JP2015182153A - surface-coated cutting tool - Google Patents
surface-coated cutting tool Download PDFInfo
- Publication number
- JP2015182153A JP2015182153A JP2014059035A JP2014059035A JP2015182153A JP 2015182153 A JP2015182153 A JP 2015182153A JP 2014059035 A JP2014059035 A JP 2014059035A JP 2014059035 A JP2014059035 A JP 2014059035A JP 2015182153 A JP2015182153 A JP 2015182153A
- Authority
- JP
- Japan
- Prior art keywords
- layer
- hard coating
- coating layer
- plane
- tool
- 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.)
- Granted
Links
- 238000005520 cutting process Methods 0.000 title claims abstract description 35
- 239000010410 layer Substances 0.000 claims abstract description 44
- 239000011247 coating layer Substances 0.000 claims abstract description 40
- 238000002441 X-ray diffraction Methods 0.000 claims abstract description 13
- 239000002131 composite material Substances 0.000 claims abstract description 10
- 150000004767 nitrides Chemical class 0.000 claims abstract description 10
- UONOETXJSWQNOL-UHFFFAOYSA-N tungsten carbide Chemical compound [W+]#[C-] UONOETXJSWQNOL-UHFFFAOYSA-N 0.000 claims abstract description 5
- 238000007740 vapor deposition Methods 0.000 abstract description 4
- 229910045601 alloy Inorganic materials 0.000 description 18
- 239000000956 alloy Substances 0.000 description 18
- 229910018575 Al—Ti Inorganic materials 0.000 description 11
- 239000000843 powder Substances 0.000 description 11
- 239000000203 mixture Substances 0.000 description 9
- 229910001220 stainless steel Inorganic materials 0.000 description 8
- 239000000758 substrate Substances 0.000 description 8
- 230000004907 flux Effects 0.000 description 7
- 239000010935 stainless steel Substances 0.000 description 7
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 6
- 229910001315 Tool steel Inorganic materials 0.000 description 6
- 239000011248 coating agent Substances 0.000 description 6
- 238000000576 coating method Methods 0.000 description 6
- 230000000052 comparative effect Effects 0.000 description 6
- 238000005259 measurement Methods 0.000 description 6
- 239000013078 crystal Substances 0.000 description 5
- 239000000463 material Substances 0.000 description 5
- 238000003801 milling Methods 0.000 description 5
- CSCPPACGZOOCGX-UHFFFAOYSA-N Acetone Chemical compound CC(C)=O CSCPPACGZOOCGX-UHFFFAOYSA-N 0.000 description 4
- 230000003247 decreasing effect Effects 0.000 description 4
- 238000010891 electric arc Methods 0.000 description 4
- 239000007789 gas Substances 0.000 description 4
- 238000012545 processing Methods 0.000 description 4
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 3
- 238000004140 cleaning Methods 0.000 description 3
- 238000012360 testing method Methods 0.000 description 3
- 230000015572 biosynthetic process Effects 0.000 description 2
- 230000007423 decrease Effects 0.000 description 2
- 229910001873 dinitrogen Inorganic materials 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 238000007733 ion plating Methods 0.000 description 2
- 238000000034 method Methods 0.000 description 2
- 229910052757 nitrogen Inorganic materials 0.000 description 2
- 239000002994 raw material Substances 0.000 description 2
- 239000006104 solid solution Substances 0.000 description 2
- 229910000975 Carbon steel Inorganic materials 0.000 description 1
- 229910000831 Steel Inorganic materials 0.000 description 1
- 238000005299 abrasion Methods 0.000 description 1
- 230000001154 acute effect Effects 0.000 description 1
- 239000010962 carbon steel Substances 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000000151 deposition Methods 0.000 description 1
- 238000005553 drilling Methods 0.000 description 1
- 238000002149 energy-dispersive X-ray emission spectroscopy Methods 0.000 description 1
- 230000008020 evaporation Effects 0.000 description 1
- 238000001704 evaporation Methods 0.000 description 1
- 238000000227 grinding Methods 0.000 description 1
- 238000002156 mixing Methods 0.000 description 1
- 230000003647 oxidation Effects 0.000 description 1
- 238000007254 oxidation reaction Methods 0.000 description 1
- 239000002245 particle Substances 0.000 description 1
- 238000005240 physical vapour deposition Methods 0.000 description 1
- 239000012495 reaction gas Substances 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 238000010008 shearing Methods 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 239000010959 steel Substances 0.000 description 1
- 238000001308 synthesis method Methods 0.000 description 1
- 229920001169 thermoplastic Polymers 0.000 description 1
- 239000004416 thermosoftening plastic Substances 0.000 description 1
- 229910052721 tungsten Inorganic materials 0.000 description 1
Landscapes
- Drilling Tools (AREA)
- Cutting Tools, Boring Holders, And Turrets (AREA)
- Physical Vapour Deposition (AREA)
Abstract
Description
この発明は、炭素鋼、ステンレス鋼などの切削加工において、硬質被覆層がすぐれた耐摩耗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 relates to a surface-coated cutting tool (hereinafter referred to as a coated tool) that exhibits excellent wear resistance in a hard coating layer in cutting of carbon steel, stainless steel, and the like.
一般に、被覆工具には、各種のステンレス鋼や合金工具鋼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、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, a throw-away tip that is used by attaching to the tip of a cutting tool for turning or planing of a work material such as various stainless steels and alloy tool steels, and drilling of the work material. There are drills used for cutting, etc., and solid type end mills used for chamfering, grooving, shoulder processing, etc. of the work material. A slow-away end mill tool that performs cutting work in the same manner as an end mill is known.
そして、従来から、被覆工具の被膜特性を改善すべく、種々の提案がなされている。
例えば、特許文献１は、被覆工具基体の表面に、０．９９７（０．４１２ｘ＋０．４２４１７３（１−ｘ））〜１．００５（０．４１２ｘ＋０．４２４１７３（１−ｘ））ｎｍの格子定数を有し、膜厚が０．０１〜５０μｍである（Ａｌ，Ｔｉ）Ｎ膜をアークイオンプレーティング等の気相合成法で形成することによって、高硬度で耐摩耗性にすぐれた耐久性の硬質被膜を提供することが提案されている。
Conventionally, various proposals have been made to improve the coating characteristics of the coated tool.
For example, Patent Document 1 discloses a lattice constant of 0.997 (0.412x + 0.424173 (1-x)) to 1.005 (0.412x + 0.424173 (1-x)) nm on the surface of a coated tool base. It has a high hardness and excellent wear resistance by forming a (Al, Ti) N film having a thickness of 0.01 to 50 μm by a gas phase synthesis method such as arc ion plating. It has been proposed to provide a coating.
また、例えば、特許文献２には、基体の表面に物理蒸着法で被覆形成した（Ａｌ，Ｔｉ）Ｎ層について、ＡｌＴｉＮの結晶構造が面心立方晶構造であり、Ｘ線回折による（Ａｌ，Ｔｉ）Ｎ（２００）面のピーク強度を（Ａｌ，Ｔｉ）Ｎ（１１１）面のピーク強度より大きくすることによって、耐酸化性、耐摩耗性、耐食性にすぐれた（Ａｌ，Ｔｉ）Ｎ被覆層が提案されている。 Further, for example, in Patent Document 2, the (Al, Ti) N layer coated on the surface of the substrate by physical vapor deposition has a face-centered cubic crystal structure of AlTiN, and (Al, Ti) by X-ray diffraction (Al, (Al, Ti) N coating layer having superior oxidation resistance, wear resistance, and corrosion resistance by making the peak intensity of the Ti) N (200) plane greater than the peak intensity of the (Al, Ti) N (111) plane Has been proposed.
さらに、例えば、特許文献３には、切削工具、金型または、機械部品で耐摩耗性が要求される基板の表面に、格子定数または配向性を変化させた２層以上の積層コーティング膜で形成された膜厚が０．１ミクロン以上２０ミクロン以下の被膜を形成し、基板表面に形成されたＴｉＮ膜の配向性が前記基板表面と平行な（２００）面と（１１１）面からのＸ線回折線強度比Ｉ（２００）／Ｉ（１１１）が５以上であって、且つ、前記ＴｉＮ膜の格子定数が０．４２３１ｎｍから０．４２５２ｎｍまでとすることによって、被膜の耐摩耗性、耐久性を改善することが提案されている。 Further, for example, in Patent Document 3, a cutting tool, a die, or a machine part that is required to have wear resistance is formed on the surface of a substrate with a multilayer coating film having two or more layers with different lattice constants or orientations. A film having a thickness of 0.1 to 20 microns is formed, and the orientation of the TiN film formed on the substrate surface is X-rays from the (200) plane and the (111) plane parallel to the substrate surface. When the diffraction line intensity ratio I (200) / I (111) is 5 or more and the lattice constant of the TiN film is from 0.4231 nm to 0.4252 nm, the wear resistance and durability of the coating are achieved. It has been proposed to improve.
近年の切削加工装置の高性能化はめざましく、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、切削加工は一段と厳しい切削条件下で行われるようになってきている。
上記従来の被覆工具においては、ある程度の耐摩耗性の改善は図り得るものの、これをステンレス鋼、合金工具鋼などの高速ミーリング加工に用いた場合には、摩耗損傷が大きくなり、これを原因として、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 performance of cutting devices has been dramatically improved, while on the other hand, there has been a strong demand for labor saving, energy saving, and cost reduction for cutting, and as a result, cutting has been performed under more severe cutting conditions. It is coming.
Although the above-mentioned conventional coated tools can improve wear resistance to some extent, when this is used for high-speed milling processing of stainless steel, alloy tool steel, etc., wear damage increases, and this is the cause. At present, the service life is reached in a relatively short time.
そこで、本発明者等は、ステンレス鋼、合金工具鋼等の高速ミーリング加工に用いた場合であっても、耐摩耗性にすぐれ、長期の使用に亘ってすぐれた切削性能を発揮する被覆工具を提供すべく、鋭意研究を行った結果、以下の知見を得た。 Therefore, the present inventors have provided a coated tool that exhibits excellent wear resistance and excellent cutting performance over a long period of use, even when used for high-speed milling of stainless steel, alloy tool steel, etc. As a result of earnest research to provide, the following knowledge was obtained.
従来の被覆工具では、（Ａｌ，Ｔｉ）Ｎからなる硬質被覆層について、その格子定数（特許文献１参照）、あるいは、（２００）面と（１１１）面のＸ線回折強度比（特許文献２参照）を夫々単独で規定していたが、格子定数と（２００）面と（１１１）面のＸ線回折強度比を、両者関連付けて規定した場合には、従来の（Ａｌ，Ｔｉ）Ｎ硬質被覆層に比して、格段に高硬度となり、その結果として、すぐれた耐摩耗性を長期にわたり発揮することを見出したのである。 In a conventional coated tool, for a hard coating layer made of (Al, Ti) N, the lattice constant (see Patent Document 1) or the X-ray diffraction intensity ratio between the (200) plane and the (111) plane (Patent Document 2). Each) is defined independently, but when the lattice constant and the X-ray diffraction intensity ratio of the (200) plane and the (111) plane are defined in association with each other, the conventional (Al, Ti) N hard It has been found that the hardness is much higher than that of the coating layer, and as a result, excellent wear resistance is exhibited over a long period of time.
この発明は、上記の知見に基づいてなされたものであって、
「 炭化タングステン基超硬合金で構成された工具基体の表面に、平均層厚が２〜１０μｍの硬質被覆層を蒸着形成した表面被覆切削工具において、
（ａ）前記硬質被覆層は、ＡｌとＴｉの複合窒化物層からなり、かつ、該層においてＡｌとＴｉの合量に占めるＡｌの含有割合ｘは、０．４０≦ｘ≦０．７５（但し、原子比）であり、
（ｂ）前記硬質被覆層を構成するＡｌとＴｉの複合窒化物層の格子定数は、−０．０５７ｘ＋４．１８（Å）〜−０．０５７ｘ＋４．２４（Å）の範囲内の値をとり、
（ｃ）Ｘ線回折による前記ＡｌとＴｉの複合窒化物層の（１１１）面の回折ピーク強度Ｉ（１１１）に対する（２００）面の回折ピーク強度Ｉ（２００）の比の値Ｉ（２００）／Ｉ（１１１）が３以上であることを特徴とする表面被覆切削工具。」
に特徴を有するものである。
This invention has been made based on the above findings,
In a surface-coated cutting tool in which a hard coating layer having an average layer thickness of 2 to 10 μm is vapor-deposited on the surface of a tool base composed of a tungsten carbide-based cemented carbide,
(A) The hard coating layer is composed of a composite nitride layer of Al and Ti, and the Al content ratio x in the total amount of Al and Ti in the layer is 0.40 ≦ x ≦ 0.75 ( However, atomic ratio)
(B) The lattice constant of the composite nitride layer of Al and Ti constituting the hard coating layer takes a value in the range of −0.057x + 4.18 (Å) to −0.057x + 4.24 (Å),
(C) A value I (200) of the ratio of the diffraction peak intensity I (200) of the (200) plane to the diffraction peak intensity I (111) of the (111) plane of the composite nitride layer of Al and Ti by X-ray diffraction A surface-coated cutting tool having a / I (111) of 3 or more. "
It has the characteristics.
つぎに、この発明の被覆工具について詳細に説明する。
（ａ）硬質被覆層の種別、平均層厚：
この発明の硬質被覆層は、ＡｌとＴｉの複合窒化物（以下、「（Ａｌ，Ｔｉ）Ｎ」で示す）層からなる。
上記（Ａｌ，Ｔｉ）Ｎ層は、Ａｌ成分が高温硬さと耐熱性を向上させ、Ｔｉ成分が高温靭性、高温強度を向上させる作用があることから、高温硬さ、耐熱性、高温強度にすぐれた硬質被覆層として既によく知られている。
本発明では、Ｔｉとの合量に占めるＡｌの含有割合ｘ（原子比、以下同じ）が０．７５を超えると、六方晶結晶構造の割合が増加するため硬さが低下し、一方、Ｔｉとの合量に占めるＡｌの含有割合（原子比）が０．４０未満となると、相対的にＡｌの含有割合が少なくなり、耐熱性の低下を招き、その結果、偏摩耗の発生、熱塑性変形の発生等により耐摩耗性が劣化するようになることから、Ｔｉとの合量に占めるＡｌの含有割合ｘ（原子比）は、０．４０〜０．７５であることが必要である。
また、（Ａｌ，Ｔｉ）Ｎ層からなる硬質被覆層の平均層厚は、２μｍ未満では、すぐれた耐摩耗性を長期に亘って発揮することができず、工具寿命短命の原因となり、一方、その平均層厚が１０μｍを越えると、硬質被覆層が自己破壊し易くなることから、その平均層厚は２〜１０μｍとすることが必要である。
Next, the coated tool of the present invention will be described in detail.
(A) Type of hard coating layer, average layer thickness:
The hard coating layer according to the present invention is composed of a composite nitride (hereinafter referred to as “(Al, Ti) N”) layer of Al and Ti.
In the (Al, Ti) N layer, the Al component improves high temperature hardness and heat resistance, and the Ti component has the action of improving high temperature toughness and high temperature strength. It is already well known as a hard coating layer.
In the present invention, if the Al content ratio x (atomic ratio, hereinafter the same) in the total amount with Ti exceeds 0.75, the ratio of the hexagonal crystal structure increases, so that the hardness decreases. When the Al content ratio (atomic ratio) in the total amount with respect to is less than 0.40, the Al content ratio is relatively reduced, resulting in a decrease in heat resistance, resulting in the occurrence of uneven wear, thermoplastic deformation. Since the wear resistance is deteriorated due to the occurrence of the above, the Al content ratio x (atomic ratio) in the total amount with Ti needs to be 0.40 to 0.75.
In addition, if the average thickness of the hard coating layer made of the (Al, Ti) N layer is less than 2 μm, excellent wear resistance cannot be exhibited over a long period of time, resulting in a short tool life. If the average layer thickness exceeds 10 μm, the hard coating layer tends to self-destruct, so the average layer thickness needs to be 2 to 10 μm.
（ｂ）（Ａｌ，Ｔｉ）Ｎ層の格子定数：
本発明では、硬質被覆層を構成する（Ａｌ，Ｔｉ）Ｎ層について、その格子定数が、
−０．０５７ｘ＋４．１８（Å）〜−０．０５７ｘ＋４．２４（Å）
の範囲内の値となるように成膜する。
本発明で、硬質被覆層を構成する（Ａｌ，Ｔｉ）Ｎ層の格子定数を上記の如く定めたのは、以下の理由による。
即ち、立方晶ＴｉＮの格子定数理論値は４．２４（Å）であり、また、準安定相である立方晶ＡｌＮの格子定数理論値は４．１２（Å）であるところ、本発明の硬質被覆層を構成する（Ａｌ，Ｔｉ）Ｎ層の格子定数が−０．０５７ｘ＋４．２４（Å）を超えると、固溶体硬化による影響が少なくなり、硬質被覆層の硬さが小さくなり、その結果、すぐれた耐摩耗性を長期にわたって確保することができなくなり、一方、格子定数が−０．０５７ｘ＋４．１８（Å）未満になると、固溶体硬化による影響で硬質被覆層の硬さが大きくなるが、その反面、刃先稜線部の鋭角な領域で切削加工時、硬質被覆層中にクラックが発生し、チッピングが発生し易くなることから、硬質被覆層を構成する（Ａｌ，Ｔｉ）Ｎ層の格子定数は、
−０．０５７ｘ＋４．１８（Å）〜−０．０５７ｘ＋４．２４（Å）
の範囲内の値となるように定めた。
より好ましくは、−０．０５７ｘ＋４．２０（Å）〜−０．０５７ｘ＋４．２３（Å）の範囲内の値である。
なお、上記の格子定数を定める数式における「ｘ」は、Ｔｉとの合量に占めるＡｌの含有割合ｘ（原子比、以下同じ）である。
(B) The lattice constant of the (Al, Ti) N layer:
In the present invention, the lattice constant of the (Al, Ti) N layer constituting the hard coating layer is as follows:
-0.057x + 4.18 (Å) to -0.057x + 4.24 (Å)
The film is formed so as to have a value within the range.
In the present invention, the lattice constant of the (Al, Ti) N layer constituting the hard coating layer is determined as described above for the following reason.
That is, the theoretical value of lattice constant of cubic TiN is 4.24 (Å), and the theoretical value of lattice constant of cubic AlN that is a metastable phase is 4.12 (Å). When the lattice constant of the (Al, Ti) N layer constituting the coating layer exceeds −0.057x + 4.24 (Å), the influence of solid solution curing is reduced, and the hardness of the hard coating layer is reduced. On the other hand, when the lattice constant becomes less than −0.057x + 4.18 (Å), the hardness of the hard coating layer increases due to the effect of solid solution hardening. On the other hand, since the cracks are generated in the hard coating layer and chipping is likely to occur at the time of cutting in an acute area of the edge of the blade edge, the lattice constant of the (Al, Ti) N layer constituting the hard coating layer is ,
-0.057x + 4.18 (Å) to -0.057x + 4.24 (Å)
It was determined to be a value within the range of.
More preferably, it is a value within the range of -0.057x + 4.20 (Å) to -0.057x + 4.23 (Å).
Note that “x” in the mathematical expression that defines the lattice constant is the Al content ratio x (atomic ratio, the same applies hereinafter) in the total amount with Ti.
上記で定めた所定数値範囲内の格子定数の（Ａｌ，Ｔｉ）Ｎ層は、例えば、図１に示すアークイオンプレーティング（以下、「ＡＩＰ」という）装置を用いて成膜するに際し、ＡＩＰ装置におけるターゲットとして、７０原子％Ａｌ−３０原子％Ｔｉ〜５０原子％Ａｌ−５０原子％Ｔｉの成分組成のＡｌ−Ｔｉ合金を用い、成膜時のターゲット表面の最大磁束密度、バイアス電圧を制御することによって、（Ａｌ，Ｔｉ）Ｎ層の格子定数を規定数値範囲内にすることができる。
より具体的に言えば、ターゲット表面の最大磁束密度を大にすることによって格子定数が小さくなり、また、バイアス電圧の絶対値を大きくすることによって格子定数が小さくなる。
When the (Al, Ti) N layer having a lattice constant within the predetermined numerical range defined above is formed using, for example, an arc ion plating (hereinafter referred to as “AIP”) apparatus shown in FIG. As the target, an Al—Ti alloy having a component composition of 70 atomic% Al-30 atomic% Ti to 50 atomic% Al-50 atomic% Ti is used, and the maximum magnetic flux density and bias voltage on the target surface during film formation are controlled. As a result, the lattice constant of the (Al, Ti) N layer can be set within the specified numerical range.
More specifically, the lattice constant is decreased by increasing the maximum magnetic flux density on the target surface, and the lattice constant is decreased by increasing the absolute value of the bias voltage.
（ｃ）（Ａｌ，Ｔｉ）Ｎ層のＸ線回折ピーク強度比Ｉ（２００）／Ｉ（１１１）：
本発明では、硬質被覆層を構成する（Ａｌ，Ｔｉ）Ｎ層について、（１１１）面の回折ピーク強度Ｉ（１１１）に対する（２００）面の回折ピーク強度Ｉ（２００）の比の値Ｉ（２００）／Ｉ（１１１）を３以上としているが、その理由は以下のとおりである。
本発明の硬質被覆層を構成する（Ａｌ，Ｔｉ）Ｎ層は立方晶構造を有するが、立方晶結晶格子の（１１１）面はすべり面であるため、強い配向を示す場合には、例えば、切削加工時せん断方向の外力が加わることで硬質被覆層の強度を保てないため、耐摩耗性を確保することができない。
一方、立方晶結晶格子の（２００）面は、最密面であるために硬質被覆層の硬さ向上における効果が大きい。
つまり、回折ピーク強度比Ｉ（２００）／Ｉ（１１１）が３未満である場合には、すべり面である（１１１）面の配向度が、硬さの大きい（２００）面に比して相対的に高いため、すべりが発生し易く、しかも、硬さが十分とはいえないことから、切削加工時における耐摩耗性が十分であるとはいえない。
したがって、上記結晶格子面が備える特徴の観点から、本発明の硬質被覆層を構成する（Ａｌ，Ｔｉ）Ｎ層について、耐摩耗性の向上を図るため、（１１１）面の回折ピーク強度Ｉ（１１１）に対する（２００）面の回折ピーク強度Ｉ（２００）の比の値Ｉ（２００）／Ｉ（１１１）を３以上と定めた。
なお、（１１１）面の回折ピーク強度Ｉ（１１１）に対する（２００）面の回折ピーク強度Ｉ（２００）の比の値Ｉ（２００）／Ｉ（１１１）は２０以上であることが好ましい。
(C) X-ray diffraction peak intensity ratio I (200) / I (111) of (Al, Ti) N layer:
In the present invention, for the (Al, Ti) N layer constituting the hard coating layer, the value I (() of the diffraction peak intensity I (200) of the (200) plane to the diffraction peak intensity I (111) of the (111) plane 200) / I (111) is set to 3 or more for the following reason.
The (Al, Ti) N layer constituting the hard coating layer of the present invention has a cubic structure, but the (111) plane of the cubic crystal lattice is a slip plane. Abrasion resistance cannot be ensured because the strength of the hard coating layer cannot be maintained by applying an external force in the shearing direction during cutting.
On the other hand, since the (200) plane of the cubic crystal lattice is a close-packed surface, the effect of improving the hardness of the hard coating layer is great.
That is, when the diffraction peak intensity ratio I (200) / I (111) is less than 3, the degree of orientation of the (111) plane, which is a slip plane, is relative to that of the (200) plane having a high hardness. Therefore, slip is likely to occur, and the hardness is not sufficient, so that it cannot be said that the wear resistance at the time of cutting is sufficient.
Therefore, from the viewpoint of the characteristics of the crystal lattice plane, in order to improve the wear resistance of the (Al, Ti) N layer constituting the hard coating layer of the present invention, the diffraction peak intensity I ( The value I (200) / I (111) of the diffraction peak intensity I (200) of the (200) plane with respect to (111) was determined to be 3 or more.
Note that the value I (200) / I (111) of the ratio of the diffraction peak intensity I (200) of the (200) plane to the diffraction peak intensity I (111) of the (111) plane is preferably 20 or more.
上記で定めた所定の数値範囲内の回折ピーク強度比Ｉ（２００）／Ｉ（１１１）は、例えば、図１に示すＡＩＰ装置を用いて、以下のとおり作製することができる。
例えば、ＡＩＰ装置における成膜時のバイアス電圧、雰囲気ガス中のＮ２分圧を制御することによって、回折ピーク強度比Ｉ（２００）／Ｉ（１１１）を３以上とした（Ａｌ，Ｔｉ）Ｎ層を形成することができる。
より具体的に言えば、バイアス電圧の絶対値を小さくすることによって、また、雰囲気ガス中のＮ２分圧を高めることによって、回折ピーク強度比Ｉ（２００）／Ｉ（１１１）の値が小さくなる。
The diffraction peak intensity ratio I (200) / I (111) within the predetermined numerical range defined above can be produced, for example, as follows using the AIP apparatus shown in FIG.
For example, the diffraction peak intensity ratio I (200) / I (111) is set to 3 or more by controlling the bias voltage during film formation in the AIP apparatus and the N 2 partial pressure in the atmospheric gas (Al, Ti) N. A layer can be formed.
More specifically, the value of the diffraction peak intensity ratio I (200) / I (111) is decreased by decreasing the absolute value of the bias voltage and increasing the N 2 partial pressure in the atmospheric gas. Become.
（ｄ）硬質被覆層の蒸着形成：
図１（ａ）、（ｂ）に、本発明の硬質被覆層を構成する（Ａｌ，Ｔｉ）Ｎ層を成膜するに好適なＡＩＰ装置を示す。
本発明の硬質被覆層は、例えば、図１（ａ）、（ｂ）に示すＡＩＰ装置において、工具基体の温度を３７０〜４５０℃に維持しつつ、工具基体をＡＩＰ装置内で自公転させ、ターゲット表面に所定の最大磁束密度に制御しながら蒸着することによって形成することができる。
例えば、ＡＩＰ装置の一方には基体洗浄用のＴｉ電極からなるカソード電極、他方には所定組成のＡｌ−Ｔｉ合金からなるターゲット（カソード電極）を設け、
まず、炭化タングステン（ＷＣ）基超硬合金からなる工具基体を洗浄・乾燥し、ＡＩＰ装置内の回転テーブル上に装着し、真空中で基体洗浄用のＴｉ電極とアノード電極との間に１００Ａのアーク放電を発生させて、工具基体に−１０００Ｖのバイアス電圧を印加しつつ工具基体表面をボンバード洗浄し、
ついで、Ａｌ−Ｔｉ合金ターゲットの表面に最大磁束密度２．５〜１５ｍＴ（ミリテスラ）に制御し、
ついで、装置内に反応ガスとして窒素ガスを導入し４〜８Ｐａの雰囲気圧力とし、工具基体の温度を３７０〜４５０℃に維持し、工具基体に―２５〜−１００Ｖのバイアス電圧を印加しつつ、Ａｌ−Ｔｉ合金ターゲット（カソード電極）とアノード電極との間に１００Ａのアーク放電を発生させ、工具基体を自公転させつつ蒸着することによって、本発明で定めた格子定数及び回折ピーク強度比を有する（Ａｌ，Ｔｉ）Ｎ層からなる硬質被覆層を蒸着形成することができる。
なお、上記のＡｌ−Ｔｉ合金ターゲット表面の最大磁束密度の制御方法は、例えば、カソード周辺に磁場発生源である電磁コイル又は永久磁石を設置する等、任意の手段で制御することができる。
(D) Vapor deposition of hard coating layer:
FIGS. 1A and 1B show an AIP apparatus suitable for forming an (Al, Ti) N layer constituting the hard coating layer of the present invention.
The hard coating layer of the present invention, for example, in the AIP apparatus shown in FIGS. 1A and 1B, revolves the tool base in the AIP apparatus while maintaining the temperature of the tool base at 370 to 450 ° C. It can form by vapor-depositing on the target surface, controlling to a predetermined maximum magnetic flux density.
For example, one of the AIP devices is provided with a cathode electrode made of a Ti electrode for substrate cleaning, and the other is provided with a target (cathode electrode) made of an Al—Ti alloy having a predetermined composition,
First, a tool substrate made of tungsten carbide (WC) -based cemented carbide is cleaned and dried, mounted on a rotary table in an AIP apparatus, and 100 A between the Ti electrode and the anode electrode for cleaning the substrate in vacuum. An arc discharge is generated, and the tool base surface is bombarded while applying a bias voltage of −1000 V to the tool base,
Next, the maximum magnetic flux density on the surface of the Al—Ti alloy target is controlled to 2.5 to 15 mT (millitesla),
Next, nitrogen gas is introduced as a reaction gas into the apparatus to make the atmospheric pressure 4 to 8 Pa, the temperature of the tool base is maintained at 370 to 450 ° C., and a bias voltage of −25 to −100 V is applied to the tool base, By generating an arc discharge of 100 A between the Al—Ti alloy target (cathode electrode) and the anode electrode and performing evaporation while rotating the tool base, the lattice constant and diffraction peak intensity ratio defined in the present invention are obtained. A hard coating layer composed of an (Al, Ti) N layer can be formed by vapor deposition.
The method for controlling the maximum magnetic flux density on the surface of the Al—Ti alloy target can be controlled by any means, for example, by installing an electromagnetic coil or a permanent magnet as a magnetic field generation source around the cathode.
この発明の被覆工具は、硬質被覆層を構成する所定組成の（Ａｌ，Ｔｉ）Ｎ層が、−０．０５７ｘ＋４．１８（Å）〜−０．０５７ｘ＋４．２４（Å）という格子定数を備え、さらに、Ｘ線回折ピーク強度比Ｉ（２００）／Ｉ（１１１）の値が３以上であることから、ステンレス鋼、合金工具鋼などの高速ミーリング加工において、すぐれた耐摩耗性を示し、長期の使用に亘ってすぐれた切削性能を発揮するものである。 In the coated tool of the present invention, the (Al, Ti) N layer having a predetermined composition constituting the hard coating layer has a lattice constant of −0.057x + 4.18 (Å) to −0.057x + 4.24 (Å), Further, since the value of the X-ray diffraction peak intensity ratio I (200) / I (111) is 3 or more, it exhibits excellent wear resistance in high-speed milling processing of stainless steel, alloy tool steel, etc. It exhibits excellent cutting performance over use.
つぎに、この発明を実施例により具体的に説明する。 Next, the present invention will be specifically described with reference to examples.
原料粉末として、平均粒径：５．５μｍを有する中粗粒ＷＣ粉末、同０．８μｍの微粒ＷＣ粉末、同１．３μｍのＴａＣ粉末、同１．２μｍのＮｂＣ粉末、同１．２μｍのＺｒＣ粉末、同２．３μｍのＣｒ３Ｃ２粉末、同１．５μｍのＶＣ粉末、同１．０μｍの（Ｔｉ，Ｗ）Ｃ［質量比で、ＴｉＣ／ＷＣ＝５０／５０］粉末、および同１．８μｍのＣｏ粉末を用意し、これら原料粉末をそれぞれ表５に示される配合組成に配合し、さらにワックスを加えてアセトン中で２４時間ボールミル混合し、減圧乾燥した後、１００ＭＰａの圧力で所定形状の各種の圧粉体に押出しプレス成形し、これらの圧粉体を、６Ｐａの真空雰囲気中、７℃／分の昇温速度で１３７０〜１４７０℃の範囲内の所定の温度に昇温し、この温度に１時間保持後、炉冷の条件で焼結して、直径が１０ｍｍの工具基体形成用丸棒焼結体を形成し、さらに前記丸棒焼結体から、研削加工にて、切刃部の直径×長さが６ｍｍ×１３ｍｍの寸法で、ねじれ角３０度の２枚刃ボール形状をもったＷＣ基超硬合金製の工具基体（エンドミル）１〜５をそれぞれ製造した。 As raw material powders, medium coarse WC powder having an average particle diameter of 5.5 μm, fine WC powder of 0.8 μm, TaC powder of 1.3 μm, NbC powder of 1.2 μm, ZrC of 1.2 μm Powder, 2.3 μm Cr 3 C 2 powder, 1.5 μm VC powder, 1.0 μm (Ti, W) C [by mass ratio, TiC / WC = 50/50] powder, and 1 .8 μm Co powder was prepared, each of these raw material powders was blended in the blending composition shown in Table 5, and then added with wax, ball milled in acetone for 24 hours, dried under reduced pressure, and then pressed into a predetermined shape at a pressure of 100 MPa. Extruded and pressed into various types of green compacts, and these green compacts were heated to a predetermined temperature in the range of 1370 to 1470 ° C. at a temperature increase rate of 7 ° C./min in a 6 Pa vacuum atmosphere. Conditions for furnace cooling after holding at this temperature for 1 hour Sintered to form a round tool sintered body for forming a tool base having a diameter of 10 mm, and further, from the round bar sintered body, the diameter x length of the cutting edge portion is 6 mm x 13 mm by grinding. Thus, tool bases (end mills) 1 to 5 made of a WC-base cemented carbide having a two-blade ball shape with a twist angle of 30 degrees were manufactured.
（ａ）上記の工具基体１〜５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に示すＡＩＰ装置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、ＡＩＰ装置の一方にボンバード洗浄用のＴｉカソード電極を、他方側に所定組成のＡｌ−Ｔｉ合金からなるターゲット（カソード電極）を配置し、
（ｂ）まず、装置内を排気して真空に保持しながら、ヒータで工具基体を４００℃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、Ｔｉ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）ついで、上記Ａｌ−Ｔｉ合金ターゲットの表面に表２に示す種々の最大磁束密度に制御し、
（ｄ）ついで、装置内に反応ガスとして窒素ガスを導入して表２に示す窒素分圧とすると共に、前記回転テーブル上で自転しながら回転する工具基体の温度を３７０〜４５０℃の範囲内に維持するとともに表２に示す直流バイアス電圧を印加し、かつ前記Ａｌ−Ｔｉ合金ターゲット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、もって前記工具基体の表面に、表２に示される組成および目標平均層厚の（Ａｌ，Ｔｉ）Ｎ層からなる硬質被覆層を蒸着形成することにより、
表２に示す本発明被覆工具としての表面被覆エンドミル１〜１０（以下、本発明１〜１０という）をそれぞれ製造した。
なお、図１に示すＡＩＰ装置では、工具基体がＡｌ−Ｔｉ合金ターゲットに最接近する際に、逃げ面の一部又は全部とＡｌ−Ｔｉ合金ターゲットの上記工具基体側の面が水平となるように装着支持されている。
(A) Each of the tool bases 1 to 5 described above is ultrasonically cleaned in acetone and dried, at a position spaced apart from the central axis on the rotary table of the AIP device shown in FIG. 1 by a predetermined distance in the radial direction. Attached along the outer periphery, a Ti cathode electrode for bombard cleaning is disposed on one side of the AIP apparatus, and a target (cathode electrode) made of an Al—Ti alloy having a predetermined composition is disposed on the other side.
(B) First, the tool base is heated to 400 ° C. with a heater while the inside of the apparatus is evacuated and kept in vacuum, and then a DC bias voltage of −1000 V is applied to the tool base that rotates while rotating on the rotary table. And an arc discharge is caused by flowing a current of 100 A between the Ti cathode electrode and the anode electrode, thereby bombarding the surface of the tool substrate,
(C) Next, the various maximum magnetic flux densities shown in Table 2 are controlled on the surface of the Al-Ti alloy target,
(D) Next, nitrogen gas is introduced into the apparatus as a reactive gas to obtain the nitrogen partial pressure shown in Table 2, and the temperature of the tool base rotating while rotating on the rotary table is within a range of 370 to 450 ° C. And a DC bias voltage shown in Table 2 is applied, and an electric current of 100 A is passed between the Al—Ti alloy target and the anode electrode to generate an arc discharge. 2 by vapor deposition of a hard coating layer composed of an (Al, Ti) N layer having a composition and a target average layer thickness shown in FIG.
Surface coated end mills 1 to 10 (hereinafter referred to as present inventions 1 to 10) as the present invention coated tools shown in Table 2 were produced.
In the AIP apparatus shown in FIG. 1, when the tool base comes closest to the Al—Ti alloy target, part or all of the flank and the surface of the Al—Ti alloy target on the tool base side are horizontal. It is supported by mounting.
比較例：
比較の目的で、上記実施例における（ｃ）の工程を表３に示す条件（即ち、Ａｌ−Ｔｉ合金ターゲットの表面の最大磁束密度を変更）で行い、また、（ｄ）の工程を同じく表３に示す条件（即ち、窒素分圧、直流バイアス電圧の変更）で行い、その他は実施例と同一の条件で、表３に示す比較例被覆工具としての表面被覆エンドミル１〜１０（以下、比較例１〜１０という）をそれぞれ製造した。
さらに、上記で作製した本発明１〜１０および比較例１〜１０の硬質被覆層について、その組成を走査型電子顕微鏡（ＳＥＭ）を用いてのエネルギー分散型Ｘ線分析法（ＥＤＳ）により測定した。また、その平均層厚を走査型電子顕微鏡を用いて断面測定し、５ヶ所の平均値より算出した。
表２、表３に、測定・算出したしたそれぞれの値を示す。
Comparative example:
For the purpose of comparison, the step (c) in the above example is performed under the conditions shown in Table 3 (that is, the maximum magnetic flux density on the surface of the Al—Ti alloy target is changed), and the step (d) is also represented in the same manner. Surface coating end mills 1 to 10 (hereinafter referred to as comparisons) as comparative example coating tools shown in Table 3 are performed under the conditions shown in FIG. 3 (ie, changes in nitrogen partial pressure and DC bias voltage), and the other conditions are the same as in the examples. Examples 1 to 10) were produced respectively.
Furthermore, about the hard coating layer of this invention 1-10 produced above and Comparative Examples 1-10, the composition was measured by the energy dispersive X ray analysis method (EDS) using a scanning electron microscope (SEM). . The average layer thickness was measured by a cross-section using a scanning electron microscope, and calculated from the average value at five locations.
Tables 2 and 3 show the measured and calculated values.
上記で作製した本発明１〜１０および比較例１〜１０について、硬質被覆層の縦断面の（Ａｌ，Ｔｉ）Ｎ層について、Ｘ線回折により、（１１１）面、（２００）面及び（２２０）面のＸ線回折ピーク強度Ｉ（１１１），Ｉ（２００）及びＩ（２２０）を求めた。
なお、Ｘ線回折は、測定条件:Ｃｕ管球、測定範囲（２θ）：３０〜８０度、スキャンステップ：０．０１３度、１ステップ辺り測定時間：０．４８ｓｅｃ／ｓｔｅｐという条件で測定した。
About this invention 1-10 produced above and Comparative Examples 1-10, about the (Al, Ti) N layer of the longitudinal cross-section of a hard coating layer, (111) plane, (200) plane, and (220) by X-ray diffraction. ) Plane X-ray diffraction peak intensities I (111), I (200) and I (220).
X-ray diffraction was measured under the conditions of measurement conditions: Cu tube, measurement range (2θ): 30 to 80 degrees, scan step: 0.013 degrees, measurement time per step: 0.48 sec / step.
また、格子定数については、当業者によく知られている
ブラッグの式：２ｄ＝λ／ｓｉｎθ，
ａ２＝ｄ２×（ｈ２＋ｋ２＋ｌ２）
を用い、上記で測定した（１１１）面，（２００）面及び（２２０）面についてそれぞれ算出し、その平均値を求め、これを格子定数とした。
なお、上記ブラッグの式におけるｄ：面間隔、λ：測定波長、θ：測定角度、ａ：格子定数、ｈ，ｋ，ｌ：面指数を表す。
表２、表３に、上記で測定・算出したそれぞれの値を示す。
As for the lattice constant, Bragg's formula well known to those skilled in the art: 2d = λ / sin θ,
a 2 = d 2 × (h 2 + k 2 + l 2 )
The (111) plane, the (200) plane, and the (220) plane measured above were respectively calculated, the average value was obtained, and this was used as the lattice constant.
In the above Bragg equation, d: surface spacing, λ: measurement wavelength, θ: measurement angle, a: lattice constant, h, k, l: surface index.
Tables 2 and 3 show the values measured and calculated above.
つぎに、上記本発明１〜１０および比較例１〜１０のエンドミルについて、下記の条件（切削条件Ａという）での合金工具鋼の側面切削加工試験を実施した。
被削材−平面寸法：１００ｍｍ×２５０ｍｍ、厚さ：５０ｍｍのＪＩＳ・ＳＫＤ６１（５２ＨＲＣ）の板材、
回転速度： １７０００ ｍｉｎ．−１、
縦方向切り込み： ２ ｍｍ、
横方向切り込み： ０．３ ｍｍ
送り速度（１刃当り）： ０．０５ ｍｍ／ｔｏｏｔｈ、
切削長：３４０ｍ、
さらに、下記の条件（切削条件Ｂという）でのステンレス鋼の側面切削加工試験を実施した。
被削材−平面寸法：１００ｍｍ×２５０ｍｍ、厚さ：５０ｍｍのＪＩＳ・ＳＵＳ３０４ （３５ＨＲＣ）の板材、
回転速度： ５６００ ｍｉｎ．−１、
縦方向切り込み： ２ ｍｍ、
横方向切り込み： ０．３ ｍｍ
送り速度（１刃当り）： ０．０６ ｍｍ／ｔｏｏｔｈ、
切削長：１４０ ｍ、
いずれの側面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４に示した。
Next, for the end mills of the present inventions 1 to 10 and Comparative Examples 1 to 10, a side cutting test of the alloy tool steel was performed under the following conditions (referred to as cutting conditions A).
Work material-Plane dimensions: 100 mm x 250 mm, thickness: 50 mm JIS / SKD61 (52HRC) plate material,
Rotational speed: 17000 min. -1 ,
Longitudinal cut: 2 mm,
Horizontal infeed: 0.3 mm
Feed rate (per blade): 0.05 mm / tooth,
Cutting length: 340m,
Further, a side cutting test of stainless steel was performed under the following conditions (referred to as cutting conditions B).
Work material-Plane dimensions: 100 mm x 250 mm, thickness: 50 mm JIS / SUS304 (35HRC) plate material,
Rotational speed: 5600 min. -1 ,
Longitudinal cut: 2 mm,
Horizontal infeed: 0.3 mm
Feed rate (per blade): 0.06 mm / tooth,
Cutting length: 140 m,
In any side cutting test, the flank wear width of the cutting edge was measured.
The measurement results are shown in Table 4.
表４に示される結果から、本発明被覆工具は、硬質被覆層を構成する所定組成の（Ａｌ，Ｔｉ）Ｎ層が、−０．０５７ｘ＋４．１８（Å）〜−０．０５７ｘ＋４．２４（Å）という格子定数を備え、さらに、Ｘ線回折ピーク強度比Ｉ（２００）／Ｉ（１１１）の値が３以上であることから、ステンレス鋼、合金工具鋼などの高速ミーリング加工において、すぐれた耐摩耗性を示し、長期の使用に亘ってすぐれた切削性能を発揮するものである。
これに対して、硬質被覆層を構成する（Ａｌ，Ｔｉ）Ｎ層の組成、格子定数、Ｘ線回折ピーク強度比、平均層厚が本発明で規定する範囲を外れる比較例被覆工具では、耐摩耗性の低下によって、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 Table 4, according to the coated tool of the present invention, the (Al, Ti) N layer of the predetermined composition constituting the hard coating layer is −0.057x + 4.18 (Å) to −0.057x + 4.24 (Å ), And the X-ray diffraction peak intensity ratio I (200) / I (111) is 3 or more, so that it has excellent resistance to high-speed milling such as stainless steel and alloy tool steel. It exhibits wear and exhibits excellent cutting performance over a long period of use.
On the other hand, in the comparative coated tool in which the composition, lattice constant, X-ray diffraction peak intensity ratio, and average layer thickness of the (Al, Ti) N layer constituting the hard coating layer are outside the range defined in the present invention, It is clear that the wear life is reduced 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、ステンレス鋼、合金工具鋼などの高速ミーリング加工に供した場合に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 exhibits excellent cutting performance over a long period when subjected to high-speed milling processing such as stainless steel and alloy tool steel. In addition, it is possible to sufficiently satisfy the labor-saving and energy-saving of the cutting process and the cost reduction.
Claims (1)
（ａ）前記硬質被覆層は、ＡｌとＴｉの複合窒化物層からなり、かつ、該層においてＡｌとＴｉの合量に占めるＡｌの含有割合ｘは、０．４０≦ｘ≦０．７５（但し、原子比）であり、
（ｂ）前記硬質被覆層を構成するＡｌとＴｉの複合窒化物層の格子定数は、−０．０５７ｘ＋４．１８（Å）〜−０．０５７ｘ＋４．２４（Å）の範囲内の値をとり、
（ｃ）Ｘ線回折による前記ＡｌとＴｉの複合窒化物層の（１１１）面の回折ピーク強度Ｉ（１１１）に対する（２００）面の回折ピーク強度Ｉ（２００）の比の値Ｉ（２００）／Ｉ（１１１）が３以上であることを特徴とする表面被覆切削工具。
In a surface-coated cutting tool in which a hard coating layer having an average layer thickness of 2 to 10 μm is vapor-deposited on the surface of a tool base composed of a tungsten carbide-based cemented carbide,
(A) The hard coating layer is composed of a composite nitride layer of Al and Ti, and the Al content ratio x in the total amount of Al and Ti in the layer is 0.40 ≦ x ≦ 0.75 ( However, atomic ratio)
(B) The lattice constant of the composite nitride layer of Al and Ti constituting the hard coating layer takes a value in the range of −0.057x + 4.18 (Å) to −0.057x + 4.24 (Å),
(C) A value I (200) of the ratio of the diffraction peak intensity I (200) of the (200) plane to the diffraction peak intensity I (111) of the (111) plane of the composite nitride layer of Al and Ti by X-ray diffraction A surface-coated cutting tool having a / I (111) of 3 or more.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2014059035A JP6233708B2 (en) | 2014-03-20 | 2014-03-20 | Surface coated cutting tool |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2014059035A JP6233708B2 (en) | 2014-03-20 | 2014-03-20 | Surface coated cutting tool |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JP2015182153A true JP2015182153A (en) | 2015-10-22 |
| JP6233708B2 JP6233708B2 (en) | 2017-11-22 |
Family
ID=54349307
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP2014059035A Active JP6233708B2 (en) | 2014-03-20 | 2014-03-20 | Surface coated cutting tool |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JP6233708B2 (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2018202533A (en) * | 2017-06-01 | 2018-12-27 | 住友電気工業株式会社 | Surface-coated cutting tool |
| US10737331B2 (en) | 2016-03-31 | 2020-08-11 | Tungaloy Corporation | Coated cutting tool |
| WO2024115196A1 (en) * | 2022-11-28 | 2024-06-06 | Ab Sandvik Coromant | A coated cutting tool |
Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH10317123A (en) * | 1997-05-16 | 1998-12-02 | Toshiba Tungaloy Co Ltd | Crystalline oriented hard coated member |
| JPH11335813A (en) * | 1998-05-21 | 1999-12-07 | Sumitomo Electric Ind Ltd | Hard coating film and laminated hard coating film |
| JP2001516654A (en) * | 1997-09-12 | 2001-10-02 | ユナキス・バルツェルス・アクチェンゲゼルシャフト | Tool with protective layer system |
| US20080273933A1 (en) * | 2004-09-10 | 2008-11-06 | Mats Ahlgren | Pvd-Coated Cutting Tool Insert |
| JP2010012564A (en) * | 2008-07-04 | 2010-01-21 | Hitachi Tool Engineering Ltd | Hard film-coated cutting tool |
| JP2011189419A (en) * | 2010-03-12 | 2011-09-29 | Hitachi Metals Ltd | Coated tool excellent in wear resistance |
| JP2012161909A (en) * | 2011-02-07 | 2012-08-30 | Kennametal Inc | Cubic aluminum titanium nitride coating and method for manufacturing the same |
-
2014
- 2014-03-20 JP JP2014059035A patent/JP6233708B2/en active Active
Patent Citations (7)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH10317123A (en) * | 1997-05-16 | 1998-12-02 | Toshiba Tungaloy Co Ltd | Crystalline oriented hard coated member |
| JP2001516654A (en) * | 1997-09-12 | 2001-10-02 | ユナキス・バルツェルス・アクチェンゲゼルシャフト | Tool with protective layer system |
| JPH11335813A (en) * | 1998-05-21 | 1999-12-07 | Sumitomo Electric Ind Ltd | Hard coating film and laminated hard coating film |
| US20080273933A1 (en) * | 2004-09-10 | 2008-11-06 | Mats Ahlgren | Pvd-Coated Cutting Tool Insert |
| JP2010012564A (en) * | 2008-07-04 | 2010-01-21 | Hitachi Tool Engineering Ltd | Hard film-coated cutting tool |
| JP2011189419A (en) * | 2010-03-12 | 2011-09-29 | Hitachi Metals Ltd | Coated tool excellent in wear resistance |
| JP2012161909A (en) * | 2011-02-07 | 2012-08-30 | Kennametal Inc | Cubic aluminum titanium nitride coating and method for manufacturing the same |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US10737331B2 (en) | 2016-03-31 | 2020-08-11 | Tungaloy Corporation | Coated cutting tool |
| JP2018202533A (en) * | 2017-06-01 | 2018-12-27 | 住友電気工業株式会社 | Surface-coated cutting tool |
| WO2024115196A1 (en) * | 2022-11-28 | 2024-06-06 | Ab Sandvik Coromant | A coated cutting tool |
Also Published As
| Publication number | Publication date |
|---|---|
| JP6233708B2 (en) | 2017-11-22 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| JP5344204B2 (en) | Surface coated cutting tool | |
| JP5838769B2 (en) | Surface coated cutting tool | |
| KR102523236B1 (en) | surface coating cutting tools | |
| JP4748450B2 (en) | A surface-coated cutting tool that exhibits excellent chipping resistance with a hard coating layer in high-speed intermittent cutting | |
| WO2017073653A1 (en) | Surface coated cutting tool | |
| JP2017064845A (en) | Surface coating cutting tool excellent in chipping resistance and abrasion resistance | |
| JP6233708B2 (en) | Surface coated cutting tool | |
| JP5850400B2 (en) | Surface coated cutting tool | |
| JP6296295B2 (en) | Surface coated cutting tool with excellent wear resistance | |
| KR102498224B1 (en) | surface coating cutting tools | |
| WO2014148488A1 (en) | Surface-coated cutting tool | |
| JP6493800B2 (en) | Surface coated cutting tool with excellent wear resistance in high speed cutting | |
| JP6604138B2 (en) | Surface-coated cutting tool having excellent chipping resistance and wear resistance with a hard coating layer and method for producing the same | |
| JP5240666B2 (en) | Surface-coated cutting tool with excellent chip evacuation | |
| JP6102571B2 (en) | Surface coated cutting tool | |
| JP6288603B2 (en) | Surface coated cutting tool | |
| WO2017073655A1 (en) | Surface coated cutting tool | |
| JP6217216B2 (en) | Surface coated cutting tool and manufacturing method thereof | |
| JP5850393B2 (en) | Surface coated cutting tool | |
| JP5240665B2 (en) | Surface-coated cutting tool with excellent chip evacuation | |
| JP6399353B2 (en) | Surface coated cutting tool with excellent chipping resistance and wear resistance | |
| JP5831708B2 (en) | Surface coated cutting tool | |
| JP2019171483A (en) | Surface-coated cutting tool | |
| JP6090033B2 (en) | Surface coated cutting tool | |
| JP2012030346A (en) | Surface coated drill excellent in wear resistance and chip discharging characteristics |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| A621 | Written request for application examination |
Free format text: JAPANESE INTERMEDIATE CODE: A621 Effective date: 20160929 |
|
| A131 | Notification of reasons for refusal |
Free format text: JAPANESE INTERMEDIATE CODE: A131 Effective date: 20170728 |
|
| A977 | Report on retrieval |
Free format text: JAPANESE INTERMEDIATE CODE: A971007 Effective date: 20170726 |
|
| A521 | Request for written amendment filed |
Free format text: JAPANESE INTERMEDIATE CODE: A523 Effective date: 20170919 |
|
| 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: 20170929 |
|
| A61 | First payment of annual fees (during grant procedure) |
Free format text: JAPANESE INTERMEDIATE CODE: A61 Effective date: 20171012 |
|
| R150 | Certificate of patent or registration of utility model |
Ref document number: 6233708 Country of ref document: JP Free format text: JAPANESE INTERMEDIATE CODE: R150 |