JP4329969B2 - Surface-coated cutting tip whose hard coating layer exhibits excellent heat-resistant plastic deformation in high-speed cutting of difficult-to-cut materials - Google Patents
Surface-coated cutting tip whose hard coating layer exhibits excellent heat-resistant plastic deformation in high-speed cutting of difficult-to-cut materials Download PDFInfo
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Description
【０００１】
【発明の属する技術分野】
この発明は、特に材質的に粘性が高いために、高い切削抵抗を示すステンレス鋼や軟鋼などの難削材を高速切削した場合に発生する高熱に対して、硬質被覆層がすぐれた耐熱塑性変形性を発揮し、これによって偏摩耗が著しく抑制されることから、すぐれた切削性能を長期に亘って発揮するようになる表面被覆切削チップ（以下、被覆切削チップという）に関するものである。
【０００２】
【従来の技術】
従来、一般に、炭化タングステン（以下、ＷＣで示す）基超硬合金または炭窒化チタン（以下、ＴｉＣＮで示す）基サーメットからなる基体の表面に、硬質被覆層を５〜３０μｍの平均層厚で化学蒸着してなる被覆切削チップが知られている。
【０００３】
また、上記の被覆切削チップにおいて、これの硬質被覆層を、
（ａ）下部層として、いずれも粒状結晶組織を有する、Ｔｉの炭化物（以下、ＴｉＣで示す）層、窒化物（以下、同じくＴｉＮで示す）層、炭窒化物（以下、ＴｉＣＮで示す）層、炭酸化物（以下、ＴｉＣＯで示す）層、および炭窒酸化物（以下、ＴｉＣＮＯで示す）層からなるＴｉの炭・窒・酸化物（以下、ＴｉＣ・Ｎ・Ｏで示す）層のうちの１層または２層以上と、縦長成長結晶組織を有するＴｉの炭窒化物（以下、ｌ−ＴｉＣＮで示す）層、
（ｂ）上部層として、同じく粒状結晶組織を有する酸化アルミニウム（以下、Ａｌ2Ｏ3で示す）層、
以上（ａ）および（ｂ）で構成すると共に、その層厚を、上記Ｔｉ炭・窒・酸化物層は相対的に薄く、一方上記Ａｌ2Ｏ3層およびｌ−ＴｉＣＮ層は相対的に厚膜化した状態で適用されている被覆切削チップも知られており、これが各種の鋼や鋳鉄などの連続切削や断続切削に用いられていることも良く知られるところである。
【０００４】
さらに、上記の従来被覆切削チップの硬質被覆層を構成するＡｌ2Ｏ3層として、α型結晶構造をもつものやκ型結晶構造をもつものなどが広く実用に供され、また、同じく硬質被覆層を構成する上記のｌ−ＴｉＣＮ層は、例えば特開平６−８０１０号公報や特開平７−３２８８０８号公報などに記載される通り、通常の化学蒸着装置にて、反応ガスとして有機炭窒化物を含む混合ガスを使用し、７００〜９５０℃の中温温度域で化学蒸着することにより形成され、層自身すぐれた靭性を具備することも知られている。
【０００５】
【発明が解決しようとする課題】
一方、近年の切削加工に対する省力化および省エネ化、さらに低コスト化の要求は強く、これに伴い、切削加工は高速化の傾向にあるが、上記の従来被覆切削チップにおいては、これを鋼や鋳鉄などの通常の条件での切削加工に用いた場合には問題はないが、これを特に材質的に粘性が高く、高い切削抵抗を示すステンレス鋼や軟鋼などの難削材の高速切削に用いると、この切削では著しい高熱の発生を伴なうために、硬質被覆層のうち、厚膜化しても耐熱性のすぐれたＡｌ2Ｏ3層には問題はないが、特に同じく厚膜化の傾向にある一方で、耐熱性の劣るｌ−ＴｉＣＮ層に熱塑性変形が発生し易くなり、これが原因で切刃面に偏摩耗が発生し、この結果比較的短時間で使用寿命に至るのが現状である。
【０００６】
【課題を解決するための手段】
そこで、本発明者等は、上述のような観点から、特に高熱発生を伴なうステンレス鋼や軟鋼などの難削材の高速切削加工に用いた場合にも、切刃面に偏摩耗の発生がない被覆切削チップを開発すべく、特に被覆切削チップの硬質被覆層のうちのｌ−ＴｉＣＮ層に着目し、これの耐熱塑性変形性の向上を目的として研究を行った結果、
（ａ）上記の従来被覆切削チップの硬質被覆層の構成層であるｌ−ＴｉＣＮ層を、通常の化学蒸着装置にて形成するに際して、反応ガス中に四塩化バナジウムを配合した条件、例えば具体的には、
反応ガス組成を、体積％で、
ＴｉＣｌ4：０．５〜５％、
ＶＣｌ4：０．０１〜０．５％、
ＣＨ3ＣＮ：０．０５〜１％、
Ａｒ：５〜４０％、
Ｎ2：３〜４５％、
Ｈ2：残り、
とし、かつ、
反応雰囲気温度：８００〜９５０℃、
反応雰囲気圧力：４〜６０ｋＰａ、
の条件で層形成を行うと、上記ｌ−ＴｉＣＮ層にＶ成分が含有してなるＴｉとＶの複合炭窒化物層が形成されること。
【０００７】
（ｂ）上記（ａ）で得られたＴｉとＶの複合炭窒化物層は、上記ｌ−ＴｉＣＮ層と同じく縦長成長結晶組織を保持するので、すぐれた靭性を有するが、これに含有するＶ成分の割合を、Ｔｉ成分との合量に占める割合で、１〜３０原子％とすると、この結果の縦長成長結晶組織を有するＴｉとＶの複合炭窒化物［以下、ｌ−（Ｔｉ，Ｖ）ＣＮで示す］層は、Ｖ成分の含有によって耐熱性が著しく向上し、すぐれた耐熱塑性変形性を具備するようになること。
【０００８】
（ｃ）上記ｌ−（Ｔｉ，Ｖ）ＣＮ層を硬質被覆層の構成層として適用した被覆切削チップをステンレス鋼や軟鋼などの難削材の高熱発生を伴なう高速切削加工に、前記ｌ−（Ｔｉ，Ｖ）ＣＮ層を厚膜化した状態で用いても、前記ｌ−（Ｔｉ，Ｖ）ＣＮ層自体が上記の通りすぐれた耐熱塑性変形性を有し、かつ同じく硬質被覆層を構成するＡｌ2Ｏ3層も耐熱塑性変形性にすぐれ、一方同ＴｉＣ・Ｎ・Ｏ層は、十分な耐熱塑性変形性を具備するものではないが、前記ｌ−（Ｔｉ，Ｖ）ＣＮ層およびＡｌ2Ｏ3層に比して層厚が相対的にきわめて薄いことから、硬質被覆層の熱塑性変形にはほとんど影響を及ぼすことがなく、この結果切刃面に偏摩耗の発生がなくなり、切刃面は正常摩耗を保持しながら、長期に亘ってすぐれた切削性能を発揮すること。
以上（ａ）〜（ｃ）に示される研究結果が得られたのである。
【０００９】
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、ＷＣ基超硬合金またはＴｉＣＮ基サーメットからなる基体の表面に、
（ａ）下部層として、ＴｉＣ層、ＴｉＮ層、ＴｉＣＮ層、ＴｉＣＯ層、およびＴｉＣＮＯ層からなるＴｉＣ・Ｎ・Ｏ層のうちの１層または２層以上と、ＶをＴｉとの合量に占める割合で１〜３０原子％含有するｌ−（Ｔｉ，Ｖ）ＣＮ層、
（ｂ）上部層として、Ａｌ2Ｏ3層、
以上（ａ）および（ｂ）で構成してなる硬質被覆層を５〜３０μｍの平均層厚で化学蒸着してなる、硬質被覆層が難削材の高速切削加工ですぐれた耐熱塑性変形性を発揮する被覆切削チップに特徴を有するものである。
【００１０】
なお、この発明の被覆切削チップにおいて、硬質被覆層を構成するｌ−（Ｔｉ，Ｖ）ＣＮ層のＶの含有割合を、Ｔｉ成分との合量に占める割合で１〜３０原子％としたのは、その割合が１原子％未満ではＶ成分によってもたらされる耐熱塑性変形性に所望の向上効果が得られず、一方その割合が３０原子％を越えると、縦長成長結晶組織によってもたらされるすぐれた靭性に低下傾向が現れるようになるという理由からであり、望ましくは３〜１５原子％の含有割合とするのがよい。
また、硬質被覆層の平均層厚を５〜３０μｍとしたのは、その層厚が５μｍでは所望のすぐれた耐摩耗性を確保することができず、一方その層厚が３０μｍを越えると、切刃に欠けやチッピングが発生し易くなるという理由によるものである。
【００１１】
【発明の実施の形態】
つぎに、この発明の被覆切削チップを実施例により具体的に説明する。
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、ＶＣ粉末、ＴａＣ粉末、ＮｂＣ粉末、Ｃｒ3 Ｃ2 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、１２０ＭＰａ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：１４１０℃に１時間保持の条件で真空焼結し、焼結後、切刃部分にＲ：０．０５ｍｍのホーニング加工を施してＩＳＯ規格・ＣＮＭＧ１２０４０８のチップ形状をもち、かつＷＣ基超硬合金で構成された基体Ａ−１，Ａ−５，Ａ−６，Ａ−８を形成した。
【００１２】
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、Ｍｏ2 Ｃ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１．３ｋＰａ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、切刃部分にＲ：０．０３ｍｍのホーニング加工を施してＩＳＯ規格・ＣＮＭＧ１２０４１２のチップ形状をもち、かつＴｉＣＮ基サーメットで構成された基体Ｂ−１，Ｂ−２〜Ｂ−４，Ｂ−６を形成した。
【００１３】
ついで、これらの基体Ａ−１，Ａ−５，Ａ−６，Ａ−８および同Ｂ−１，Ｂ−２〜Ｂ−４，Ｂ−６の表面に、通常の化学蒸着装置を用い、表３、４に示される条件にて、ＴｉＣ・Ｎ・Ｏ層およびＡｌ2Ｏ3層、さらにｌ−（Ｔｉ，Ｖ）ＣＮ層またはｌ−ＴｉＣＮ層からなる硬質被覆層を表５、６に示される目標層厚および組み合わせで形成することにより、本発明被覆切削チップ１〜８および従来被覆切削チップ１〜８をそれぞれ製造した。
【００１４】
この結果の本発明被被覆切削チップ１〜８の硬質被覆層を構成するｌ−（Ｔｉ，Ｖ）ＣＮ層におけるＶ成分の含有割合を、オージェ分光分析装置を用いて測定したところ、目標含有割合と実質的に同じ含有割合を示し、また本発明被覆切削チップ１〜８および従来被覆切削チップ１〜８の硬質被覆層の構成層の厚さを、それぞれ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層厚（５点測定の平均値）を示した。
【００１５】
つぎに、上記本発明被覆切削チップ１〜８および従来被覆切削チップ１〜８について、これを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、
被削材：ＪＩＳ・ＳＵＳ３０４の丸棒、
切削速度：２２０ｍ／ｍｉｎ、
切り込み：２ｍｍ、
送り：０．２５ｍｍ／ｒｅｖ、
切削時間：１０分、
の条件でのステンレス鋼１の乾式高速連続旋削加工試験、
被削材：ＪＩＳ・Ｓ１５Ｃの丸棒、
切削速度：４５０ｍ／ｍｉｎ、
切り込み：２ｍｍ、
送り：０．２５ｍｍ／ｒｅｖ、
切削時間：１０分、
の条件での軟鋼１の乾式高速連続旋削加工試験、さらに、
被削材：ＪＩＳ・ＳＵＳ３０４の長さ方向等間隔４本縦溝入り丸棒、
切削速度：２００ｍ／ｍｉｎ、
切り込み：２ｍｍ、
送り：０．２ｍｍ／ｒｅｖ、
切削時間：５分、
の条件でのステンレス鋼２の乾式高速断続旋削加工試験、
被削材：ＪＩＳ・Ｓ１５Ｃの長さ方向等間隔４本縦溝入り丸棒、
切削速度：３００ｍ／ｍｉｎ、
切り込み：１．５ｍｍ、
送り：０．５ｍｍ／ｒｅｖ、
切削時間：５分、
の条件での軟鋼２の乾式高速断続旋削加工試験を行い、いずれの旋削加工試験でも切刃の最大逃げ面摩耗幅を測定した。この測定結果を表７に示した。
【００１６】
【表１】
【表２】
【表３】
【表４】
【表５】
【表６】
【表７】
【発明の効果】
表５〜７に示される結果から、ｌ−ＴｉＣＮ層に代ってｌ−（Ｔｉ，Ｖ）ＣＮ層を硬質被覆層の構成層とする本発明被覆切削チップ１〜８は、いずれも前記ｌ−（Ｔｉ，Ｖ）ＣＮ層がすぐれた耐熱塑性変形性を具備することから、ステンレス鋼や軟鋼の切削加工を高い発熱を伴う高速で行っても、硬質被覆層の塑性変形が抑制され、この結果切刃部の摩耗は正常摩耗となり、すぐれた耐摩耗性を長期に亘って発揮するのに対して、ｌ−ＴｉＣＮ層を構成層とする従来被覆切削チップ１〜８は、いずれも前記ｌ−ＴｉＣＮ層が切削時の高い発熱で塑性変形を起し、この結果切刃部に偏摩耗が発生し、これが摩耗進行を著しく促進することが明らかである。
上述のように、この発明の被覆切削チップは、各種の鋼や鋳鉄などの通常の条件での切削加工は勿論のこと、特にステンレス鋼や軟鋼などの難削材の高速切削加工でもすぐれた切削性能を発揮し、汎用性のある切削性能を示すものであるから、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。[0001]
BACKGROUND OF THE INVENTION
This invention is particularly resistant to heat and plastic deformation due to its excellent hard coating layer against the high heat generated when cutting difficult-to-cut materials such as stainless steel and mild steel that exhibit high cutting resistance due to its high viscosity. The present invention relates to a surface-coated cutting tip (hereinafter referred to as a coated cutting tip ) that exhibits excellent cutting performance over a long period of time because uneven wear is remarkably suppressed.
[0002]
[Prior art]
Conventionally, in general, a hard coating layer is chemically formed with an average layer thickness of 5 to 30 μm on the surface of a substrate made of tungsten carbide (hereinafter referred to as WC) -based cemented carbide or titanium carbonitride (hereinafter referred to as TiCN) -based cermet. A coated cutting tip formed by vapor deposition is known.
[0003]
Moreover, in the above-mentioned coated cutting tip , this hard coating layer is
(A) Ti carbide (hereinafter referred to as TiC) layer, nitride (hereinafter also referred to as TiN) layer, carbonitride (hereinafter referred to as TiCN) layer each having a granular crystal structure as a lower layer A carbon dioxide (hereinafter referred to as TiCO) layer, and a carbon dioxide (hereinafter referred to as TiCNO) layer of Ti carbon / nitrogen / oxide (hereinafter referred to as TiC / N / O) layer. 1 layer or 2 layers or more and a Ti carbonitride (hereinafter referred to as 1-TiCN) layer having a vertically grown crystal structure,
(B) As an upper layer, an aluminum oxide (hereinafter referred to as Al 2 O 3 ) layer having a granular crystal structure,
It is composed of the above (a) and (b), and the layer thickness of the Ti charcoal / nitrogen / oxide layer is relatively thin, while the Al 2 O 3 layer and l-TiCN layer are relatively thick. A coated cutting tip applied in a film state is also known, and it is well known that this is used for continuous cutting and intermittent cutting of various types of steel and cast iron.
[0004]
Further, as the Al 2 O 3 layer constituting the hard coating layer of the above-mentioned conventional coated cutting chip , those having α-type crystal structure and those having κ-type crystal structure are widely used practically, The l-TiCN layer constituting the layer is an organic carbonitride as a reaction gas in a normal chemical vapor deposition apparatus as described in, for example, JP-A-6-8010 and JP-A-7-328808. It is also known that the layer itself has excellent toughness, formed by chemical vapor deposition at a medium temperature range of 700 to 950 ° C. using a mixed gas containing the above.
[0005]
[Problems to be solved by the invention]
On the other hand, labor saving and energy saving for recent machining, the further cost reduction strongly required, along with this, but cutting tends speeding, in the conventional coated cutting tip described above, which Ya steel There is no problem when it is used for cutting under normal conditions such as cast iron, but it is used for high-speed cutting of difficult-to-cut materials such as stainless steel and mild steel that are particularly viscous and have high cutting resistance. In this cutting, a significant amount of heat is generated, so even if the thickness of the hard coating layer is increased, there is no problem with the Al 2 O 3 layer having excellent heat resistance. On the other hand, the l-TiCN layer with poor heat resistance tends to be subject to thermoplastic deformation, and this causes uneven wear on the cutting edge surface, resulting in a service life in a relatively short time. It is.
[0006]
[Means for Solving the Problems]
In view of the above, the present inventors, in view of the above, generate uneven wear on the cutting edge surface even when used for high-speed cutting of difficult-to-cut materials such as stainless steel and mild steel, particularly with high heat generation. to develop a free coated cutting tip, especially coated cutting tip focuses on l-TiCN layer of the hard coating layer, as a result of studies for the purpose of improving this heat plastic deformation resistance,
(A) When the l-TiCN layer, which is a constituent layer of the hard coating layer of the above-mentioned conventional coated cutting tip , is formed by an ordinary chemical vapor deposition apparatus, the reaction gas is mixed with vanadium tetrachloride, for example, concrete In
Reactive gas composition in volume%
TiCl 4: 0.5~5%,
VCl 4: 0.01~0.5%,
CH 3 CN: 0.05~1%,
Ar: 5 to 40%
N 2 : 3 to 45%,
H 2 : Remaining
And
Reaction atmosphere temperature: 800-950 ° C.
Reaction atmosphere pressure: 4 to 60 kPa,
When the layer is formed under the above conditions, a Ti and V composite carbonitride layer in which the V component is contained in the l-TiCN layer is formed.
[0007]
(B) The composite carbonitride layer of Ti and V obtained in the above (a) retains a vertically grown crystal structure as in the case of the l-TiCN layer, and thus has excellent toughness. When the ratio of the component is 1 to 30 atomic% in the total amount with the Ti component, the resulting composite carbonitride of Ti and V having the vertically elongated crystal structure [hereinafter referred to as l- (Ti, V ) The layer denoted by CN is remarkably improved in heat resistance due to the inclusion of the V component, and has excellent heat-resistant plastic deformation.
[0008]
(C) the l- (Ti, V) the coated cutting tip the CN layer was applied as a layer of a hard coating layer on the accompanying high speed cutting the high heat generation of hard-to-cut materials such as stainless steel or mild steel, the l Even when the-(Ti, V) CN layer is used in a thick state, the 1- (Ti, V) CN layer itself has excellent heat-resistant plastic deformation as described above, and a hard coating layer is also used. The constituting Al 2 O 3 layer is also excellent in heat-resistant plastic deformability, while the TiC · N · O layer does not have sufficient heat-resistant plastic deformability, but the l- (Ti, V) CN layer and Compared to the Al 2 O 3 layer, the layer thickness is relatively very thin, so there is almost no effect on the thermoplastic deformation of the hard coating layer. As a result, there is no occurrence of uneven wear on the cutting edge surface. The blade surface exhibits excellent cutting performance over a long period of time while maintaining normal wear. thing.
The research results shown in (a) to (c) above were obtained.
[0009]
The present invention has been made based on the above research results, and on the surface of a substrate made of a WC-based cemented carbide or TiCN-based cermet,
(A) As a lower layer, one or more of TiC / N / O layers composed of a TiC layer, a TiN layer, a TiCN layer, a TiCO layer, and a TiCNO layer, and V occupies the total amount of Ti 1- (Ti, V) CN layer containing 1 to 30 atomic% in proportion,
(B) As an upper layer, an Al 2 O 3 layer,
The hard coating layer formed by the above (a) and (b) is chemically vapor-deposited with an average layer thickness of 5 to 30 μm, and the hard coating layer has excellent heat-resistant plastic deformability by high-speed cutting of difficult-to-cut materials. It is characterized by the coated cutting tip to be exhibited.
[0010]
In the coated cutting tip of the present invention, the content ratio of V in the 1- (Ti, V) CN layer constituting the hard coating layer is set to 1 to 30 atomic% in the ratio to the total amount with the Ti component. When the proportion is less than 1 atomic%, the desired improvement effect on the heat-resistant plastic deformation caused by the V component cannot be obtained. On the other hand, when the proportion exceeds 30 atomic%, excellent toughness caused by the vertically grown crystal structure is obtained. For this reason, a decreasing tendency appears, and the content ratio is desirably 3 to 15 atomic%.
Also, the reason why the average thickness of the hard coating layer is 5 to 30 μm is that if the layer thickness is 5 μm, the desired excellent wear resistance cannot be secured, while if the layer thickness exceeds 30 μm, This is because chipping and chipping are likely to occur in the blade.
[0011]
DETAILED DESCRIPTION OF THE INVENTION
Next, the coated cutting tip of the present invention will be specifically described with reference to examples.
As raw material powders, WC powder, TiC powder, VC powder, TaC powder, NbC powder, Cr 3 C 2 powder, and Co powder, all having an average particle diameter of 1 to 3 μm, were prepared. And then wet-mixed with a ball mill for 72 hours, dried, and pressed into a green compact at a pressure of 120 MPa. The green compact was vacuumed at 6 Pa at a temperature of 1410 ° C. for 1 hour. Vacuum-sintered under the holding conditions, and after sintering, the cutting edge portion is subjected to a honing process of R: 0.05 mm to have a chip shape of ISO standard / CNMG120408 and made of WC-based cemented carbide A -1, A-5, A-6, A-8 were formed.
[0012]
In addition, as raw material powders, TiCN (mass ratio TiC / TiN = 50/50) powder, Mo 2 C powder, NbC powder, TaC powder, WC powder, Co powder, all having an average particle diameter of 0.5 to 2 μm. , And Ni powder, these raw material powders are blended in the blending composition shown in Table 2, wet mixed with a ball mill for 24 hours, dried, and then pressed into a compact at a pressure of 100 MPa. The powder was sintered in a nitrogen atmosphere of 1.3 kPa at a temperature of 1500 ° C. for 1 hour, and after sintering, the cutting edge portion was subjected to a honing process of R: 0.03 mm to comply with ISO standard / CNMG120212. Substrates B-1, B-2 to B-4, and B-6 having a chip shape and composed of TiCN-based cermets were formed.
[0013]
Next, a normal chemical vapor deposition apparatus was used on the surfaces of these substrates A-1, A-5, A-6, A-8 and B-1, B-2 to B-4, B-6. Tables 5 and 6 show hard coating layers comprising TiC / N / O layers and Al 2 O 3 layers, and 1- (Ti, V) CN layers or l-TiCN layers under the conditions shown in 3 and 4. The present invention coated cutting tips 1 to 8 and the conventional coated cutting tips 1 to 8 were produced respectively by forming the target layer thickness and the combination.
[0014]
As a result of measuring the content ratio of the V component in the 1- (Ti, V) CN layer constituting the hard coating layer of the coated cutting chips 1 to 8 of the present invention as a result of the measurement using an Auger spectroscopic analyzer, the target content ratio is obtained. The thicknesses of the constituent layers of the hard coating layers of the present coated cutting chips 1 to 8 and the conventional coated cutting chips 1 to 8 were each measured by cross-section using a scanning electron microscope. However, all showed the average layer thickness (average value of five-point measurement) substantially the same as the target layer thickness.
[0015]
Next, for the above-described coated cutting chips 1-8 of the present invention and the conventional coated cutting chips 1-8, in a state where this is screwed to the tip of the tool steel tool with a fixing jig,
Work material: JIS / SUS304 round bar,
Cutting speed: 220 m / min,
Cutting depth: 2mm,
Feed: 0.25mm / rev,
Cutting time: 10 minutes,
Dry high-speed continuous turning test of stainless steel 1 under the conditions of
Work material: JIS / S15C round bar,
Cutting speed: 450 m / min,
Cutting depth: 2mm,
Feed: 0.25mm / rev,
Cutting time: 10 minutes,
Dry high-speed continuous turning test of mild steel 1 under the conditions of
Work material: JIS / SUS304 lengthwise equidistant four round grooved round bars,
Cutting speed: 200 m / min,
Cutting depth: 2mm,
Feed: 0.2mm / rev,
Cutting time: 5 minutes
Dry high-speed intermittent turning test of stainless steel 2 under the conditions of
Work material: JIS / S15C lengthwise equal length 4 vertical grooved round bars,
Cutting speed: 300 m / min,
Incision: 1.5mm,
Feed: 0.5mm / rev,
Cutting time: 5 minutes
The dry high-speed intermittent turning test of mild steel 2 under the conditions described above was performed, and the maximum flank wear width of the cutting edge was measured in any turning test. The measurement results are shown in Table 7.
[0016]
[Table 1]
[Table 2]
[Table 3]
[Table 4]
[Table 5]
[Table 6]
[Table 7]
【The invention's effect】
From the results shown in Tables 5 to 7, the present coated cutting tips 1 to 8 having the l- (Ti, V) CN layer as a constituent layer of the hard coating layer instead of the l-TiCN layer are all the above-mentioned l. -Since the (Ti, V) CN layer has excellent heat-resistant plastic deformability, even if cutting of stainless steel or mild steel is performed at high speed with high heat generation, the plastic deformation of the hard coating layer is suppressed. As a result, the wear of the cutting edge portion is normal wear, and excellent wear resistance is exhibited over a long period of time, whereas the conventional coated cutting tips 1 to 8 having the l-TiCN layer as the constituent layers are all l It is clear that the TiCN layer undergoes plastic deformation due to high heat generation during cutting, resulting in uneven wear at the cutting edge, which significantly accelerates the progress of wear.
As described above, the coated cutting tip according to the present invention is excellent in cutting not only under normal conditions such as various types of steel and cast iron, but also particularly in high-speed cutting of difficult-to-cut materials such as stainless steel and mild steel. Since it exhibits performance and exhibits versatile cutting performance, it can sufficiently satisfy the labor saving and energy saving of cutting work and further cost reduction.
Claims (1)
（ａ）下部層として、いずれも粒状結晶組織を有する、Ｔｉの炭化物層、窒化物層、炭窒化物層、炭酸化物層、および炭窒酸化物層からなるＴｉ炭・窒・酸化物層のうちの１層または２層以上と、縦長成長結晶組織を有し、かつＶをＴｉとの合量に占める割合で１〜３０原子％含有するＴｉとＶの複合炭窒化物層、
（ｂ）上部層として、粒状結晶組織を有する酸化アルミニウム層、
以上（ａ）および（ｂ）で構成された硬質被覆層を５〜３０μｍの平均層厚で化学蒸着してなる、硬質被覆層が難削材の高速切削加工ですぐれた耐熱塑性変形性を発揮する表面被覆切削チップ。On the surface of the substrate made of tungsten carbide based cemented carbide or titanium carbonitride based cermet,
(A) Ti carbon / nitrogen / oxide layer comprising a Ti carbide layer, nitride layer, carbonitride layer, carbonate layer, and carbonitride oxide layer, each having a granular crystal structure, as the lower layer Ti and V composite carbonitride layers having one or two or more of them, having a vertically grown crystal structure, and containing 1 to 30 atomic% of V in the total amount with Ti,
(B) As an upper layer, an aluminum oxide layer having a granular crystal structure,
The hard coating layer composed of the above (a) and (b) is chemically vapor-deposited with an average layer thickness of 5 to 30 μm, and the hard coating layer exhibits excellent heat-resistant plastic deformation by high-speed cutting of difficult-to-cut materials. Surface coated cutting tip to be used .
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Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US7766091B2 (en) | 1998-05-15 | 2010-08-03 | Tyco Fire Products Lp | Early suppression fast response fire protection sprinkler |
| US9142389B2 (en) | 2010-12-23 | 2015-09-22 | Element Six Technologies Limited | Microwave power delivery system for plasma reactors |
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| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP4518258B2 (en) * | 2004-08-11 | 2010-08-04 | 三菱マテリアル株式会社 | A surface-coated cermet cutting tool that exhibits excellent chipping resistance with a hard coating layer in high-speed intermittent cutting |
| RU2747054C1 (en) * | 2020-09-12 | 2021-04-23 | Общество с ограниченной ответственностью "Вириал" (ООО "Вириал") | Multilayer carbide plate and method for its production (options) |
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Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US7766091B2 (en) | 1998-05-15 | 2010-08-03 | Tyco Fire Products Lp | Early suppression fast response fire protection sprinkler |
| US8176988B2 (en) | 1998-05-15 | 2012-05-15 | Tyco Fire Products Lp | Early suppression fast response fire protection sprinkler |
| US9142389B2 (en) | 2010-12-23 | 2015-09-22 | Element Six Technologies Limited | Microwave power delivery system for plasma reactors |
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