high-speed, high-feed cutting with high load exhibits excellent chipping resistance and exhibits excellent wear resistance over a long period of time.
つぎに、この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のチップ形状をもった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 in 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-based cemented carbide with ISO standard / CNMG120408 chip 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のチップ形状をもった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, the 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 base B made of TiCN-based cermet having an ISO standard / CNMG120408 chip shape was obtained. -1 to B-6 were formed.
（ａ）ついで、上記の工具基体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そって装着し、前記回転テーブルを挟んで相対向する両側にカソード電極（蒸発源）を配置し、その一方にはカソード電極（蒸発源）として所定組成のＴｉ−Ａｌ−Ｍ合金を配置し、また、その他方にはカソード電極（蒸発源）として所定組成のＣｒ−Ｙ合金を配置し、
（ｂ）まず、装置内を排気して０．１Ｐａ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、前記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、かつカソード電極の前記Ｔｉ−Ａｌ−Ｍ合金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前記Ｔｉ−Ａｌ−Ｍ合金によってボンバード洗浄し、
（ｃ）次に、装置内に反応ガスとして窒素ガスを導入して４Ｐａの反応雰囲気とすると共に、前記回転テーブル上で自転しながら回転する工具基体に−１００Ｖの直流バイアス電圧を印加し、かつカソード電極の前記Ｔｉ−Ａｌ−Ｍ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、前記工具基体の表面に、表３、表４に示される目標組成、一層目標層厚の（Ｔｉ，Ａｌ，Ｍ）Ｎ薄層を蒸着形成した後、前記Ｔｉ−Ａｌ−Ｍ合金のカソード電極（蒸発源）とアノード電極との間のアーク放電を停止し、
（ｄ）引き続いて装置内雰囲気を２Ｐａの窒素雰囲気に保持したままで、カソード電極（蒸発源）であるＣｒ−Ｙ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、表４に示される目標組成、一層目標層厚の（Ｃｒ，Ｙ）Ｎ薄層を蒸着形成し、
上記（ｃ）、（ｄ）の操作を、所定の合計平均層厚になるまで繰り返し行って硬質被覆層を蒸着形成し、本発明被覆工具としての本発明表面被覆スローアウエイチップ（以下、本発明被覆チップと云う）１〜３９をそれぞれ製造した。
(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 shown in FIG. Attached along the outer periphery at a predetermined distance in the radial direction from the central axis on the rotary table in the apparatus, cathode electrodes (evaporation sources) are arranged on opposite sides across the rotary table, one of which Is arranged with a Ti-Al-M alloy having a predetermined composition as a cathode electrode (evaporation source), and a Cr-Y alloy with a predetermined composition is arranged as a cathode electrode (evaporation source) on the other side.
(B) First, the inside of the apparatus is heated to 500 ° C. with a heater while the inside of the apparatus is evacuated and kept at a vacuum of 0.1 Pa or less, and then the tool base that rotates while rotating on the rotary table is −1000 V. A DC bias voltage is applied and a current of 100 A is passed between the Ti-Al-M alloy of the cathode electrode and the anode electrode to generate an arc discharge, whereby the surface of the tool base is made of the Ti-Al-M alloy. Bombard washed,
(C) Next, nitrogen gas is introduced as a reaction gas into the apparatus to form a reaction atmosphere of 4 Pa, a DC bias voltage of −100 V is applied to the tool base that rotates while rotating on the rotary table, and A current of 120 A is passed between the Ti-Al-M alloy of the cathode electrode and the anode electrode to generate an arc discharge, and the target composition shown in Tables 3 and 4 is formed on the surface of the tool base. After vapor-depositing a thick (Ti, Al, M) N thin layer, the arc discharge between the cathode electrode (evaporation source) and the anode electrode of the Ti-Al-M alloy is stopped,
(D) Subsequently, an arc discharge is generated by flowing a current of 120 A between the cathode electrode (evaporation source) Cr—Y alloy electrode and the anode electrode while maintaining the atmosphere in the apparatus in a nitrogen atmosphere of 2 Pa. Then, a target composition shown in Tables 3 and 4 and a (Cr, Y) N thin layer having a target layer thickness are formed by vapor deposition.
The above operations (c) and (d) are repeated until a predetermined total average layer thickness is obtained, and a hard coating layer is formed by vapor deposition, and the present surface-coated throwaway tip (hereinafter referred to as the present invention) as the coated tool of the present invention. 1 to 39 were manufactured.
また、比較の目的で、これら工具基体Ａ−１〜Ａ−１０およびＢ−１〜Ｂ−６を、アセトン中で超音波洗浄し、乾燥した状態で、それぞれ図２に示されるアークイオンプレーティング装置に装入し、カソード電極（蒸発源）として所定組成のＴｉ−Ａｌ−Ｍ合金を装着し、まず、装置内を排気して０．１Ｐａ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、前記工具基体に−１０００Ｖの直流バイアス電圧を印加し、かつカソード電極のＴｉ−Ａｌ−Ｍ合金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前記Ｔｉ−Ａｌ−Ｍ合金でボンバード洗浄し、ついで装置内に反応ガスとして窒素ガスを導入して３Ｐａの反応雰囲気とすると共に、前記工具基体に印加するバイアス電圧を−１００Ｖに下げて、前記所定組成の各カソード電極とアノード電極との間にアーク放電を発生させ、前記工具基体Ａ−１〜Ａ−１０およびＢ−１〜Ｂ−６のそれぞれの表面に、表５、表６に示される目標組成および目標層厚の（Ｔｉ，Ａｌ，Ｍ）Ｎ層で構成された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スローアウエイチップ（以下、比較被覆チップと云う）１〜１６をそれぞれ製造した。 For comparison purposes, these tool bases A-1 to A-10 and B-1 to B-6 were ultrasonically cleaned in acetone and dried, respectively, and the arc ion plating shown in FIG. Insert the Ti-Al-M alloy of a predetermined composition as a cathode electrode (evaporation source), and first evacuate the interior of the apparatus and keep it at a vacuum of 0.1 Pa or less, while heating the interior of the apparatus with a heater. After heating to 500 ° C., a DC bias voltage of −1000 V is applied to the tool base, and an arc discharge is generated by flowing a current of 100 A between the Ti—Al—M alloy of the cathode electrode and the anode electrode, Thus, the surface of the tool base is bombarded with the Ti-Al-M alloy, and then nitrogen gas is introduced into the apparatus as a reaction gas to form a reaction atmosphere of 3 Pa, and a via is applied to the tool base. The voltage is lowered to −100 V to generate an arc discharge between each cathode electrode and anode electrode of the predetermined composition, and the respective surfaces of the tool bases A-1 to A-10 and B-1 to B-6 A surface-coated throwaway tip as a comparative coating tool is formed by vapor-depositing a hard coating layer composed of (Ti, Al, M) N layers having the target compositions and target layer thicknesses shown in Tables 5 and 6 1 to 16 (hereinafter referred to as comparative coated chips) were produced.
つぎに、上記の各種の被覆チップを、いずれも工具鋼製バイトの先端部に固定治具にてネジ止めした状態で、本発明被覆チップ１〜３９および比較被覆チップ１〜１６について、
被削材：ＪＩＳ・ＳＵＳ４２０Ｊ（ＨＲＣ５０）の丸棒、
切削速度： １００ ｍ／ｍｉｎ．、
切り込み： １．５ ｍｍ、
送り： ０．３ ｍｍ／ｒｅｖ．、
切削時間： ５ 分、
の条件（切削条件Ａ）での高硬度ステンレス鋼の乾式連続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、６０ｍ／ｍｉｎ．、０．１ｍｍ／ｒｅｖ．）、
被削材：ＪＩＳ・ＳＣＭ４４０（ＨＢ２２０）の丸棒、
切削速度： ２００ ｍ／ｍｉｎ．、
切り込み： ２ ｍｍ、
送り： ０．５ ｍｍ／ｒｅｖ．、
切削時間： ５ 分、
の条件（切削条件Ｂ）での合金鋼の乾式連続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、１２０ｍ／ｍｉｎ．、０．２ｍｍ／ｒｅｖ．）、
被削材：ＪＩＳ・ＳＫＤ６１（ＨＲＣ６０）の丸棒、
切削速度： ９０ ｍ／ｍｉｎ．、
切り込み： １．０ ｍｍ、
送り： ０．１５ ｍｍ／ｒｅｖ．、
切削時間： ５ 分、
の条件（切削条件Ｃ）での合金工具鋼（焼入れ材）の乾式連続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、５０ｍ／ｍｉｎ．、０．１ｍｍ／ｒｅｖ．）、
を行い、いずれの高速高送り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７、表８に示した。
Next, in the state where each of the above various coated chips is screwed to the tip of the tool steel tool with a fixing jig, the present coated chips 1 to 39 and the comparative coated chips 1 to 16 are as follows.
Work material: JIS / SUS420J (HRC50) round bar,
Cutting speed: 100 m / min. ,
Cutting depth: 1.5 mm,
Feed: 0.3 mm / rev. ,
Cutting time: 5 minutes,
(Continuous cutting speed and feed are 60 m / min. And 0.1 mm / rev., Respectively)
Work material: JIS SCM440 (HB220) round bar,
Cutting speed: 200 m / min. ,
Incision: 2 mm,
Feed: 0.5 mm / rev. ,
Cutting time: 5 minutes,
(Continuous cutting speed and feed are 120 m / min. And 0.2 mm / rev., Respectively)
Work material: JIS · SKD61 (HRC60) round bar,
Cutting speed: 90 m / min. ,
Cutting depth: 1.0 mm,
Feed: 0.15 mm / rev. ,
Cutting time: 5 minutes,
Dry continuous high-speed high-feed cutting test of alloy tool steel (quenched material) under the following conditions (cutting condition C) (normal cutting speed and feed are 50 m / min. And 0.1 mm / rev., Respectively),
The flank wear width of the cutting edge was measured in any high-speed, high-feed cutting test. The measurement results are shown in Tables 7 and 8.
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 is 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. , 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、上記実施例１と同一の条件で、表１０に示される目標組成および一層目標層厚の（Ｔｉ，Ａｌ，Ｍ）Ｎ薄層、および、同じく表９に示される目標組成および一層目標層厚の（Ｃｒ，Ｙ）Ｎ薄層の交互積層構造からなる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）１〜２７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 inserted into the arc ion plating apparatus shown in FIG. Under the same conditions as in Example 1, the target composition and the target layer thickness (Ti, Al, M) N thin layer shown in Table 10 and the target composition and target layer thickness (Cr , Y) By forming a hard coating layer having an alternating laminated structure of N thin layers by vapor deposition, the surface coated carbide end mill (hereinafter referred to as the present coated end mill) 1 to 27 as the coated tool of the present invention is formed. Each was manufactured.
また、比較の目的で、上記の工具基体（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２に示されるアークイオンプレーティング装置に装入し、上記実施例１と同一の条件で、表１０に示される目標組成および目標層厚の（Ｔｉ，Ａｌ，Ｍ）Ｎ層からなる硬質被覆層を蒸着することにより、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）１〜１０をそれぞれ製造した。 For the purpose of comparison, the surfaces of the tool bases (end mills) A-1 to A-10 are ultrasonically cleaned in acetone and dried, and then mounted on the arc ion plating apparatus shown in FIG. Then, under the same conditions as in Example 1, the hard coating layer composed of the (Ti, Al, M) N layer having the target composition and the target layer thickness shown in Table 10 is vapor-deposited. Surface-coated carbide end mills (hereinafter referred to as comparative coated end mills) 1 to 10 were produced.
つぎに、上記本発明被覆エンドミル１〜２７および比較被覆エンドミル１〜１０について、
被削材−平面寸法：１００ｍｍ×２５０ｍｍ、厚さ：５０ｍｍのＪＩＳ・ＳＵＳ４２０Ｊ２（ＨＲＣ５０）の板材、
切削速度： ６０ ｍ／ｍｉｎ．、
溝深さ（切り込み）： ０．５ ｍｍ、
テーブル送り： ４２０ ｍｍ／分、
の条件（切削条件Ｄ）での高硬度ステンレス鋼の乾式高速高送り溝切削加工試験（通常の切削速度およびテーブル送りは、それぞれ、３０ｍ／ｍｉｎ．、２５０ｍｍ／分）、
被削材−平面寸法：１００ｍｍ×２５０ｍｍ、厚さ：５０ｍｍのＪＩＳ・ＳＣＭ４４０（ＨＢ２２０）の板材、
切削速度： ９０ ｍ／ｍｉｎ．、
溝深さ（切り込み）： ０．５ ｍｍ、
テーブル送り： ５５０ ｍｍ／分、
の条件（切削条件Ｅ）での合金鋼の乾式高速高送り溝切削加工試験（通常の切削速度およびテーブル送りは、それぞれ、４０ｍ／ｍｉｎ．、３００ｍｍ／分）、
被削材−平面寸法：１００ｍｍ×２５０ｍｍ、厚さ：５０ｍｍのＪＩＳ・ＳＫＤ６１（ＨＲＣ６０）の板材、
切削速度： ９０ ｍ／ｍｉｎ．、
溝深さ（切り込み）： ０．５ ｍｍ、
テーブル送り： ４３０ ｍｍ／分、
の条件（切削条件Ｆ）での合金工具鋼（焼入れ材）の乾式高速高送り溝切削加工試験（通常の切削速度およびテーブル送りは、それぞれ、５０ｍ／ｍｉｎ．、２５０ｍｍ／分）、
をそれぞれ行い、いずれの高速高送り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。この測定結果を表９、表１０にそれぞれ示した。
Next, with respect to the present invention coated end mills 1 to 27 and comparative coated end mills 1 to 10,
Work material-planar dimensions: 100 mm x 250 mm, thickness: 50 mm JIS / SUS420J2 (HRC50) plate material,
Cutting speed: 60 m / min. ,
Groove depth (cut): 0.5 mm,
Table feed: 420 mm / min,
High-hardness stainless steel dry high-speed high-feed groove cutting test under normal conditions (cutting condition D) (normal cutting speed and table feed are 30 m / min. And 250 mm / min, respectively),
Work material-Plane dimensions: 100 mm x 250 mm, thickness: 50 mm JIS / SCM440 (HB220) plate material,
Cutting speed: 90 m / min. ,
Groove depth (cut): 0.5 mm,
Table feed: 550 mm / min,
(High cutting speed and table feed are 40 m / min. And 300 mm / min, respectively)
Work material-Plane dimensions: 100 mm x 250 mm, thickness: 50 mm JIS SKD61 (HRC60) plate material,
Cutting speed: 90 m / min. ,
Groove depth (cut): 0.5 mm,
Table feed: 430 mm / min,
Dry high-speed high-feed groove cutting test of alloy tool steel (quenched material) under the following conditions (cutting condition F) (normal cutting speed and table feed are 50 m / min. And 250 mm / min, respectively),
The cutting groove length was measured until the flank wear width of the outer peripheral edge of the cutting edge reaches 0.1 mm, which is a guide for the service life, in any high-speed, high-feed groove cutting test. The measurement results are shown in Table 9 and Table 10, respectively.
上記の実施例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。 Using the round bar sintered body with a diameter of 13 mm manufactured in Example 2 above, from this round bar sintered body, the diameter x length of the groove forming portion is 8 mm x 22 mm, respectively, by grinding, and WC-base cemented carbide tool bases (drills) A-1 to A-10 having a two-blade shape with a twist angle of 30 degrees were manufactured.
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、上記実施例１と同一の条件で、表１１に示される目標組成および一層目標層厚の（Ｔｉ，Ａｌ，Ｍ）Ｎ薄層、および、同じく表１１に示される目標組成および一層目標層厚の（Ｃｒ，Ｙ）Ｎ薄層の交互積層構造からなる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）１〜２７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 above, the target composition shown in Table 11 and the (Ti, Al, M) N thin layer of the target layer thickness, and the target composition and layer shown in Table 11 are also shown. By subjecting the hard coating layer composed of the alternately laminated structure of the (Cr, Y) N thin layers of the target layer thickness to vapor deposition, the surface coated carbide drill of the present invention (hereinafter referred to as the present invention coated drill) 1) to 27 were produced.
また、比較の目的で、上記の工具基体（ドリル）Ａ−１〜Ａ−１０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２に示されるアークイオンプレーティング装置に装入し、上記実施例１と同一の条件で、表１２に示される目標組成および目標層厚を有する（Ｔｉ，Ａｌ，Ｍ）Ｎ層からなる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）１〜１０をそれぞれ製造した。 For the purpose of comparison, the surfaces of the above-mentioned tool bases (drills) A-1 to A-10 are subjected to honing, ultrasonically cleaned in acetone and dried, and the arc ions shown in FIG. A hard coating layer composed of a (Ti, Al, M) N layer having the target composition and target layer thickness shown in Table 12 is formed by vapor deposition under the same conditions as in Example 1 above. Thus, surface coated carbide drills (hereinafter referred to as comparative coated drills) 1 to 10 as comparative coated tools were manufactured, respectively.
つぎに、上記本発明被覆ドリル１〜２７および比較被覆ドリル１〜１０について、
被削材−平面寸法：１００ｍｍ×２５０ｍｍ、厚さ：５０ｍｍのＪＩＳ・ＳＵＳ４２０Ｊ２（ＨＲＣ５０）の板材、
切削速度： ９０ ｍ／ｍｉｎ．、
送り： ０．５ ｍｍ／ｒｅｖ、
穴深さ： ６ ｍｍ、
の条件（切削条件Ｇ）での高硬度ステンレス鋼の湿式高速高送り穴あけ切削加工試験（通常の切削速度および送りは、それぞれ、４０ｍ／ｍｉｎ．、０．２ｍｍ／ｒｅｖ．）、
被削材−平面寸法：１００ｍｍ×２５０ｍｍ、厚さ：５０ｍｍのＪＩＳ・ＳＣＭ４４０（ＨＢ２２０）の板材、
切削速度： １１０ ｍ／ｍｉｎ．、
送り： ０．６ ｍｍ／ｒｅｖ、
穴深さ： ５ ｍｍ、
の条件（切削条件Ｈ）での合金鋼の湿式高速高送り穴あけ切削加工試験（通常の切削速度および送りは、それぞれ、５０ｍ／ｍｉｎ．、０．３ｍｍ／ｒｅｖ．）、
被削材−平面寸法：１００ｍｍ×２５０ｍｍ、厚さ：５０ｍｍのＪＩＳ・ＳＫＤ６１（ＨＲＣ６０）の板材、
切削速度： ９０ ｍ／ｍｉｎ．、
送り： ０．４ ｍｍ／ｒｅｖ、
穴深さ： ５ ｍｍ、
の条件（切削条件Ｉ）での合金工具鋼（焼入れ材）の湿式高速高送り穴あけ切削加工試験（通常の切削速度および送りは、それぞれ、４０ｍ／ｍｉｎ．、０．２ｍｍ／ｒｅｖ．）、
をそれぞれ行い、いずれの湿式高速穴あけ切削加工試験（水溶性切削油使用）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。この測定結果を表１１、表１２にそれぞれ示した。
Next, about the said invention coated drill 1-27 and the comparative coated drill 1-10,
Work material-planar dimensions: 100 mm x 250 mm, thickness: 50 mm JIS / SUS420J2 (HRC50) plate material,
Cutting speed: 90 m / min. ,
Feed: 0.5 mm / rev,
Hole depth: 6 mm,
Wet high-speed high-feed drilling test of high-hardness stainless steel under the following conditions (cutting condition G) (normal cutting speed and feed are 40 m / min. And 0.2 mm / rev., Respectively),
Work material-Plane dimensions: 100 mm x 250 mm, thickness: 50 mm JIS / SCM440 (HB220) plate material,
Cutting speed: 110 m / min. ,
Feed: 0.6 mm / rev,
Hole depth: 5 mm,
Wet high-speed high-feed drilling test of alloy steel under the following conditions (cutting condition H) (normal cutting speed and feed are 50 m / min. And 0.3 mm / rev., Respectively),
Work material-Plane dimensions: 100 mm x 250 mm, thickness: 50 mm JIS SKD61 (HRC60) plate material,
Cutting speed: 90 m / min. ,
Feed: 0.4 mm / rev,
Hole depth: 5 mm,
Wet high-speed high-feed drilling test of alloy tool steel (quenched material) under the following conditions (cutting condition I) (normal cutting speed and feed are 40 m / min. And 0.2 mm / rev., Respectively),
In each wet high-speed drilling test (using water-soluble cutting oil), 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 shown in Tables 11 and 12, 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チップ１〜３９、本発明被覆エンドミル１〜２７、および本発明被覆ドリル１〜２７の硬質被覆層を構成する（Ｔｉ，Ａｌ，Ｍ）Ｎ薄層および（Ｃｒ，Ｙ）Ｎ薄層の組成、並びに、比較被覆工具としての比較被覆チップ１〜１６、比較被覆エンドミル１〜１０、および比較被覆ドリル１〜１０の（Ｔｉ，Ａｌ，Ｍ）Ｎ層からなる硬質被覆層の組成を、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。 (Ti, Al, M) N constituting the hard coating layers of the present coated chips 1 to 39, the present coated end mills 1 to 27, and the present coated drills 1 to 27 as the present coated tools obtained as a result. Composition of thin layer and (Cr, Y) N thin layer, and (Ti, Al, M) of comparative coated tip 1-16 as comparative coated tool, comparative coated end mill 1-10, and comparative coated drill 1-10 When the composition of the hard coating layer composed of the N layer was measured by an energy dispersive X-ray analysis method using a transmission electron microscope, the composition was substantially the same as the target composition.
また、上記の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同じ平均値（５ヶ所の平均値）を示した。 Moreover, when the average layer thickness of each layer which comprises said hard coating layer was cross-sectional measured using the scanning electron microscope, all showed the substantially same average value (average value of five places) as target layer thickness. .
表７〜１２に示される結果から、本発明被覆工具は、いずれも特に合金工具鋼の焼入れ材、高硬度ステンレス鋼などの高硬度被削材の高速高送り切削加工でも、硬質被覆層の交互積層構造を構成する（Ｔｉ，Ａｌ，Ｍ）Ｎ薄層が、すぐれた高温硬さ、高温強度、あるいは、これに加えてさらにすぐれた耐摩耗性、高温耐酸化性を有し、同じく交互積層構造を構成する（Ｃｒ，Ｙ）Ｎ薄層が耐熱性にすぐれ、高温条件下でも前記被削材および切粉との間のすぐれた潤滑性を保持し、その結果、（Ｔｉ，Ａｌ，Ｍ）Ｎ薄層に不足する潤滑性が、これに交互に積層される（Ｃｒ，Ｙ）Ｎ薄層により補完されることによって、硬質被覆層全体として、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のに対して、硬質被覆層が（Ｔｉ，Ａｌ，Ｍ）Ｎ層で構成され、（Ｃｒ，Ｙ）Ｎ層を備えない比較被覆工具においては、いずれも前記被削材の高速高送り切削加工では被削材（難削材）および切粉と前記硬質被覆層との粘着性および反応性が一段と高くなるために、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 7 to 12, all of the coated tools of the present invention have alternating hard coating layers even in high-speed and high-feed cutting of high-hardness work materials such as hardened materials of alloy tool steel and high-hardness stainless steel. The (Ti, Al, M) N thin layers that make up the laminated structure have excellent high-temperature hardness, high-temperature strength, or in addition to this, excellent wear resistance and high-temperature oxidation resistance. The (Cr, Y) N thin layer constituting the structure is excellent in heat resistance and maintains excellent lubricity between the work material and the chips even under high temperature conditions. As a result, (Ti, Al, M ) The lack of lubricity of the N thin layer is complemented by the (Cr, Y) N thin layers alternately stacked on the N thin layer, so that the entire hard coating layer is excellent over a long period of time without occurrence of chipping. The hard coating layer is (Ti In the comparative coated tool which is composed of an Al, M) N layer and does not have a (Cr, Y) N layer, all of the work material (hard-to-cut material) and chips in the high-speed high-feed cutting of the work material It is clear that the adhesiveness and reactivity between the hard coating layer and the hard coating layer are further increased, so that chipping occurs in the cutting edge portion and the service life is reached in a relatively short time.
上述のように、この発明の被覆工具は、一般的な被削材の切削加工は勿論のこと、特に合金工具鋼の焼入れ材、高硬度ステンレス鋼などの高硬度被削材の高速高送り切削加工でもすぐれた耐チッピング性と耐摩耗性を発揮し、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ＦＡ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 capable of cutting not only general work materials but also high-speed high-feed cutting of hard work materials such as hardened materials of alloy tool steel and high-hardness stainless steel. Excellent chipping resistance and wear resistance even during machining, and excellent cutting performance over a long period of time. Therefore, FA for cutting equipment, labor saving and energy saving of cutting, and lower cost It is possible to cope with the conversion sufficiently satisfactorily.
Claims (2)
（ａ）０．０１〜０．１μｍの一層平均層厚を有し、かつ、
組成式：（Ｔｉ１−αＡｌα）Ｎ（但し、αはＡｌの含有割合を示し、原子比で、０．４５≦α≦０．７５である）を満足するＴｉとＡｌの複合窒化物層からなる（Ｔｉ，Ａｌ）Ｎ薄層、
（ｂ）０．０１〜０．１μｍの一層平均層厚を有し、かつ、
組成式：（Ｃｒ１−γＹγ）Ｎ（但し、γはＹの含有割合を示し、原子比で、０．０１≦γ≦０．１である）を満足するＣｒとＹの複合窒化物層からなる（Ｃｒ，Ｙ）Ｎ薄層、
上記（ａ）、（ｂ）の交互積層からなり、１〜５μｍの合計平均層厚を有する硬質被覆層を形成してなる、高速高送り切削加工で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切削工具。 On the surface of the tool base composed of tungsten carbide based cemented carbide or titanium carbonitride based cermet,
(A) having an average layer thickness of 0.01 to 0.1 μm, and
Ti and Al composite nitride satisfying the composition formula: (Ti 1-α Al α ) N (where α is the Al content ratio and the atomic ratio is 0.45 ≦ α ≦ 0.75) (Ti, Al) N thin layer consisting of layers,
(B) having an average layer thickness of 0.01 to 0.1 μm, and
Cr and Y composite nitride satisfying the composition formula: (Cr 1-γ Y γ ) N (where γ represents the Y content and the atomic ratio is 0.01 ≦ γ ≦ 0.1) (Cr, Y) N thin layer consisting of layers,
Demonstrating excellent chipping resistance in high-speed, high-feed cutting, consisting of alternating layers (a) and (b) above, and forming a hard coating layer with a total average layer thickness of 1 to 5 μm A surface-coated cutting tool.
（ａ）０．０１〜０．１μｍの一層平均層厚を有し、かつ、
組成式：（Ｔｉ１−α−βＡｌαＭβ）Ｎ（ここで、Ｍは、Ｔｉを除く周期律表４ａ，５ａ，６ａ族の元素、Ｓｉ、Ｂ、Ｙのうちから選ばれた１種又は２種以上の添加成分を示し、また、αはＡｌの含有割合、βはＭの含有割合をそれぞれ示し、原子比で、０．４５≦α≦０．７５、０．０１≦β≦０．２５、α+β＜１．００である）を満足するＴｉとＡｌとＭの複合窒化物層からなる（Ｔｉ，Ａｌ，Ｍ）Ｎ薄層、
（ｂ）０．０１〜０．１μｍの一層平均層厚を有し、かつ、
組成式：（Ｃｒ１−γＹγ）Ｎ（但し、γはＹの含有割合を示し、原子比で、０．０１≦γ≦０．１である）を満足するＣｒとＹの複合窒化物層からなる（Ｃｒ，Ｙ）Ｎ薄層、
上記（ａ）、（ｂ）の交互積層からなり、１〜５μｍの合計平均層厚を有する硬質被覆層を形成してなる、高速高送り切削加工で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切削工具。
On the surface of the tool base composed of tungsten carbide based cemented carbide or titanium carbonitride based cermet,
(A) having an average layer thickness of 0.01 to 0.1 μm, and
Composition formula: (Ti 1-α-β Al α M β ) N (where M is a member selected from the group 4a, 5a, 6a elements except Si, Si, B, Y) Seeds or two or more kinds of additive components, α is a content ratio of Al, β is a content ratio of M, and atomic ratio is 0.45 ≦ α ≦ 0.75, 0.01 ≦ β ≦ (Ti, Al, M) N thin layer composed of a composite nitride layer of Ti, Al, and M satisfying 0.25 , α + β <1.00 )
(B) having an average layer thickness of 0.01 to 0.1 μm, and
Cr and Y composite nitride satisfying the composition formula: (Cr 1-γ Y γ ) N (where γ represents the Y content and the atomic ratio is 0.01 ≦ γ ≦ 0.1) (Cr, Y) N thin layer consisting of layers,
Demonstrating excellent chipping resistance in high-speed, high-feed cutting, consisting of alternating layers (a) and (b) above, and forming a hard coating layer with a total average layer thickness of 1 to 5 μm A surface-coated cutting tool.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2008139300A JP5234332B2 (en) | 2008-05-28 | 2008-05-28 | A surface-coated cutting tool that exhibits excellent chipping resistance with a hard coating layer in high-speed, high-feed cutting. |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2008139300A JP5234332B2 (en) | 2008-05-28 | 2008-05-28 | A surface-coated cutting tool that exhibits excellent chipping resistance with a hard coating layer in high-speed, high-feed cutting. |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JP2009285759A JP2009285759A (en) | 2009-12-10 |
| JP5234332B2 true JP5234332B2 (en) | 2013-07-10 |
Family
ID=41455493
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2008139300A Expired - Fee Related JP5234332B2 (en) | 2008-05-28 | 2008-05-28 | A surface-coated cutting tool that exhibits excellent chipping resistance with a hard coating layer in high-speed, high-feed cutting. |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP5234332B2 (en) |
Families Citing this family (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP5287383B2 (en) * | 2009-03-13 | 2013-09-11 | 三菱マテリアル株式会社 | Surface-coated cutting tool that exhibits excellent chipping resistance and wear resistance with a hard coating layer in high-speed cutting |
| CN110860673B (en) * | 2019-12-30 | 2021-04-23 | 岭南师范学院 | CrYBN composite coating attached to surface of die-casting die, die-casting die and preparation method |
Family Cites Families (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2006070730A1 (en) * | 2004-12-28 | 2006-07-06 | Sumitomo Electric Hardmetal Corp. | Surface-coated cutting tool and process for producing the same |
| JP4645821B2 (en) * | 2005-04-08 | 2011-03-09 | 三菱マテリアル株式会社 | Cutting tool made of surface-coated cemented carbide with excellent wear resistance due to high-speed cutting of heat-resistant alloys |
| AT8346U1 (en) * | 2005-04-29 | 2006-06-15 | Ceratitzit Austria Ges M B H | COATED TOOL |
| JP4697661B2 (en) * | 2005-06-30 | 2011-06-08 | 三菱マテリアル株式会社 | Surface coated cutting tool with excellent wear resistance with hard coating layer in high speed cutting of heat resistant alloy |
| JP4706915B2 (en) * | 2005-09-02 | 2011-06-22 | 三菱マテリアル株式会社 | Surface-coated cutting tool with excellent wear resistance with hard coating layer in high-speed cutting of heat-resistant alloys |
| JP2009285764A (en) * | 2008-05-28 | 2009-12-10 | Mitsubishi Materials Corp | Surface-coated cutting tool with hard coating layer exhibiting superior chipping resistance in high-speed high-feed cutting work |
-
2008
- 2008-05-28 JP JP2008139300A patent/JP5234332B2/en not_active Expired - Fee Related
Also Published As
| Publication number | Publication date |
|---|---|
| JP2009285759A (en) | 2009-12-10 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| JP2009101491A (en) | Surface-coated cutting tool having hard coating layer exerting excellent lubricity and wear resistance in high-speed cutting | |
| WO2014061292A1 (en) | Surface-coated cutting tool | |
| JP2009119551A (en) | Surface-coated cutting tool with hard coating layer exhibiting superior chipping resistance in high-speed feed cutting work | |
| JP5440346B2 (en) | Surface coated cutting tool | |
| JP5196122B2 (en) | Surface coated cutting tool | |
| JP5234499B2 (en) | A surface-coated cutting tool that exhibits excellent chipping resistance with a hard coating layer in high-speed, high-feed cutting. | |
| JP5783462B2 (en) | Surface coated cutting tool | |
| JP5234332B2 (en) | A surface-coated cutting tool that exhibits excellent chipping resistance with a hard coating layer in high-speed, high-feed cutting. | |
| JP4697662B2 (en) | Surface coated cutting tool with excellent wear resistance due to high hard coating layer in high speed cutting of high hardness steel | |
| JP4645820B2 (en) | Cutting tool made of surface-coated cemented carbide that provides excellent wear resistance with a hard coating layer in high-speed cutting of hardened steel | |
| JP2011240438A (en) | Surface coated cutting tool excellent in heat resistance and fusion resistance | |
| JP5975214B2 (en) | Surface coated cutting tool | |
| JP2009285764A (en) | Surface-coated cutting tool with hard coating layer exhibiting superior chipping resistance in high-speed high-feed cutting work | |
| JP6102653B2 (en) | Surface coated cutting tool | |
| JP5975339B2 (en) | Surface coated cutting tool | |
| JP5499861B2 (en) | Surface coated cutting tool with excellent chipping resistance due to hard coating layer | |
| JP2011240436A (en) | Surface coated cutting tool excellent in heat resistance and fusion resistance | |
| JP5077743B2 (en) | Surface coated cutting tool with excellent chipping resistance and wear resistance due to hard coating layer | |
| JP5287383B2 (en) | Surface-coated cutting tool that exhibits excellent chipping resistance and wear resistance with a hard coating layer in high-speed cutting | |
| JP2011173176A (en) | Surface coated cutting tool superior in heat resistance and deposition resistance | |
| JP2011240437A (en) | Surface coated cutting tool excellent in heat resistance and fusion resistance | |
| JP2012143851A (en) | Surface-coated cutting tool | |
| JP2011177800A (en) | Surface coated cutting tool having excellent heat resistance and welding resistance | |
| JP5499862B2 (en) | Surface coated cutting tool with excellent chipping resistance and wear resistance due to hard coating layer | |
| JP5796354B2 (en) | Surface coated cutting tool with excellent heat resistance and welding resistance |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| A621 | Written request for application examination |
Free format text: JAPANESE INTERMEDIATE CODE: A621 Effective date: 20110331 |
|
| A131 | Notification of reasons for refusal |
Free format text: JAPANESE INTERMEDIATE CODE: A131 Effective date: 20121219 |
|
| A977 | Report on retrieval |
Free format text: JAPANESE INTERMEDIATE CODE: A971007 Effective date: 20121219 |
|
| A521 | Request for written amendment filed |
Free format text: JAPANESE INTERMEDIATE CODE: A523 Effective date: 20130205 |
|
| TRDD | Decision of grant or rejection written | ||
| A01 | Written decision to grant a patent or to grant a registration (utility model) |
Free format text: JAPANESE INTERMEDIATE CODE: A01 Effective date: 20130228 |
|
| A61 | First payment of annual fees (during grant procedure) |
Free format text: JAPANESE INTERMEDIATE CODE: A61 Effective date: 20130313 |
|
| R150 | Certificate of patent or registration of utility model |
Free format text: JAPANESE INTERMEDIATE CODE: R150 Ref document number: 5234332 Country of ref document: JP Free format text: JAPANESE INTERMEDIATE CODE: R150 |
|
| FPAY | Renewal fee payment (event date is renewal date of database) |
Free format text: PAYMENT UNTIL: 20160405 Year of fee payment: 3 |
|
| LAPS | Cancellation because of no payment of annual fees |