JP5644388B2 - Cermet and coated cermet - Google Patents
Cermet and coated cermet Download PDFInfo
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- JP5644388B2 JP5644388B2 JP2010249267A JP2010249267A JP5644388B2 JP 5644388 B2 JP5644388 B2 JP 5644388B2 JP 2010249267 A JP2010249267 A JP 2010249267A JP 2010249267 A JP2010249267 A JP 2010249267A JP 5644388 B2 JP5644388 B2 JP 5644388B2
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本発明は、サーメットおよび被覆サーメットに関するものである。 The present invention relates to a cermet and a coated cermet.
サーメットの従来技術として、サーメット表面部の硬度を高めて耐摩耗性を向上させたサーメットがある（例えば、特許文献１参照。）。 As a conventional cermet technology, there is a cermet in which the hardness of the cermet surface portion is increased to improve the wear resistance (see, for example, Patent Document 1).
しかしながら、上記特許文献１の発明では、耐欠損性が不十分であり、切削工具として用いると工具寿命が短いという問題があった。本発明は、上記問題を解決するためになされたもので、耐欠損性を高め、切削工具として用いると従来よりも切削工具の寿命を長くすることができるサーメットを提供することを目的とする。 However, the invention of the above-mentioned Patent Document 1 has a problem that the fracture resistance is insufficient and the tool life is short when used as a cutting tool. The present invention has been made to solve the above-described problems, and an object of the present invention is to provide a cermet that can improve fracture resistance and can prolong the life of a cutting tool as compared with the prior art when used as a cutting tool.
本発明は上記の課題を解決するためになされ、その要旨は次のとおりである。
（１）表面から内部に向って２〜２００μｍの厚さで、板状炭化タングステンを主成分とする炭化タングステン相と、鉄族金属を主成分とする結合相とからなる表面領域が形成され、表面領域よりも内部に、粒状炭化タングステンを主成分とする炭化タングステン相と、Ｔｉ、Ｗの炭化物、窒化物、炭窒化物およびこれらの相互固溶体の中から選ばれた少なくとも１種からなる硬質相と、鉄族金属を主成分とする結合相とからなる内部領域が形成されたサーメット。
（２）硬質相がコアとリムからなる有芯構造のコアリム相を含む硬質相である（１）に記載のサーメット。
（３）表面領域の断面組織における、炭化タングステン相の面積率は７５〜９９面積％、結合相の面積率は１〜２５面積％、これらの合計は１００面積％であり、内部領域の断面組織における、炭化タングステン相の面積率は１０〜９０面積％、硬質相の面積率は５〜７５面積％、結合相の面積率は５〜２５面積％、これらの合計は１００面積％である（１）または（２）に記載のサーメット。
（４）表面領域と内部領域の間に、表面領域の直下から内部に向って２〜５００μｍの厚さがあり、炭化タングステン相と硬質相と結合相とからなり、サーメットの断面組織における、硬質相のコアリム相のリムの面積率が内部領域にある硬質相のコアリム相のリムの面積率よりも増加し、硬質相のコアリム相のコアの面積率が内部領域にある硬質相のコアリム相のコアの面積率よりも減少し、炭化タングステン相の面積率が内部領域にある炭化タングステン相の面積率よりも減少した中間領域が形成された（２）または（３）に記載のサーメット。
（５）中間領域の断面組織における、炭化タングステン相の面積率は０〜８０面積％、硬質相の面積率は２０〜８０面積％、結合相の面積率は０〜１５面積％、これらの合計は１００面積％である（１）〜（４）のいずれかに記載のサーメット。
（６）サーメットの表面からＸ線回折測定したときのＷＣ（００１）面のピーク強度ｈ（００１）とＷＣ（１００）面のピーク強度ｈ（１００）は、（ｈ（００１）／ｈ（１００））≧０．６を満足し、サーメットの内部領域をＸ線回折測定したときのＷＣ（００１）面のピーク強度ｈ（００１）とＷＣ（１００）面のピーク強度ｈ（１００）は（ｈ（００１）／ｈ（１００））＜０．６を満足する（１）〜（５）のいずれかに記載のサーメット。
（７）炭化タングステンの最長辺に平行な直線で炭化タングステンを横切る直線の最大長さをＡ（μｍ）と表し、炭化タングステンの最長辺に垂直な直線で炭化タングステンを横切る直線の最大長さをＢ（μｍ）と表したとき、Ｂに対するＡの比（Ａ／Ｂ）が２以上であり、かつ、ＡとＢとを乗じた値Ｃ（Ｃ＝Ａ×Ｂ）が２×１０-12ｍ2以上である炭化タングステンが表面領域に含まれる（１）〜（６）のいずれかに記載のサーメット。
（８）（１）〜（７）のいずれかに記載のサーメットの表面に、Ｔｉ、Ｚｒ、Ｈｆ、Ｖ、Ｎｂ、Ｔａ、Ｃｒ、Ｍｏ、Ｗ、Ａｌ、Ｓｉの金属、炭化物、窒化物、酸化物およびこれらの相互固溶体の中から選ばれた少なくとも１種の被膜を被覆した被覆サーメット。
The present invention has been made to solve the above problems, and the gist thereof is as follows.
(1) A surface region composed of a tungsten carbide phase mainly composed of plate-like tungsten carbide and a binder phase mainly composed of an iron group metal is formed with a thickness of 2 to 200 μm from the surface toward the inside. A hard phase comprising at least one selected from a tungsten carbide phase mainly composed of granular tungsten carbide and Ti, W carbides, nitrides, carbonitrides, and their mutual solid solutions inside the surface region. And a cermet having an internal region composed of a binder phase mainly composed of an iron group metal.
(2) The cermet according to (1), wherein the hard phase is a hard phase including a core rim phase having a core structure composed of a core and a rim.
(3) In the cross-sectional structure of the surface region, the area ratio of the tungsten carbide phase is 75 to 99 area%, the area ratio of the binder phase is 1 to 25 area%, and the total of these is 100 area%. The area ratio of the tungsten carbide phase is 10 to 90 area%, the area ratio of the hard phase is 5 to 75 area%, the area ratio of the binder phase is 5 to 25 area%, and the total of these is 100 area% (1 ) Or cermet according to (2).
(4) Between the surface region and the internal region, there is a thickness of 2 to 500 μm from directly under the surface region to the inside, and it consists of a tungsten carbide phase, a hard phase, and a binder phase, and is hard in the cross-sectional structure of the cermet. The area ratio of the rim of the core rim phase of the phase is greater than the area ratio of the rim of the core rim phase of the hard phase in the inner area, and the area ratio of the core of the hard rim phase of the hard phase in the inner area is The cermet according to (2) or (3), wherein an intermediate region is formed in which the area ratio of the tungsten carbide phase is smaller than the area ratio of the tungsten carbide phase in the inner region.
(5) In the cross-sectional structure of the intermediate region, the area ratio of the tungsten carbide phase is 0 to 80 area%, the area ratio of the hard phase is 20 to 80 area%, the area ratio of the binder phase is 0 to 15 area%, and the total of these Is 100 area%, The cermet in any one of (1)-(4).
(6) The peak intensity h (001) of the WC (001) plane and the peak intensity h (100) of the WC (100) plane when X-ray diffraction measurement is performed from the surface of the cermet are (h (001) / h (100 )) ≧ 0.6, and the peak intensity h (001) of the WC (001) plane and the peak intensity h (100) of the WC (100) plane when the internal region of the cermet is measured by X-ray diffraction are (h) The cermet according to any one of (1) to (5), which satisfies (001) / h (100)) <0.6.
(7) A (μm) represents the maximum length of a straight line that crosses tungsten carbide on a straight line parallel to the longest side of tungsten carbide, and the maximum length of a straight line that crosses tungsten carbide on a straight line perpendicular to the longest side of tungsten carbide. When expressed as B (μm), the ratio of A to B (A / B) is 2 or more, and the value C (C = A × B) obtained by multiplying A and B is 2 × 10 −12 m The cermet according to any one of (1) to (6), wherein tungsten carbide that is 2 or more is contained in the surface region.
(8) On the surface of the cermet according to any one of (1) to (7), Ti, Zr, Hf, V, Nb, Ta, Cr, Mo, W, Al, Si metal, carbide, nitride, A coated cermet coated with at least one film selected from oxides and their mutual solid solutions.
本発明のサーメットは、サーメットの表面側に形成された表面領域と、その表面領域よりも内部に形成された内部領域とを含む。本発明のサーメットは、表面領域と内部領域との間に中間領域が形成されてもよい。 The cermet of the present invention includes a surface region formed on the surface side of the cermet and an internal region formed inside the surface region. In the cermet of the present invention, an intermediate region may be formed between the surface region and the internal region.
本発明の内部領域は、粒状炭化タングステンを主成分とする炭化タングステン相と、Ｔｉ、Ｗの炭化物、窒化物、炭窒化物およびこれらの相互固溶体の中から選ばれた少なくとも１種からなる硬質相と、鉄族金属を主成分とする結合相とからなる。 The internal region of the present invention includes a hard phase comprising at least one selected from a tungsten carbide phase mainly composed of granular tungsten carbide, and Ti, W carbide, nitride, carbonitride, and their mutual solid solutions. And a binder phase mainly composed of an iron group metal.
本発明において粒状炭化タングステンとは、断面組織における、炭化タングステンの最長辺に平行な直線で炭化タングステンを横切る直線の最大長さをＡ（μｍ）と表し、炭化タングステン相の最長辺に垂直な直線で炭化タングステン相を横切る直線の最大長さをＢ（μｍ）と表したとき、Ｂに対するＡの比（Ａ／Ｂ）が２未満の炭化タングステンを意味する。なお、本発明において、粒状炭化タングステンを主成分とする炭化タングステン相とは、断面組織において、炭化タングステン全体の面積に対する粒状炭化タングステンの面積の割合が５１面積％以上である炭化タングステン相を意味する。 In the present invention, granular tungsten carbide refers to the maximum length of a straight line that crosses tungsten carbide in a cross-sectional structure parallel to the longest side of tungsten carbide as A (μm), and is a straight line perpendicular to the longest side of the tungsten carbide phase. When the maximum length of the straight line crossing the tungsten carbide phase is represented by B (μm), it means tungsten carbide having a ratio of A to B (A / B) of less than 2. In the present invention, the tungsten carbide phase mainly composed of granular tungsten carbide means a tungsten carbide phase in which the ratio of the area of the granular tungsten carbide to the area of the entire tungsten carbide is 51 area% or more in the cross-sectional structure. .
本発明の硬質相は、Ｔｉ、Ｗの炭化物、窒化物、炭窒化物およびこれらの相互固溶体の中から選ばれた少なくとも１種からなる。具体的には、ＴｉＣ、ＴｉＮ、ＴｉＣＮ、（ＴｉＷ）Ｃ、（ＴｉＷ）Ｎ、（ＴｉＷ）ＣＮなどを挙げることができる。硬質相は、ＴｉＣ、ＴｉＮ、ＴｉＣＮ、（ＴｉＷ）Ｃ、（ＴｉＷ）Ｎ、（ＴｉＷ）ＣＮなどの単一相のみからなる場合よりも、ＴｉＣ、ＴｉＮ、ＴｉＣＮなどのコアと（ＴｉＷ）Ｃ、（ＴｉＷ）Ｎ、（ＴｉＷ）ＣＮなどのリムとから構成された有芯構造のコアリム相を含むと、耐摩耗性および耐欠損性が向上するため、さらに好ましい。 The hard phase of the present invention comprises at least one selected from Ti, W carbides, nitrides, carbonitrides, and their mutual solid solutions. Specific examples include TiC, TiN, TiCN, (TiW) C, (TiW) N, and (TiW) CN. The hard phase has a core such as TiC, TiN, TiCN and (TiW) C, rather than a single phase such as TiC, TiN, TiCN, (TiW) C, (TiW) N, (TiW) CN, etc. It is more preferable to include a core rim phase having a core structure composed of rims such as (TiW) N and (TiW) CN, since the wear resistance and fracture resistance are improved.
本発明において鉄族金属を主成分とする結合相とは、Ｃｏ、ＮｉおよびＦｅの少なくとも１種、または、Ｃｏ、ＮｉおよびＦｅの少なくとも１種にＴｉおよびＷの少なくとも１種を３０質量％未満固溶させたものである。その中でも、ＣｏおよびＮｉの１種または２種を主成分とする結合相であると、機械的強度が向上するのでさらに好ましく、その中でもＣｏを主成分とする結合相であると、サーメットと被膜との密着性が向上するのでさらに好ましい。 In the present invention, the binder phase containing iron group metal as the main component is less than 30% by mass of at least one of Co, Ni and Fe, or at least one of Ti and W in at least one of Co, Ni and Fe. It is a solid solution. Among them, a binder phase mainly composed of one or two of Co and Ni is more preferable because mechanical strength is improved, and among them, a cermet and a coating are preferably bonded phases mainly composed of Co. This is more preferable because the adhesion to the surface is improved.
本発明の表面領域は、表面から内部に向って２〜２００μｍの厚さがあり、板状炭化タングステンを主成分とする炭化タングステン相と、鉄族金属を主成分とする結合相とからなる。 The surface region of the present invention has a thickness of 2 to 200 μm from the surface to the inside, and is composed of a tungsten carbide phase mainly composed of plate-like tungsten carbide and a binder phase mainly composed of an iron group metal.
本発明において板状炭化タングステンとは、断面組織における、炭化タングステンの最長辺に平行な直線で炭化タングステンを横切る直線の最大長さをＡ（μｍ）と表し、炭化タングステン相の最長辺に垂直な直線で炭化タングステン相を横切る直線の最大長さをＢ（μｍ）と表したとき、Ｂに対するＡの比（Ａ／Ｂ）が２以上の炭化タングステンを意味する。なお、本発明において板状炭化タングステンを主成分とする炭化タングステン相とは、断面組織において、炭化タングステン全体の面積に対する板状炭化タングステンの面積の割合が５１面積％以上である炭化タングステン相を意味する。具体的には、炭化タングステンのＡとＢは、断面組織を走査型電子顕微鏡で３０００倍に拡大し、３４μｍ×２４μｍの長方形の断面組織写真から測定することができる。 In the present invention, plate-like tungsten carbide is represented by A (μm) as the maximum length of a straight line parallel to the longest side of tungsten carbide in the cross-sectional structure, and perpendicular to the longest side of the tungsten carbide phase. When the maximum length of a straight line that crosses the tungsten carbide phase in a straight line is expressed as B (μm), it means tungsten carbide having a ratio of A to B (A / B) of 2 or more. In the present invention, the tungsten carbide phase mainly composed of plate-like tungsten carbide means a tungsten carbide phase in which the ratio of the area of the plate-like tungsten carbide to the area of the entire tungsten carbide is 51 area% or more in the cross-sectional structure. To do. Specifically, tungsten carbides A and B can be measured from a 34 μm × 24 μm rectangular cross-sectional structure photograph by magnifying the cross-sectional structure 3000 times with a scanning electron microscope.
本発明の表面領域の厚さが２μｍ未満になると、サーメットの耐欠損性を高める効果が十分に得られず、本発明の表面領域の厚さが２００μｍを超えて厚くなるとサーメットの耐摩耗性が低下するので、本発明の表面領域の厚さを２〜２００μｍの範囲とした。 When the thickness of the surface region of the present invention is less than 2 μm, the effect of increasing the fracture resistance of the cermet is not sufficiently obtained, and when the thickness of the surface region of the present invention exceeds 200 μm, the wear resistance of the cermet is reduced. Therefore, the thickness of the surface region of the present invention is set in the range of 2 to 200 μm.
本発明の表面領域の断面組織における、炭化タングステン相の面積率は７５〜９９面積％、結合相の面積率は１〜２５面積％であって、これらの合計は１００面積％であり、内部領域の断面組織における、炭化タングステン相の面積率は１０〜９０面積％、硬質相の面積率は５〜７５面積％、結合相の面積率は５〜２５面積％であって、これらの合計は１００面積％であると好ましい。これは、表面領域の断面組織における、炭化タングステン相の面積率が７５面積％未満になり結合相の面積率が２５面積％を超えて多くなるとサーメットの耐摩耗性が低下し、炭化タングステン相の面積率が９９面積％を超えて多くなり結合相の面積率が１面積％未満になると耐欠損性が低下するためである。また、内部領域の断面組織における、炭化タングステン相の面積率が１０面積％未満になると耐欠損性が低下し、炭化タングステン相の面積率が９０面積％を超えて多くなると耐摩耗性が低下し、硬質相の面積率が５面積％未満になると耐摩耗性が低下し、硬質相の面積率が７５面積％を超えて多くなると耐欠損性が低下し、結合相の面積率が５面積％未満になると耐欠損性が低下し、結合相の面積率が２５面積％を超えて多くなると耐摩耗性が低下するためである。 In the cross-sectional structure of the surface region of the present invention, the area ratio of the tungsten carbide phase is 75 to 99 area%, the area ratio of the binder phase is 1 to 25 area%, and the total of these is 100 area%, In the cross-sectional structure, the area ratio of the tungsten carbide phase is 10 to 90 area%, the area ratio of the hard phase is 5 to 75 area%, and the area ratio of the binder phase is 5 to 25 area%. Area% is preferred. This is because, when the area ratio of the tungsten carbide phase in the cross-sectional structure of the surface region is less than 75 area% and the area ratio of the binder phase is more than 25 area%, the wear resistance of the cermet decreases, and the tungsten carbide phase This is because if the area ratio exceeds 99 area% and the area ratio of the binder phase is less than 1 area%, the chipping resistance decreases. In addition, when the area ratio of the tungsten carbide phase in the cross-sectional structure of the internal region is less than 10 area%, the chipping resistance decreases, and when the area ratio of the tungsten carbide phase exceeds 90 area%, the wear resistance decreases. When the area ratio of the hard phase is less than 5% by area, the wear resistance decreases, and when the area ratio of the hard phase exceeds 75% by area, the chipping resistance decreases and the area ratio of the binder phase is 5% by area. This is because the chipping resistance decreases when the ratio is less than 1, and the wear resistance decreases when the area ratio of the binder phase exceeds 25 area%.
本発明のサーメットにおいて、表面領域と内部領域の間に、表面領域の直下から内部に向って２〜５００μｍの厚さがあり、炭化タングステン相と硬質相と結合相とからなり、サーメットの断面組織における、硬質相のコアリム相のリムの面積率が内部領域にある硬質相のリムの面積率よりも増加し、硬質相のコアリム相のコアの面積率が内部領域にある硬質相のコアリム相のコアの面積率よりも減少し、炭化タングステン相の面積率が内部領域にある炭化タングステン相の面積率よりも減少した中間領域が形成されると、耐摩耗性が向上するので、さらに好ましい。中間領域の厚さが２μｍ以上になるとさらに耐摩耗性を向上させる効果が得られるが、中間領域の厚さが５００μｍを超えて厚くなると耐欠損性が低下する傾向を示す。 In the cermet of the present invention, between the surface region and the internal region, there is a thickness of 2 to 500 μm from directly below the surface region to the inside, and it comprises a tungsten carbide phase, a hard phase, and a binder phase, and the cermet cross-sectional structure The area ratio of the rim of the core rim phase of the hard phase is larger than the area ratio of the rim of the hard phase in the inner region, and the area ratio of the core of the hard phase rim phase of the hard phase in the inner region is It is more preferable that an intermediate region is formed in which the area ratio of the tungsten carbide phase is smaller than the area ratio of the tungsten carbide phase in the inner region because the wear resistance is improved. When the thickness of the intermediate region is 2 μm or more, an effect of further improving the wear resistance can be obtained. However, when the thickness of the intermediate region exceeds 500 μm, the fracture resistance tends to decrease.
本発明の中間領域の断面組織における、炭化タングステン相の面積率は０〜８０面積％、硬質相の面積率は２０〜１００面積％、結合相の面積率は０〜１５面積％であり、これらの合計は１００面積％であると耐摩耗性が向上するので、さらに好ましい。これは、中間領域の断面組織における、炭化タングステン相の面積率は８０面積％が超えて多くなると耐摩耗性が低下し、硬質相の面積率が２０面積％未満になると耐摩耗性が低下し、結合相の面積率が１５面積％を超えて多くなると耐摩耗性が低下するためである。 In the cross-sectional structure of the intermediate region of the present invention, the area ratio of the tungsten carbide phase is 0 to 80 area%, the area ratio of the hard phase is 20 to 100 area%, and the area ratio of the binder phase is 0 to 15 area%. The total of 100% by area is more preferable because the wear resistance is improved. This is because, when the area ratio of the tungsten carbide phase in the cross-sectional structure of the intermediate region exceeds 80 area%, the wear resistance decreases, and when the hard phase area ratio is less than 20 area%, the wear resistance decreases. This is because the wear resistance decreases when the area ratio of the binder phase exceeds 15 area%.
本発明のサーメットの表面をＸ線回折測定したときのＷＣ（００１）面のピーク強度ｈ（００１）とＷＣ（１００）面のピーク強度ｈ（１００）は、（ｈ（００１）／ｈ（１００））≧０．６を満足し、本発明のサーメットの内部領域をＸ線回折測定したときのＷＣ（００１）面のピーク強度ｈ（００１）とＷＣ（１００）面のピーク強度ｈ（１００）は（ｈ（００１）／ｈ（１００））＜０．６を満足すると、耐欠損性が向上するので、さらに好ましい。本発明の表面領域に多く含まれる板状炭化タングステンは、（００１）面が優先的に成長したもので、表面領域の（ｈ（００１）／ｈ（１００））の比は、粒状炭化タングステンを多く含む内部領域の（ｈ（００１）／ｈ（１００））の比よりも高くなる。具体的には、サーメットの表面にＣｕ−Ｋα線を照射して、２θ／θ法により表面をＸ線回折測定したときのＷＣ（００１）面のピーク強度ｈ（００１）およびＷＣ（１００）面のピーク強度ｈ（１００）を測定して、表面領域の（ｈ（００１）／ｈ（１００））の比を求めることができる。また、表面領域および中間領域を研削や鏡面研磨などで除去して得られた内部領域にＣｕ−Ｋα線を照射して、２θ／θ法により内部領域をＸ線回折測定したときのＷＣ（００１）面のピーク強度ｈ（００１）およびＷＣ（１００）面のピーク強度ｈ（１００）を測定して、内部領域の（ｈ（００１）／ｈ（１００））の比を求めることができる。 The peak intensity h (001) of the WC (001) plane and the peak intensity h (100) of the WC (100) plane when the surface of the cermet of the present invention is measured by X-ray diffraction are (h (001) / h (100 )) ≧ 0.6, and the peak intensity h (001) of the WC (001) plane and the peak intensity h (100) of the WC (100) plane when the internal region of the cermet of the present invention is measured by X-ray diffraction. If (h (001) / h (100)) <0.6 is satisfied, the fracture resistance is improved, which is more preferable. The plate-like tungsten carbide contained in a large amount in the surface region of the present invention has a (001) plane preferentially grown, and the ratio of (h (001) / h (100)) in the surface region is that of granular tungsten carbide. The ratio is higher than the ratio (h (001) / h (100)) of the inner region including a large amount. Specifically, the peak intensity h (001) and WC (100) plane of the WC (001) plane when the surface of the cermet is irradiated with Cu-Kα rays and the surface is subjected to X-ray diffraction measurement by the 2θ / θ method. The peak intensity h (100) can be measured to determine the ratio (h (001) / h (100)) of the surface region. Further, when the inner region obtained by removing the surface region and the intermediate region by grinding or mirror polishing is irradiated with Cu-Kα rays and the inner region is subjected to X-ray diffraction measurement by the 2θ / θ method, WC (001 ) Plane peak intensity h (001) and WC (100) plane peak intensity h (100) can be measured to determine the ratio of (h (001) / h (100)) in the internal region.
炭化タングステンの最長辺に平行な直線で炭化タングステンを横切る直線の最大長さをＡ（μｍ）と表し、炭化タングステンの最長辺に垂直な直線で炭化タングステンを横切る直線の最大長さをＢ（μｍ）と表したとき、Ｂに対するＡの比（Ａ／Ｂ）が２以上であり、かつ、ＡとＢとを乗じた値Ｃ（Ｃ＝Ａ×Ｂ）が２×１０-12ｍ2以上である炭化タングステンが表面領域に含まれると、耐欠損性が向上するので、さらに好ましい。 The maximum length of a straight line that crosses tungsten carbide on a straight line parallel to the longest side of tungsten carbide is represented by A (μm), and the maximum length of a straight line that intersects tungsten carbide on a straight line perpendicular to the longest side of tungsten carbide is B (μm). ), The ratio of A to B (A / B) is 2 or more, and the value C (C = A × B) obtained by multiplying A and B is 2 × 10 −12 m 2 or more. It is more preferable that certain tungsten carbide is included in the surface region since the fracture resistance is improved.
本発明のサーメットの表面に、ＰＶＤ法やＣＶＤ法によりＴｉ、Ｚｒ、Ｈｆ、Ｖ、Ｎｂ、Ｔａ、Ｃｒ、Ｍｏ、Ｗ、Ａｌ、Ｓｉの金属、炭化物、窒化物、酸化物およびこれらの相互固溶体の中から選ばれた少なくとも１種の被膜を被覆した被覆サーメットは耐摩耗性に優れる。本発明の被膜としては、具体的に、ＴｉＮ、ＴｉＣ、ＴｉＣＮ、ＴｉＣＮＯ、ＴｉＡｌＮ、ＴｉＳｉＮ、ＡｌＣｒＮ、Ａｌ2Ｏ3などを挙げることができる。被膜の総膜厚の平均値は０．１μｍ以上になると耐摩耗性が向上し、３０μｍを超えて厚くなると耐欠損性が低下する傾向が見られるので、０．１〜３０μｍが好ましい。 On the surface of the cermet of the present invention, Ti, Zr, Hf, V, Nb, Ta, Cr, Mo, W, Al, Si metal, carbide, nitride, oxide, and their mutual solid solutions are obtained by PVD or CVD. A coated cermet coated with at least one film selected from among the above is excellent in wear resistance. Specific examples of the coating of the present invention include TiN, TiC, TiCN, TiCNO, TiAlN, TiSiN, AlCrN, and Al 2 O 3 . When the average value of the total thickness of the coating is 0.1 μm or more, the wear resistance is improved, and when the thickness exceeds 30 μm, the chipping resistance tends to decrease. Therefore, 0.1 to 30 μm is preferable.
本発明のサーメットを製造する方法としては、
（Ａ）ＴｉＮ、ＴｉＣＮ、金属元素がＴｉおよびＷである炭化物、窒化物、炭窒化物およびこれらの相互固溶体の中の少なくとも１種：５０〜８０体積％と、ＷＣ：１５〜３０体積％と、鉄族金属：５〜２０体積％とからなり合計で１００体積％となる混合物を準備する混合工程と、
（Ｂ）混合物を非酸化雰囲気中で常温から１１５０〜１３５０℃の第１加熱温度まで昇温させる第１昇温工程と、
（Ｃ）混合物を窒素雰囲気中で１１５０〜１３５０℃の第１加熱温度から１４５０〜１６５０℃の第２加熱温度まで圧力２ｋＰａ以上の窒素雰囲気中で昇温させる第２昇温工程と、
（Ｄ）混合物を１４５０〜１６５０℃の第２加熱温度にて第２昇温工程よりも低い圧力の窒素雰囲気中または真空中で保持する保持工程と、
（Ｅ）混合物を１４５０〜１６５０℃の第２加熱温度から１０００〜１３００℃の第１冷却温度まで保持工程よりも低い圧力の窒素雰囲気中または真空中で冷却する第１冷却工程と、
（Ｆ）混合物を１０００〜１３００℃の第１冷却温度から常温に冷却する第２冷却工程と
を含むサーメットの製造方法により得ることができる。
As a method for producing the cermet of the present invention,
(A) TiN, TiCN, at least one of carbides, nitrides, carbonitrides and their mutual solid solutions whose metal elements are Ti and W: 50 to 80% by volume; WC: 15 to 30% by volume A mixing step of preparing a mixture of iron group metal: 5 to 20% by volume and totaling 100% by volume;
(B) a first temperature raising step for raising the temperature of the mixture from normal temperature to a first heating temperature of 1150 to 1350 ° C. in a non-oxidizing atmosphere;
(C) a second heating step in which the mixture is heated in a nitrogen atmosphere at a pressure of 2 kPa or more from a first heating temperature of 1150 to 1350 ° C. to a second heating temperature of 1450 to 1650 ° C. in a nitrogen atmosphere;
(D) a holding step of holding the mixture at a second heating temperature of 1450 to 1650 ° C. in a nitrogen atmosphere or a vacuum at a pressure lower than that of the second heating step;
(E) a first cooling step of cooling the mixture from a second heating temperature of 1450 to 1650 ° C. to a first cooling temperature of 1000 to 1300 ° C. in a nitrogen atmosphere or a vacuum lower than the holding step;
(F) It can obtain by the manufacturing method of a cermet including the 2nd cooling process which cools a mixture from 1st cooling temperature of 1000-1300 degreeC to normal temperature.
第１昇温工程において、混合物を非酸化雰囲気中で昇温させることにより混合物の酸化を防いでいる。非酸化雰囲気として具体的には、真空、窒素雰囲気、不活性雰囲気、水素雰囲気などを挙げることができる。第２昇温工程における窒素雰囲気の圧力は２ｋＰａ以上であるが、窒素雰囲気の圧力が１００ｋＰａを超えて高くなるとサーメットの焼結性が低下する傾向を示すので、第２昇温工程における窒素雰囲気の圧力は２〜１００ｋＰａであると好ましい。 In the first temperature raising step, the mixture is heated in a non-oxidizing atmosphere to prevent oxidation of the mixture. Specific examples of the non-oxidizing atmosphere include a vacuum, a nitrogen atmosphere, an inert atmosphere, and a hydrogen atmosphere. The pressure of the nitrogen atmosphere in the second temperature raising step is 2 kPa or more. However, when the pressure of the nitrogen atmosphere is higher than 100 kPa, the cermet sinterability tends to decrease. The pressure is preferably 2 to 100 kPa.
本発明のサーメットの具体的な製造方法としては、以下の方法が挙げられる。ＴｉＮ、ＴｉＣＮ、金属元素がＴｉおよびＷである炭化物、窒化物、炭窒化物およびこれらの相互固溶体の中の少なくとも１種の粉末と、ＷＣ粉と、鉄族金属の粉末を用意する。これらの粉末は、市販のものまたは固溶化高温熱処理により調製されたものであり、その平均粒径等は特に制限されないが、例えば、米国材料試験協会（ＡＳＴＭ）規格Ｂ３３０に記載のフィッシャー法（Fisher Sub-Sieve Sizer（FSSS））により測定した平均粒径が０．１〜１０μｍであることが好ましく、さらに好ましくは０．５〜８μｍである。これらの粉末を所定比率に秤量し、溶媒とともに湿式ボールミルにて混合し、混合後に溶媒を蒸発させて混合物を得る。得られた混合物にパラフィン等の成形用ワックスを添加して所定の形状に成形する。なお、所定の形状に成形する方法としては、プレス成形、押出成形、射出成形などを挙げることができる。成形した混合物を焼結炉に入れて、真空中で３５０〜５００℃まで昇温してワックスを除去させた後、真空中または窒素雰囲気で３５０〜５００℃から１１５０〜１３５０℃の第１加熱温度まで昇温させる。さらに、混合物を１１５０〜１３５０℃の第１加熱温度から１４５０〜１６５０℃の第２加熱温度まで圧力２ｋＰａ以上の窒素雰囲気中で昇温させ、１４５０〜１６５０℃の第２加熱温度にて、第２加熱温度まで昇温させる昇温工程よりも低い圧力の窒素雰囲気中または真空中で１０〜６０分間保持する。その後、第２加熱温度まで昇温させる工程よりも低い圧力の窒素雰囲気中または真空中で１０００〜１３００℃の第１冷却温度まで冷却し、その後、常温まで冷却すると本発明のサーメットを製造することができる。 The following method is mentioned as a specific manufacturing method of the cermet of this invention. At least one powder among TiN, TiCN, carbides, nitrides, carbonitrides and their mutual solid solutions whose metal elements are Ti and W, WC powder, and iron group metal powder are prepared. These powders are commercially available or prepared by solution heat treatment at high temperatures, and the average particle size and the like are not particularly limited. For example, the Fisher method (Fisher method described in American Society for Testing and Materials (ASTM) standard B330) The average particle size measured by Sub-Sieve Sizer (FSSS) is preferably 0.1 to 10 μm, more preferably 0.5 to 8 μm. These powders are weighed at a predetermined ratio, mixed with a solvent by a wet ball mill, and after mixing, the solvent is evaporated to obtain a mixture. A molding wax such as paraffin is added to the obtained mixture to form a predetermined shape. In addition, as a method of shape | molding in a predetermined shape, press molding, extrusion molding, injection molding, etc. can be mentioned. The molded mixture is put in a sintering furnace and heated to 350 to 500 ° C. in vacuum to remove the wax, and then the first heating temperature of 350 to 500 ° C. to 1150 to 1350 ° C. in vacuum or in a nitrogen atmosphere. Let the temperature rise. Furthermore, the mixture was heated from a first heating temperature of 1150 to 1350 ° C. to a second heating temperature of 1450 to 1650 ° C. in a nitrogen atmosphere having a pressure of 2 kPa or more, and at a second heating temperature of 1450 to 1650 ° C., It hold | maintains for 10 to 60 minutes in the nitrogen atmosphere or the vacuum of a pressure lower than the temperature rising process heated up to heating temperature. Then, it cools to 1000-1300 degreeC 1st cooling temperature in a nitrogen atmosphere or a vacuum lower than the process of heating up to 2nd heating temperature, and manufactures the cermet of this invention when it cools to normal temperature after that. Can do.
本発明のサーメットおよび被覆サーメットは耐摩耗性と耐欠損性に優れる。本発明のサーメットおよび被覆サーメットは、切削工具として用いると切削工具の寿命を長くするという効果を奏する。 The cermet and coated cermet of the present invention are excellent in wear resistance and fracture resistance. The cermet and coated cermet of the present invention have an effect of prolonging the life of the cutting tool when used as a cutting tool.
サーメットの原料粉末として、平均粒径４．３μｍのＴｉ（Ｃ0.5Ｎ0.5）粉、平均粒径３．２μｍのＴｉ（Ｃ0.3Ｎ0.7）粉、平均粒径１．５μｍのＴｉＮ粉、平均粒径１．５μｍの（Ｔｉ0.9Ｗ0.1）（Ｃ0.5Ｎ0.5）粉、平均粒径１．５μｍのＷＣ粉、平均粒径２．０μｍのＷ粉、平均粒径６μｍの黒鉛粉（Ｇと記す）、平均粒径１．０μｍの（Ｗ，Ｔｉ）Ｃ粉（重量比でＷＣ：ＴｉＣ＝７０：３０）、平均粒径３．２μｍのＭｏ2Ｃ粉、平均粒径１．５μｍのＴａＣ粉、平均粒径１．１μｍのＮｂＣ粉、平均粒径３．１μｍのＺｒＣ粉、平均粒径１．４μｍのＣｒ3Ｃ2粉、平均粒径１．４μｍのＣｏ粉、平均粒径１．３μｍのＮｉ粉を用意した。これらを用いて表１に示す配合組成に秤量した。 As raw material powder of cermet, Ti (C 0.5 N 0.5 ) powder with an average particle size of 4.3 μm, Ti (C 0.3 N 0.7 ) powder with an average particle size of 3.2 μm, TiN powder with an average particle size of 1.5 μm, average particle (Ti 0.9 W 0.1 ) (C 0.5 N 0.5 ) powder having a diameter of 1.5 μm, WC powder having an average particle diameter of 1.5 μm, W powder having an average particle diameter of 2.0 μm, graphite powder having an average particle diameter of 6 μm (denoted as G) ), (W, Ti) C powder with an average particle size of 1.0 μm (weight ratio WC: TiC = 70: 30), Mo 2 C powder with an average particle size of 3.2 μm, TaC powder with an average particle size of 1.5 μm NbC powder having an average particle size of 1.1 μm, ZrC powder having an average particle size of 3.1 μm, Cr 3 C 2 powder having an average particle size of 1.4 μm, Co powder having an average particle size of 1.4 μm, 1.3 μm of average particle size Ni powder was prepared. These were weighed to the composition shown in Table 1.
秤量した原料粉末を溶媒とともに湿式ボールミルにより混合した。なお、スラリー状の混合物の総重量に対して１〜２重量％のパラフィンを混合時に入れた。湿式ボールミル後に溶媒を蒸発させた混合物を、焼結後の大きさがＩＳＯ規格ＴＮＭＧ１６０４０８のインサート形状になるようにプレス成形した。 The weighed raw material powder was mixed with a solvent by a wet ball mill. In addition, 1-2 weight% of paraffin with respect to the total weight of a slurry-like mixture was put at the time of mixing. The mixture obtained by evaporating the solvent after the wet ball mill was press-molded so that the size after sintering became an insert shape of ISO standard TNMG160408.
発明品１〜５および比較品１については、プレス成形した混合物を焼結炉に入れて、真空中で常温から４５０℃まで徐々に昇温してパラフィンを蒸発させた後、真空中で４５０℃から１２２０℃の第１加熱温度まで昇温させた。さらに、混合物を１２２０℃の第１加熱温度から１５３０℃の第２加熱温度まで圧力１０ｋＰａの窒素雰囲気中にて昇温させ、さらに１５３０℃の第２加熱温度にて圧力１０．０Ｐａの真空中で６０分間保持した後、１５３０℃の第２加熱温度から１２００℃の第１冷却温度まで圧力１０．０Ｐａの真空雰囲気中にて冷却させ、さらに１２００℃の第１冷却温度から常温まで圧力２５０ｋＰａのアルゴン雰囲気中にて冷却した。 For invention products 1 to 5 and comparative product 1, the press-molded mixture was placed in a sintering furnace and gradually heated from room temperature to 450 ° C. in vacuum to evaporate paraffin, and then 450 ° C. in vacuum. To 1220 ° C. to the first heating temperature. Further, the mixture was heated from a first heating temperature of 1220 ° C. to a second heating temperature of 1530 ° C. in a nitrogen atmosphere at a pressure of 10 kPa, and further in a vacuum at a pressure of 10.0 Pa at a second heating temperature of 1530 ° C. After holding for 60 minutes, cooling is performed in a vacuum atmosphere at a pressure of 10.0 Pa from a second heating temperature of 1530 ° C. to a first cooling temperature of 1200 ° C., and argon at a pressure of 250 kPa from the first cooling temperature of 1200 ° C. to room temperature. Cooled in the atmosphere.
比較品２については、プレス成形した混合物を焼結炉に入れて、真空中で常温から４５０℃まで徐々に昇温してパラフィンを蒸発させた後、真空中で４５０℃から１３００℃の第１加熱温度まで昇温させた。さらに、混合物を１３００℃の第１加熱温度から１４５０℃の第２加熱温度まで圧力１０ｋＰａのアルゴン雰囲気中で昇温させ、さらに１４５０℃の第２加熱温度にて圧力１０ｋＰａのアルゴン雰囲気中で６０分間保持した。その後、真空中で１４５０℃の第２加熱温度から常温まで冷却した。 For the comparative product 2, the press-molded mixture was put in a sintering furnace and gradually heated from room temperature to 450 ° C. in a vacuum to evaporate the paraffin, and then the first of 450 ° C. to 1300 ° C. in vacuum. The temperature was raised to the heating temperature. Further, the mixture was heated from a first heating temperature of 1300 ° C. to a second heating temperature of 1450 ° C. in an argon atmosphere at a pressure of 10 kPa, and further in an argon atmosphere at a pressure of 10 kPa at a second heating temperature of 1450 ° C. for 60 minutes. Retained. Then, it cooled from the 2nd heating temperature of 1450 degreeC to normal temperature in the vacuum.
比較品３については、プレス成形した混合物を焼結炉に入れて、真空中で常温から５００℃まで徐々に昇温してパラフィンを蒸発させた後、真空中で５００℃から１２００℃の第１加熱温度まで昇温させた。さらに、混合物を１２００℃の第１加熱温度から１５３０℃の第２加熱温度まで圧力０．１ｋＰａの窒素雰囲気中で昇温させ、さらに１５３０℃の第２加熱温度にて圧力０．１ｋＰａの窒素雰囲気中で６０分間保持した後、１５３０℃の第２加熱温度から１２００℃の第１冷却温度まで圧力０．１ｋＰａの窒素雰囲気中にて冷却させ、さらに真空中で１２００℃の第１冷却温度から常温まで冷却した。 For Comparative Product 3, the press-molded mixture was placed in a sintering furnace and gradually heated from room temperature to 500 ° C. in a vacuum to evaporate paraffin. The temperature was raised to the heating temperature. Further, the mixture was heated in a nitrogen atmosphere at a pressure of 0.1 kPa from a first heating temperature of 1200 ° C. to a second heating temperature of 1530 ° C., and further a nitrogen atmosphere at a pressure of 0.1 kPa at the second heating temperature of 1530 ° C. In a nitrogen atmosphere at a pressure of 0.1 kPa from a second heating temperature of 1530 ° C. to a first cooling temperature of 1200 ° C., and further from a first cooling temperature of 1200 ° C. to room temperature in a vacuum. Until cooled.
比較品４については、プレス成形した混合物を焼結炉に入れて、真空中で常温から４５０℃まで徐々に昇温してパラフィンを蒸発させた後、真空中で４５０℃から１４２０℃まで昇温させ、さらに１４２０℃にて真空中で６０分間保持した後、真空中で１４２０℃から常温まで冷却した。 For the comparative product 4, the press-molded mixture is put in a sintering furnace, and the temperature is gradually raised from room temperature to 450 ° C. in a vacuum to evaporate paraffin, and then the temperature is raised from 450 ° C. to 1420 ° C. in a vacuum. The mixture was further held at 1420 ° C. in a vacuum for 60 minutes, and then cooled from 1420 ° C. to room temperature in a vacuum.
得られたサーメットの断面組織から走査型電子顕微鏡付属のＥＤＳおよび透過型電子顕微鏡付属のＥＤＳを用いて表面領域、中間領域および内部領域に含まれる各相の組成を分析した。また、サーメットの断面組織写真から画像処理ソフトＩｍａｇｅ Ｐｒｏ−Ｐｌｕｓを用いて表面領域、中間領域および内部領域に含まれる各相の面積率を測定した。さらに、サーメットの断面組織から走査型電子顕微鏡により表面領域、中間領域および内部領域に含まれる炭化タングステン相の形状を調べた。得られた結果は、表２〜１０に示した。ここで、表面領域とはサーメットの表面近傍にある、炭化タングステン相と結合相とからなる領域のことであり、内部領域とは、表面領域よりも内部にある、炭化タングステン相と硬質相と結合相とからなる領域のことである。また、表面領域と内部領域との間に中間領域が形成される場合がある。中間領域は、炭化タングステン相と硬質相と結合相とからなり、サーメットの断面組織における、硬質相のコアリム相のリムの面積率が内部領域にある硬質相のコアリム相のリムの面積率よりも増加し、硬質相のコアリム相のコアの面積率が内部領域にある硬質相のコアリム相のコアの面積率よりも減少し、炭化タングステン相の面積率が内部領域にある炭化タングステン相の面積率よりも減少した領域である。中間領域においては、表面側から内部側に向かって各相の組成と面積率が漸減または漸増しているので、中間領域の表面側と中間領域の内部側における各相の組成と面積率を表２〜７に示した。また、発明品１〜５、比較品１〜４に含まれる炭化タングステン相の組成はＷＣのみであったので、以下、発明品１〜５、比較品１〜４のサーメットに含まれる炭化タングステン相はＷＣ相と記載した。 From the cross-sectional structure of the obtained cermet, the composition of each phase contained in the surface region, the intermediate region and the internal region was analyzed using EDS attached to the scanning electron microscope and EDS attached to the transmission electron microscope. Moreover, the area ratio of each phase contained in the surface region, the intermediate region and the internal region was measured from the cross-sectional structure photograph of the cermet using image processing software Image Pro-Plus. Further, the shape of the tungsten carbide phase contained in the surface region, the intermediate region and the internal region was examined from the cross-sectional structure of the cermet by a scanning electron microscope. The obtained results are shown in Tables 2 to 10. Here, the surface region is a region composed of a tungsten carbide phase and a binder phase in the vicinity of the surface of the cermet, and the inner region is a bond between the tungsten carbide phase and the hard phase inside the surface region. It is an area consisting of phases. In addition, an intermediate region may be formed between the surface region and the internal region. The intermediate region is composed of a tungsten carbide phase, a hard phase, and a binder phase, and the area ratio of the rim of the hard phase core rim phase in the cross-sectional structure of the cermet is larger than the area ratio of the rim of the hard phase core rim phase in the inner region. The area ratio of the core of the hard rim phase of the hard phase is increased and the area ratio of the core of the core rim phase of the hard phase in the inner region is decreased, and the area ratio of the tungsten carbide phase in the inner region is increased. This is a reduced area. In the intermediate region, the composition and area ratio of each phase gradually decrease or increase from the surface side to the inner side, so the composition and area ratio of each phase on the surface side of the intermediate region and the inner side of the intermediate region are displayed. Shown in 2-7. Moreover, since the composition of the tungsten carbide phase contained in the inventive products 1 to 5 and the comparative products 1 to 4 was only WC, hereinafter, the tungsten carbide phase contained in the cermets of the inventive products 1 to 5 and the comparative products 1 to 4 Was described as WC phase.
また、得られたサーメットの表面領域、中間領域および内部領域の断面組織を走査型電子顕微鏡にて観察し、３０００倍に拡大して長さ３４μｍ×幅２４μｍの長方形の断面組織写真を撮影し、画像処理ソフトＩｍａｇｅ Ｐｒｏ−Ｐｌｕｓを用いて、表面領域、中間領域および内部領域の断面組織を含まれるＷＣ相について、ＷＣ相全体の面積に対する、Ｂに対するＡの比（Ａ／Ｂ）が２以上である板状ＷＣの面積率と、ＷＣ相全体の面積に対する、Ｂに対するＡの比（Ａ／Ｂ）が２未満である粒状ＷＣの面積率とを測定した。その結果を表１１に示す。 Further, the cross-sectional structure of the surface region, the intermediate region and the internal region of the obtained cermet was observed with a scanning electron microscope, and a photograph of a rectangular cross-sectional structure having a length of 34 μm and a width of 24 μm was taken at a magnification of 3000 times, Using the image processing software Image Pro-Plus, the ratio of A to B (A / B) with respect to the area of the entire WC phase is 2 or more for the WC phase including the cross-sectional structures of the surface region, the intermediate region, and the internal region. The area ratio of a certain plate-like WC and the area ratio of granular WC in which the ratio of A to B (A / B) with respect to the area of the entire WC phase was less than 2 were measured. The results are shown in Table 11.
得られたサーメットの逃げ面側の表面に対してＣｕ−Ｋα線を用いたＸ線回折測定を行って、ＷＣ（１００）面のピーク強度に対するＷＣ（００１）面のピーク強度比（ｈ（００１）／ｈ（１００））を測定した。また、得られたサーメットの表面から深さ方向に２ｍｍまで研削し、さらに鏡面研磨してサーメット内部領域の鏡面研磨面を得た。内部領域の鏡面研磨面に対してＣｕ−Ｋα線を用いたＸ線回折測定を行って、内部領域のＷＣ（１００）面のピーク強度に対するＷＣ（００１）面のピーク強度比（ｈ（００１）／ｈ（１００））を測定した。その結果を表１２に示す。 X-ray diffraction measurement using Cu—Kα rays was performed on the flank side surface of the obtained cermet, and the peak intensity ratio of the WC (001) plane to the peak intensity of the WC (100) plane (h (001 ) / H (100)). Moreover, it grind | polished to 2 mm from the surface of the obtained cermet to the depth direction, and also mirror-polished and obtained the mirror-polished surface of the cermet internal area | region. The X-ray diffraction measurement using Cu—Kα ray is performed on the mirror-polished surface in the inner region, and the peak intensity ratio of the WC (001) surface to the peak intensity of the WC (100) surface in the inner region (h (001) / H (100)). The results are shown in Table 12.
サーメットの表面領域と内部領域の断面組織を走査型電子顕微鏡により３０００倍に拡大した長さ３４μｍ×幅２４μｍの長方形の断面組織について、ＷＣ相の最も長い辺に平行な直線でＷＣ相を横切る直線の最大長さをＡ（μｍ）と表し、炭化タングステンの最長辺に垂直な直線で炭化タングステンを横切る直線の最大長さをＢ（μｍ）と表したとき、Ｂに対するＡの比（Ａ／Ｂ）が２以上であり、かつ、ＡとＢとを乗じた値Ｃ（Ｃ＝Ａ×Ｂ）が２×１０-12ｍ2以上であるＷＣ相の有無を調べた。各試料の表面領域と内部領域の３４μｍ×２４μｍの断面組織写真中に、（Ａ／Ｂ）が２以上であり、かつ、Ｃが２×１０-12ｍ2以上であるＷＣ相が含まれているときは表１３に○印で表し、写真の中に含まれていないときは表１３に×印で表した。 A straight line crossing the WC phase with a straight line parallel to the longest side of the WC phase of a rectangular cross-sectional structure of length 34 μm × width 24 μm obtained by magnifying the cross-sectional structure of the surface region and the internal region of the cermet 3000 times with a scanning electron microscope Is expressed as A (μm), and when the maximum length of a straight line perpendicular to the longest side of tungsten carbide and crossing tungsten carbide is expressed as B (μm), the ratio of A to B (A / B) ) Is 2 or more, and the presence or absence of a WC phase in which a value C (C = A × B) obtained by multiplying A and B is 2 × 10 −12 m 2 or more was examined. The 34 μm × 24 μm cross-sectional structure photograph of the surface region and internal region of each sample includes a WC phase in which (A / B) is 2 or more and C is 2 × 10 −12 m 2 or more. When it is present, it is represented by a circle in Table 13, and when it is not included in the photograph, it is represented by a cross in Table 13.
ＩＳＯ規格ＴＮＭＧ１６０４０８形状の発明品１〜５、比較品１〜４のサーメットの拘束面に研削を施し、刃先にホーニングを施した。さらに膜構成が、（基材側）平均膜厚１．０μｍＴｉＮ−平均膜厚８．０μｍＴｉ（Ｃ，Ｎ）−平均膜厚０．５μｍＴｉ（Ｃ，Ｎ，Ｏ）−平均膜厚１．５μｍＡｌ2Ｏ3−平均膜厚０．２μｍＴｉＮ（表面側）、総膜厚の平均値が１１．２μｍである被膜をＣＶＤ法により被覆した。ＣＶＤ被覆して得られた被覆サーメットを用いて切削試験１，２を行った。 The constraining surfaces of the cermets of inventions 1 to 5 and comparative products 1 to 4 having the ISO standard TNMG160408 shape were ground and the blade edge was honed. Further, the film structure is (base material side) average film thickness 1.0 μmTiN−average film thickness 8.0 μmTi (C, N) −average film thickness 0.5 μmTi (C, N, O) −average film thickness 1.5 μm Al 2 A film having an O 3 -average film thickness of 0.2 μm TiN (surface side) and an average value of the total film thickness of 11.2 μm was coated by a CVD method. Cutting tests 1 and 2 were performed using a coated cermet obtained by CVD coating.
[切削試験１]
耐欠損性評価試験
試料形状：ＴＮＭＧ１６０４０８
被削材：Ｓ４５Ｃ（形状：円柱に４本の溝を入れた略円柱状）
切削速度：１５０ｍ／ｍｉｎ
切り込み：２．０ｍｍ
送り量：０．２５ｍｍ／ｒｅｖ
雰囲気：湿式切削
試験回数：３回
寿命の判定基準：欠損するまでの衝撃回数を寿命とする。なお、衝撃回数が２５０００回になるまでに欠損しない場合は、その時点で試験を終了する。
[Cutting test 1]
Fracture resistance evaluation test sample shape: TNMG160408
Work material: S45C (shape: substantially cylindrical shape with four grooves in a cylinder)
Cutting speed: 150 m / min
Cutting depth: 2.0mm
Feed amount: 0.25mm / rev
Atmosphere: Number of wet cutting tests: 3 times Judgment criteria of life: The number of impacts until chipping is regarded as the life. In addition, a test is complete | finished at that time, when it does not lose | delete by the frequency | count of impact reaching 25000 times.
[切削試験２]
耐摩耗性評価試験
試料形状：ＴＮＭＧ１６０４０８
被削材：Ｓ４５Ｃ（形状：円柱）
切削速度：２００ｍ／ｍｉｎ
切り込み：２．０ｍｍ
送り量：０．２５ｍｍ／ｒｅｖ
雰囲気：湿式切削
寿命の判定基準：欠損したとき、または、最大逃げ面摩耗量ＶBmaxが０．３ｍｍ以上になったときを寿命とする。
[Cutting test 2]
Abrasion resistance evaluation test sample shape: TNMG160408
Work material: S45C (shape: cylinder)
Cutting speed: 200 m / min
Cutting depth: 2.0mm
Feed amount: 0.25mm / rev
Atmosphere: Criteria for wet cutting life: Life is defined as when it is missing or when the maximum flank wear amount V Bmax is 0.3 mm or more.
切削試験１、２の結果を点数化した。すなわち、切削試験１の衝撃回数について、２５０００回以上を３点、２００００回以上２５０００回未満を２点、１５０００回以上２００００回未満を１点、１５０００回未満を０点とし、１回目から３回目までの結果を平均した。また、切削試験２の加工長について、４．５ｋｍ以上を３点、３．０ｋｍ以上４．５ｋｍ未満を２点、１．５ｋｍ以上３．０ｋｍ未満を１点、１．５ｋｍ未満を０点とした。切削試験１の点数の平均値と切削試験２の点数とを合計し、その値を総合評価の結果とした。点数が大きいほど切削性能に優れる。得られた総合評価の結果を表１６に示した。 The results of cutting tests 1 and 2 were scored. That is, the number of impacts in the cutting test 1 is 3 times from 25000 times, 2 points from 20000 times to less than 25000 times, 1 point from 15000 times to less than 20000 times, and 0 points from less than 15000 times. The results were averaged. Moreover, about the processing length of the cutting test 2, 4.5 km or more is 3 points, 3.0 km or more and less than 4.5 km is 2 points, 1.5 km or more and less than 3.0 km is 1 point, and less than 1.5 km is 0 point did. The average value of the score of the cutting test 1 and the score of the cutting test 2 were totaled, and the value was used as the result of comprehensive evaluation. The larger the score, the better the cutting performance. The obtained comprehensive evaluation results are shown in Table 16.
発明品の総合評価はすべて５点以上となり、総合評価において比較品よりも優れることが分かる。 The overall evaluation of the invention products is all 5 points or more, and it is understood that the overall evaluation is superior to the comparative product.
Claims (6)
The surface of the cermet according to any one of claims 1 to 5 , Ti, Zr, Hf, V, Nb, Ta, Cr, Mo, W, Al, Si metal, carbide, nitride, oxide and A coated cermet coated with at least one film selected from these mutual solid solutions.
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