JP5436083B2 - Cermet sintered body and cutting tool - Google Patents
Cermet sintered body and cutting tool Download PDFInfo
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Description
本発明はサーメット焼結体および切削工具に関する。 The present invention relates to a cermet sintered body and a cutting tool.
現在、切削工具としてＴｉを主成分とするサーメット焼結体が広く使われている。サーメットの硬質相は芯部と周辺部とからなる有芯構造をとりやすいことが知られているが、例えば、特許文献１では、周辺部の面積割合が多いほど、鋳鉄との耐化学反応性が向上することが開示され、周辺部の平均粒径／芯部の平均粒径の比率を３〜８としたサーメットが記載されている。 At present, cermet sintered bodies mainly composed of Ti are widely used as cutting tools. Although it is known that the hard phase of cermet tends to have a cored structure composed of a core part and a peripheral part, for example, in Patent Document 1, as the area ratio of the peripheral part increases, the chemical reactivity with cast iron increases. Is disclosed, and cermets are described in which the ratio of the average particle diameter of the peripheral part / the average particle diameter of the core part is 3 to 8.
しかしながら、特許文献１のように周辺部の面積比率を多くするにはサーメットの焼成温度を高くする必要があるが、焼成温度を高くすると、焼成中に生じる金属原子の移動や窒素原子の拡散の影響で、焼結体が元の成形体の形状から大きく変形してしまうという問題があった。焼結体が変形した場合、焼結体の表面を研磨加工して形状を整える方法もあるが、製造コストがかさむとともに複雑な形状の切削工具の場合には研磨加工自体が困難であった。 However, as in Patent Document 1, in order to increase the area ratio of the peripheral part, it is necessary to increase the cermet firing temperature. However, if the firing temperature is increased, the movement of metal atoms and the diffusion of nitrogen atoms that occur during firing are increased. Due to the influence, there was a problem that the sintered body was greatly deformed from the shape of the original molded body. When the sintered body is deformed, there is a method of adjusting the shape by polishing the surface of the sintered body. However, the manufacturing cost increases, and in the case of a cutting tool having a complicated shape, the polishing process itself is difficult.
本発明は上記問題を解決するためのものであり、その目的は切削性能が高い組織を有するとともに、焼結体の変形を抑制できて複雑な形状でも容易に作製可能なサーメット焼結体および切削工具を提供することである。 The present invention is intended to solve the above-mentioned problems, and its purpose is to provide a cermet sintered body that has a structure with high cutting performance and that can suppress deformation of the sintered body and can be easily produced even in a complicated shape. Is to provide a tool.
本発明のサーメット焼結体は、第１サーメットと、該第１サーメットの表面に配置されて少なくとも切刃を構成する第２サーメットとが積層されてなり、
前記第１サーメットおよび前記第２サーメットは、周期表第４、５および６族金属のうちの１種以上の炭化物、窒化物、炭窒化物およびこれらの固溶体の中から選ばれた１種以上からなる硬質相と、主として鉄族金属からなる結合相とから構成され、前記硬質相は、ＴｉＣＮを主成分とする第１硬質相と、周期表第４、５および６族金属の少なくとも1種と
Ｔｉとの複合炭窒化物固溶体の第２硬質相とからなり、
前記第２サーメットは前記第１サーメットよりも前記硬質相中の前記第２硬質相の存在割合が多く、前記第１サーメットは前記第２サーメットよりも前記結合相の存在割合が少ないものである。
The cermet sintered body of the present invention is formed by laminating a first cermet and a second cermet disposed on the surface of the first cermet and constituting at least a cutting blade,
The first cermet and the second cermet may be one or more selected from one or more carbides, nitrides, carbonitrides, and solid solutions of the metals in Groups 4, 5, and 6 of the periodic table. The hard phase is composed of a first hard phase mainly composed of TiCN and at least one of Group 4, 5 and 6 metals of the periodic table. Comprising a second hard phase of a composite carbonitride solid solution with Ti,
Said second cermet is often existence ratio of the second hard phase of the hard phase than said first cermet, said first cermet are those existing ratio of said binder phase is less than said second cermet.
ここで、前記第２サーメットの厚みはサーメット全体の厚みに対して１０〜３５％であることが望ましい。 Here, the thickness of the second cermet is preferably 10 to 35% with respect to the thickness of the entire cermet.
また、前記第２サーメットには、表面側に、前記硬質相中の前記第２硬質相の存在割合が前記第２サーメットの前記第１サーメット側の前記第２硬質相の存在割合より多く、かつ前記結合相の存在割合が前記第２サーメットの前記第１サーメット側の前記結合相の存在割合より少ない表面領域が存在することが望ましい。
Further, wherein the second cermet, a surface side, the existence ratio of the second hard phase of the hard phase is more than the presence ratio of the second hard phase of the first cermet side of the second cermet, and it is desirable that less surface area than the presence ratio of the binder phase of the first cermet side of the existing ratio of the binder phase is said second cermet is present.
さらに、前記第１サーメットの硬度が前記第２サーメットの硬度より高く、かつ前記第２サーメットの前記表面領域の硬度が前記第２サーメットの前記第１サーメット側の硬度よりも高いことが望ましい。 Furthermore, it is desirable that the hardness of the first cermet is higher than the hardness of the second cermet, and the hardness of the surface region of the second cermet is higher than the hardness of the second cermet on the first cermet side.
また、前記第１サーメットにおける前記硬質相の平均粒径が前記第２サーメットにおける前記硬質相の平均粒径より大きく、かつ前記第２サーメットの前記表面領域における前記硬質相の平均粒径が前記第２サーメットの前記第１サーメット側における前記硬質相の平均粒径よりも大きいことが望ましい。 The average particle size of the hard phase in the first cermet is larger than the average particle size of the hard phase in the second cermet, and the average particle size of the hard phase in the surface region of the second cermet is It is desirable that the average particle size of the hard phase on the first cermet side of 2 cermets be larger.
さらに、前記第１サーメットと前記第２サーメットとの境界に界面が存在し、かつ前記第２サーメットの前記表面領域と前記第１サーメット側との境界には界面が存在しない構成となっている。 Further, an interface exists at the boundary between the first cermet and the second cermet, and no interface exists at the boundary between the surface region of the second cermet and the first cermet side.
また、本発明の切削工具は、周期表第４、５および６族金属のうちの１種以上の炭化物、窒化物、炭窒化物およびこれらの固溶体の中から選ばれた１種以上からなる硬質相と、主として鉄族金属からなる結合相との焼結体から構成され、前記硬質相は、ＴｉＣＮを主成分とする第１硬質相と、周期表第４、５および６族金属の少なくとも1種とＴｉとの複
合炭窒化物固溶体の第２硬質相とからなり、
切刃を含むすくい面およびその近傍領域をＡ領域とし、該Ａ領域以外の領域である前記焼結体の内部および逃げ面の中央部位をＢ領域としたとき、前記Ａ領域では前記Ｂ領域よりも前記硬質相中の前記第２硬質相の存在割合が多く、前記Ｂ領域では前記Ａ領域よりも前記結合相の存在割合が少ないものである。
Further, the cutting tool of the present invention is a hard material composed of one or more selected from the group consisting of one or more carbides, nitrides, carbonitrides and solid solutions of the metals in Groups 4, 5 and 6 of the periodic table. The hard phase is composed of a first hard phase mainly composed of TiCN and at least one of Group 4, 5, and 6 metals of the periodic table. A second hard phase of a composite carbonitride solid solution of seeds and Ti,
When the rake face including the cutting edge and the vicinity region thereof are defined as A region, and the inside of the sintered body and the central portion of the flank which are regions other than the A region are defined as B region, the A region is more than the B region. In the hard phase, the second hard phase is present in a large proportion, and the B region has a smaller proportion of the binder phase than the A region.
ここで、断面組織観察にて、前記Ａ領域における前記第１硬質相の面積比率をＳ１Ａ、該第２硬質相の面積比率をＳ２Ａとし、前記Ｂ領域における前記第１硬質相の面積比率をＳ１Ｂ、前記第２硬質相の面積比率をＳ２Ｂとしたとき、前記Ｓ１Ａと前記Ｓ２Ａとの比率（Ｓ２Ａ／Ｓ１Ａ）が２〜８であり、前記Ｓ１Ｂと前記Ｓ２Ｂとの比率（Ｓ２Ｂ／Ｓ１Ｂ）が０．５〜１．５であることが望ましい。 Here, in cross-sectional structure observation, the area ratio of the first hard phase in the A region is S 1A , the area ratio of the second hard phase is S 2A, and the area ratio of the first hard phase in the B region the S 1B, when the area ratio of the second hard phase was S 2B, the a ratio (S 2A / S 1A) from 2 to 8 and S 1A and the S 2A, the S 1B and the S 2B The ratio (S 2B / S 1B ) is preferably 0.5 to 1.5.
また、前記Ａ領域は前記すくい面から５〜１００μｍの厚みで存在することが望ましい。 Moreover, it is desirable that the region A exists in a thickness of 5 to 100 μm from the rake face.
さらに、前記Ａ領域と前記Ｂ領域との間に、前記Ｂ領域よりも前記硬質相中の前記第２硬質相の存在割合が少なく、かつ前記Ａ領域よりも前記結合相の存在割合が多いＣ領域が存在することが望ましい。
Further, the between the A region and the B region, the B less abundance ratio of the second hard phase of the hard phase than the region, and the abundance ratio of the binder phase than the A region is often C It is desirable that the area exists.
また、前記Ａ領域の硬度が前記Ｃ領域の硬度より高く、かつ前記Ｂ領域の硬度が前記Ｃ領域の硬度よりも高いことが望ましい。 Further, it is desirable that the hardness of the A region is higher than the hardness of the C region, and the hardness of the B region is higher than the hardness of the C region.
さらに、前記Ａ領域における前記硬質相の平均粒径が前記Ｃ領域における前記硬質相の平均粒径より大きく、かつ前記Ｂ領域における前記硬質相の平均粒径が前記Ｃ領域における硬質相の平均粒径よりも大きいことが望ましい。 Further, the average particle size of the hard phase in the A region is larger than the average particle size of the hard phase in the C region, and the average particle size of the hard phase in the B region is the average particle of the hard phase in the C region. Desirably larger than the diameter.
また、前記Ａ領域と前記Ｃ領域との境界に界面が存在せず、かつ前記Ｂ領域と前記Ｃ領域との境界には界面が存在する構成となっている。 Further, there is no interface at the boundary between the A region and the C region, and there is an interface at the boundary between the B region and the C region.
本発明のサーメット焼結体および切削工具によれば、結合相の存在割合が少ない第１サーメットと、第２硬質相の存在割合が多い第２サーメットとが積層された構造、すなわち、切刃を含むすくい面およびその近傍領域をＡ領域、前記Ａ領域以外の領域である焼結体の内部および逃げ面の中央部位をＢ領域としたとき、前記Ａ領域では前記Ｂ領域よりも前記硬質相中の前記第２硬質相の存在割合が多く、前記Ｂ領域では前記Ａ領域よりも結合相の存在割合が少ない構成からなるので、サーメット焼結体の表面に存在する切刃は切削性能が高い第２サーメットの組織からなるとともに、基体を構成する第１サーメットは焼結による変形が小さいので、焼結体全体の変形を抑制できて複雑な形状でも容易に寸法精度の高い切削工具を作製できる。
According to the cermet sintered body and the cutting tool of the present invention, a structure in which a first cermet having a low presence ratio of a binder phase and a second cermet having a high presence ratio of a second hard phase are laminated, that is, a cutting edge is formed. When the rake face to be included and the vicinity thereof are the A region, and the inside of the sintered body, which is a region other than the A region, and the central portion of the flank face are the B region, the A region is more in the hard phase than the B region. many existing ratio of the second hard phase is, since the in region B consisting configuration abundance ratio of the binder phase is less than the area a, the cutting edge on the surface of the sintered cermet is the high cutting performance Since the first cermet constituting the substrate is small in deformation due to sintering, the first cermet constituting the base body can suppress deformation of the entire sintered body, and a cutting tool with high dimensional accuracy can be easily produced even in a complicated shape.
なお、断面組織観察にて、Ａ領域における前記第１硬質相の面積比率をＳ１Ａ、該第２硬質相の面積比率をＳ２Ａ、Ｂ領域における前記第１硬質相の面積比率をＳ１Ｂ、該第２硬質相の面積比率をＳ２Ｂとしたとき、前記Ｓ１Ａと前記Ｓ２Ａとの比率（Ｓ２Ａ／Ｓ１Ａ）が２〜８であり、前記Ｓ１Ｂと前記Ｓ２Ｂとの比率（Ｓ２Ｂ／Ｓ１Ｂ）が０．５〜１．５であることが、切削性能を高くかつ変形を小さく抑制できる点で望ましい。 In cross-sectional structure observation, the area ratio of the first hard phase in the A region is S 1A , the area ratio of the second hard phase is S 2A , and the area ratio of the first hard phase in the B region is S 1B , When the area ratio of the second hard phase is S 2B , the ratio of S 1A to S 2A (S 2A / S 1A ) is 2 to 8, and the ratio of S 1B to S 2B ( S 2B / S 1B ) is preferably 0.5 to 1.5 in terms of high cutting performance and low deformation.
ここで、前記第２サーメットの厚みはサーメット全体の厚みに対して１０〜３５％であることが望ましい。なお、第２サーメットが上下層の両方存在する場合には、第２サーメットの総厚みはサーメット全体の厚みに対して２０〜７０％となる。このとき、前記Ａ領域は前記すくい面から５〜１００μｍの厚みで存在することが、切削性能が高くかつ変形が小さい切削工具が製造上容易に作製できる点で望ましい。 Here, the thickness of the second cermet is preferably 10 to 35% with respect to the thickness of the entire cermet. In addition, when a 2nd cermet exists in both upper and lower layers, the total thickness of a 2nd cermet will be 20 to 70% with respect to the thickness of the whole cermet. At this time, it is desirable that the region A exists in a thickness of 5 to 100 μm from the rake face because a cutting tool having high cutting performance and small deformation can be easily manufactured.
また、前記第２サーメットには、表面側に、前記硬質相中の前記第２硬質相の存在割合が前記第２サーメットの前記第１サーメット側の前記第２硬質相の存在割合より多く、かつ前記結合相の存在割合が前記第２サーメットの前記第１サーメット側の前記結合相の存在割合より少ない表面領域が存在すること、すなわち前記Ａ領域と前記Ｂ領域との間に、前記Ｂ領域よりも硬質相中の前記第２硬質相の存在割合が少なく、かつ前記Ａ領域よりも結合相の存在割合が多いＣ領域が存在することによって、切削性能をさらに高めることができる点で望ましい。
Further, wherein the second cermet, a surface side, the existence ratio of the second hard phase of the hard phase is more than the presence ratio of the second hard phase of the first cermet side of the second cermet, and The surface area of the second cermet is less than the ratio of the binder phase on the first cermet side of the second cermet , that is, between the A region and the B region, from the B region. even small existence ratio of the second hard phase of the hard phase, and by the a C region existing ratio of the binder phase is greater than the area exists, preferable in that it can further enhance the cutting performance.
さらに、前記第１サーメットの硬度が前記第２サーメットの硬度より高く、かつ前記第２サーメットの表面領域の硬度が前記第２サーメットの前記第１サーメット側の硬度よりも高いこと、すなわち、前記Ａ領域の硬度が前記Ｃ領域の硬度より高く、かつ前記Ｂ領域の硬度が前記Ｃ領域の硬度よりも高いことが、変形を防止できるとともに切刃の耐摩耗性を高めることができる点で望ましい。 Further, the hardness of the first cermet is higher than the hardness of the second cermet, and the hardness of the surface region of the second cermet is higher than the hardness of the second cermet on the first cermet side, that is, the A It is desirable that the hardness of the region is higher than the hardness of the C region and that the hardness of the B region is higher than the hardness of the C region in that deformation can be prevented and the wear resistance of the cutting edge can be improved.
また、前記第１サーメットにおける硬質相の平均粒径が前記第２サーメットにおける硬質相の平均粒径より大きく、かつ前記第２サーメットの表面領域における硬質相の平均粒径が前記第２サーメットの前記第１サーメット側における硬質相の平均粒径よりも大きいこと、すなわち、前記Ａ領域における硬質相の平均粒径が前記Ｃ領域における硬質相の平均粒径より大きく、かつ前記Ｂ領域における硬質相の平均粒径が前記Ｃ領域における硬質相の平均粒径よりも大きいことが、組織の制御が容易な点で望ましい。
Also, larger than the average grain size of the hard phase average grain size of the hard phase in the first cermet in the second cermet, and the average particle size of the hard phase in the surface region of the second cermet of the second cermet Larger than the average particle size of the hard phase on the first cermet side, that is, the average particle size of the hard phase in the A region is larger than the average particle size of the hard phase in the C region, and It is desirable that the average particle size is larger than the average particle size of the hard phase in the C region because the structure can be easily controlled.
なお、特定の製造方法にて作製することによって、前記第１サーメットと前記第２サーメットとの境界に界面が存在し、かつ前記第２サーメットの表面領域と基体側との境界には界面が存在しない構成、すなわち前記Ａ領域と前記Ｃ領域との境界に界面が存在せず、かつ前記Ｂ領域と前記Ｃ領域との境界には界面が存在する構成となっている。
In addition, by producing by a specific manufacturing method, an interface exists at the boundary between the first cermet and the second cermet, and an interface exists at the boundary between the surface region of the second cermet and the substrate side. In other words, there is no interface at the boundary between the A area and the C area, and there is an interface at the boundary between the B area and the C area.
本発明のサーメット焼結体からなる切削工具の一例について、その（ａ）概略斜視図、（ｂ）断面模式図である図１、断面組織観察におけるＡ領域とＣ領域（第２サーメット）、Ｂ領域（第１サーメット）についての走査型電子顕微鏡写真を基に説明する。 About an example of the cutting tool which consists of a cermet sintered compact of the present invention, (a) a schematic perspective view, (b) a cross-sectional schematic diagram of FIG. 1, A region and C region (second cermet) in cross-sectional structure observation, B A description will be given based on a scanning electron micrograph of the region (first cermet).
図１の切削工具１は、第１サーメット２と、第１サーメット２の表面に配置されて少なくとも切刃７を構成する第２サーメット３とが積層されている。そして、図２に示すように、第１サーメット２および第２サーメット３は、周期表第４、５および６族金属のうちの１種以上の炭化物、窒化物、炭窒化物およびこれらの固溶体の中から選ばれた１種以上からなる硬質相５と、主として鉄族金属からなる結合相６とから構成され、硬質相５は、ＴｉＣＮを主成分とする第１硬質相５ａと、周期表第４、５および６族金属の少なくとも1種とＴｉとの複合炭窒化物固溶体の第２硬質相５ｂとからなる。 The cutting tool 1 shown in FIG. 1 includes a first cermet 2 and a second cermet 3 disposed on the surface of the first cermet 2 and constituting at least a cutting edge 7. As shown in FIG. 2, the first cermet 2 and the second cermet 3 are made of one or more kinds of carbides, nitrides, carbonitrides, and solid solutions of the metals in Groups 4, 5, and 6 of the periodic table. The hard phase 5 is composed of one or more hard phases 5 selected from the inside and a binder phase 6 mainly composed of an iron group metal. The hard phase 5 includes a first hard phase 5a mainly composed of TiCN, and a periodic table. It consists of the 2nd hard phase 5b of the composite carbonitride solid solution of at least 1 sort (s) of a 4,5,6 group metal and Ti.
そして、第２サーメット３は第１サーメット２よりも硬質相５中の第２硬質相５ｂの存在割合が多く、第１サーメット２は第２サーメット３よりも結合相６の存在割合が少ない構成となっている。
The second cermet 3 has a higher proportion of the second hard phase 5b in the hard phase 5 than the first cermet 2, and the first cermet 2 has a smaller proportion of the binder phase 6 present than the second cermet 3. It has become.
また、別の見方をすれば、切削工具１は、切刃７を含むすくい面８およびその近傍領域をＡ領域（第２サーメット３に相当）１１、Ａ領域１１以外の領域である焼結体の内部１０および逃げ面９の中央部位をＢ領域（第１サーメット２に相当）１２としたとき、Ａ領域１１ではＢ領域１２よりも硬質相５中の第２硬質相５ｂの存在割合が多く、Ｂ領域１２ではＡ領域１１よりも結合相６の存在割合が少ない構成からなっている。
From another point of view, the cutting tool 1 includes a sintered body in which the rake face 8 including the cutting edge 7 and the area near the rake face 8 are areas A (corresponding to the second cermet 3) 11 and areas other than the area A 11. When the inner portion 10 and the central portion of the flank 9 are defined as the B region (corresponding to the first cermet 2) 12, the A region 11 has a higher proportion of the second hard phase 5b in the hard phase 5 than the B region 12. The B region 12 has a structure in which the existence ratio of the binder phase 6 is smaller than that in the A region 11.
上記構成によって、切刃７は切削性能が高い第２サーメット３の組織からなるとともに、基体を構成する第１サーメット２は焼結による変形が小さいので、焼結体全体の変形を抑制できて複雑な形状でも容易に寸法精度の高い切削工具１を作製できる。なお、図１の切削工具１のすくい面８の中央部にはネジ穴１４が形成されている。 With the above configuration, the cutting edge 7 is composed of the structure of the second cermet 3 having high cutting performance, and the first cermet 2 constituting the base body is less deformed by sintering, so that deformation of the entire sintered body can be suppressed and complicated. Even with a simple shape, the cutting tool 1 with high dimensional accuracy can be easily produced. In addition, the screw hole 14 is formed in the center part of the rake face 8 of the cutting tool 1 of FIG.
ここで、図２の走査型電子顕微鏡写真から明らかなとおり、第１硬質相５ａは黒色の粒子として観察され、第２硬質相５ｂは灰白色の粒子、または白色の芯部の周辺に灰白色の周辺部が存在する有芯構造からなる粒子として観察される。なお、上記灰白色とは、写真撮影の条件によって白色に近い色調に見えることもあり、灰色に近い色調に見えることもある。ここで、第１硬質相５ａはＴｉＣＮからなる黒色粒子であるがＣｏやＮｉを含有していても良い。また、第１硬質相５ａの外周には、灰白色の第２硬質相５ｂからなる周辺部が存在した有芯構造をなしていてもよい。 Here, as is apparent from the scanning electron micrograph of FIG. 2, the first hard phase 5a is observed as black particles, and the second hard phase 5b is grayish white particles, or a grayish white periphery around the white core. It is observed as a particle having a cored structure with a part. The grayish white color may appear to be a color tone close to white or may be a color tone close to gray depending on the conditions of photography. Here, the first hard phase 5a is black particles made of TiCN, but may contain Co or Ni. Further, the outer periphery of the first hard phase 5a may have a cored structure in which a peripheral portion made of the grayish white second hard phase 5b exists.
なお、断面組織観察にて、Ａ領域１１における第１硬質相５ａの面積比率をＳ１Ａ、第２硬質相５ｂの面積比率をＳ２Ａ、Ｂ領域における第１硬質相５ａの面積比率をＳ１Ｂ、第２硬質相５ｂの面積比率をＳ２Ｂとしたとき、Ｓ１ＡとＳ２Ａとの比率（Ｓ２Ａ／Ｓ１Ａ）が２〜８であり、Ｓ１ＢとＳ２Ｂとの比率（Ｓ２Ｂ／Ｓ１Ｂ）が０．５〜１．５であることが、切削性能を高くかつ変形を小さく抑制できる点で望ましい。 In cross-sectional structure observation, the area ratio of the first hard phase 5a in the A region 11 is S 1A , the area ratio of the second hard phase 5b is S 2A , and the area ratio of the first hard phase 5a in the B region is S 1B. when the area ratio of the second hard phase 5b was S 2B, the ratio of S 1A and S 2A (S 2A / S 1A ) is 2 to 8, the ratio of S 1B and S 2B (S 2B / S 1B ) is preferably from 0.5 to 1.5 in terms of high cutting performance and small deformation.
なお、切削工具１に含有される硬質相５をなすＴｉを主成分とする周期表第４、５および６族金属の窒化物または炭窒化物の合計含有比率は、サーメット全体で見て８０〜９０質量％であることが望ましく、一方、結合相６の含有比率は、サーメット全体で見て１０〜２０質量％であることによって、サーメットの硬度および靭性のバランスに優れたものとなる。そして、第１サーメット２においては、焼成における寸法変化の抑制の点で、硬質相の含有比率が９０〜９５質量％、結合相の含有比率が５〜１０質量％であることが望ましい。また、第２サーメット３においては、耐摩耗性の維持の点で、硬質相５の含有比率が７５〜８５質量％、結合相６の含有比率が１５〜２５質量％であることが望ましい。さらに、結合相６としては、鉄族金属の総量に対してＣｏを６５質量％以上含有することが切削工具１の耐熱衝撃性を高めるために望ましい。なお、サーメットの焼肌面が平滑な面となるようにサーメットの良好な焼結性を維持するためには、鉄族金属としてＮｉを５〜５０質量％、特に１０〜３５質量％の割合で含有せしめることが望ましい。 In addition, the total content of the nitrides or carbonitrides of the periodic table groups 4, 5, and 6 metal mainly composed of Ti forming the hard phase 5 contained in the cutting tool 1 is 80 to 80 in the whole cermet. On the other hand, the content ratio of the binder phase 6 is preferably 10 to 20% by mass in the whole cermet, so that the balance of hardness and toughness of the cermet is excellent. And in the 1st cermet 2, it is desirable that the content rate of a hard phase is 90-95 mass% and the content rate of a binder phase is 5-10 mass% from the point of suppression of the dimensional change in baking. Moreover, in the 2nd cermet 3, it is desirable that the content rate of the hard phase 5 is 75-85 mass% and the content rate of the binder phase 6 is 15-25 mass% from the point of maintenance of abrasion resistance. Furthermore, it is desirable that the binder phase 6 contains 65 mass% or more of Co with respect to the total amount of the iron group metal in order to improve the thermal shock resistance of the cutting tool 1. In addition, in order to maintain the favorable sinterability of the cermet so that the burned skin surface of the cermet becomes a smooth surface, Ni is contained in an amount of 5 to 50% by mass, particularly 10 to 35% by mass as an iron group metal. It is desirable to make it contain.
ここで、第２サーメット３の厚みはサーメット全体の厚みに対して１０〜３５％であることが望ましい。なお、第２サーメット３が上下層の両方存在する場合には、第２サーメット３の総厚みはサーメット全体の厚みに対して２０〜７０％となる。このとき、Ａ領域１１はすくい面８から５〜１００μｍの厚みで存在することが、切削性能が高くかつ変形が小さい切削工具１が製造上容易に作製できる点で望ましい。 Here, the thickness of the second cermet 3 is desirably 10 to 35% with respect to the thickness of the entire cermet. In addition, when the 2nd cermet 3 exists in both upper and lower layers, the total thickness of the 2nd cermet 3 will be 20 to 70% with respect to the thickness of the whole cermet. At this time, it is desirable that the A region 11 exists in a thickness of 5 to 100 μm from the rake face 8 in that the cutting tool 1 having high cutting performance and small deformation can be easily manufactured.
また、第２サーメット３には、表面側に、硬質相５中の第２硬質相５ｂ存在割合が多く、かつ結合相６の存在割合が少ない表面領域３Ｘが存在する構成、すなわち、Ａ領域１１とＢ領域１２との間に、Ｂ領域１２よりも第２硬質相４ｂの存在割合が少なく、かつＡ領域１１よりも結合相７の存在割合が多いＣ領域１３が存在することによって、切削性能をさらに高めることができる点で望ましい。
The second cermet 3, on the surface side, constituting the second hard phase 5b presence ratio of hard phase 5 is large, and the existing ratio is less surface area 3X binder phase 6 is present, ie, A region 11 Between the B region 12 and the B region 12, there is a C region 13 in which the second hard phase 4 b is less present than the B region 12, and the binder phase 7 is present more than the A region 11. Is desirable in that it can be further increased.
さらに、第１サーメット２の硬度が第２サーメット３の硬度より高く、かつ第２サーメット３の表面領域３Ｘの硬度が第２サーメット３の基体側３Ｙの硬度よりも高い構成、すなわち、Ａ領域１１の硬度がＣ領域１３の硬度より高く、かつＢ領域１２の硬度がＣ領域１３の硬度よりも高いことが、変形を防止できるとともに切刃７の耐摩耗性を高めることができる点で望ましい。 Furthermore, the hardness of the first cermet 2 is higher than the hardness of the second cermet 3 and the hardness of the surface region 3X of the second cermet 3 is higher than the hardness of the substrate side 3Y of the second cermet 3, that is, the A region 11 It is desirable that the hardness of the cutting region 7 is higher than the hardness of the C region 13 and the hardness of the B region 12 is higher than the hardness of the C region 13 in that deformation can be prevented and the wear resistance of the cutting edge 7 can be improved.
また、第１サーメット２における硬質相５の平均粒径が第２サーメット３における硬質相５の平均粒径より大きく、かつ第２サーメット３の表面領域３Ｘにおける硬質相５の平均粒径が第２サーメットの基体側３Ｙにおける硬質相５の平均粒径よりも大きい構成、すなわち、Ａ領域１１における硬質相５の平均粒径がＣ領域１３における硬質相５の平均粒径より大きく、かつＢ領域１２における硬質相５の平均粒径がＣ領域１３における硬質相５の平均粒径よりも大きいことが、組織の制御が容易な点で望ましい。 The average particle size of the hard phase 5 in the first cermet 2 is larger than the average particle size of the hard phase 5 in the second cermet 3, and the average particle size of the hard phase 5 in the surface region 3X of the second cermet 3 is the second. A structure larger than the average particle diameter of the hard phase 5 on the substrate side 3Y of the cermet, that is, the average particle diameter of the hard phase 5 in the A region 11 is larger than the average particle diameter of the hard phase 5 in the C region 13, and the B region 12 It is desirable that the average particle size of the hard phase 5 in is larger than the average particle size of the hard phase 5 in the C region 13 in terms of easy control of the structure.
なお、上記切削工具１は、下記製造方法にて作製することから、第１サーメット２と第２サーメット３との境界に界面が存在し、かつ第２サーメットの表面領域３Ｘと基体側３Ｙとの境界には界面が存在しない構成、すなわちＡ領域１１とＣ領域１３との境界に界面が存在せず、かつＢ領域１２とＣ領域１３との境界には界面が存在する構成となる。 In addition, since the said cutting tool 1 is produced with the following manufacturing method, an interface exists in the boundary of the 1st cermet 2 and the 2nd cermet 3, and the surface area | region 3X of 2nd cermet and base | substrate side 3Y There is a configuration in which no interface exists at the boundary, that is, there is no interface at the boundary between the A region 11 and the C region 13, and there is a configuration in which an interface exists at the boundary between the B region 12 and the C region 13.
（製造方法）
次に、上述したサーメット焼結体からなる切削工具の製造方法について説明する。
原料として、２種類の混合原料粉末を準備する。
第２の混合原料粉末は低温で焼結する組成からなり、具体的には、平均粒径０．６〜１．０μｍ、望ましくは０．８〜１．０μｍのＴｉＣＮ粉末と、平均粒径０．１〜２μｍの上述した他の周期表第４、５および６族金属の炭化物粉末、窒化物粉末または炭窒化物粉末のいずれか１種と、平均粒径１．０〜３．０μｍのＣｏ粉末と平均粒径０．３〜０．８μｍのＮｉ粉末との少なくとも１種と、所望により平均粒径０．５〜１０μｍのＭｎＣＯ３粉末を混合した混合粉末とする。
(Production method)
Next, the manufacturing method of the cutting tool which consists of a cermet sintered compact mentioned above is demonstrated.
Two kinds of mixed raw material powders are prepared as raw materials.
The second mixed raw material powder is composed of a composition sintered at a low temperature. Specifically, the TiCN powder having an average particle diameter of 0.6 to 1.0 μm, desirably 0.8 to 1.0 μm, and an average particle diameter of 0 Any one of carbide powder, nitride powder, or carbonitride powder of Group 4, 5, and 6 metals of the above-mentioned other periodic table of 1-2 μm described above, and Co having an average particle diameter of 1.0-3.0 μm A mixed powder in which at least one of powder and Ni powder having an average particle size of 0.3 to 0.8 μm and, if desired, MnCO 3 powder having an average particle size of 0.5 to 10 μm are mixed.
一方、第１の原料粉末は第１の混合粉末よりも焼成温度の高い組成からなり、平均粒径１．０〜２．０μｍ、望ましくは１．１〜１．５μｍのＴｉＣＮ粉末と、平均粒径０．１〜２μｍの上述した他の周期表第４、５および６族金属の炭化物粉末、窒化物粉末または炭窒化物粉末のいずれか１種と、平均粒径１．０〜３．０μｍのＣｏ粉末と平均粒径０．３〜０．８μｍのＮｉ粉末との少なくとも１種と、所望により平均粒径０．５〜１０μｍのＭｎＣＯ３粉末を混合した混合粉末とする。 On the other hand, the first raw material powder has a composition having a higher firing temperature than the first mixed powder, and has an average particle size of 1.0 to 2.0 μm, preferably 1.1 to 1.5 μm, and an average particle size. Any one of carbide powders, nitride powders or carbonitride powders of other Group 4, 5 and 6 metals of the above-mentioned periodic table having a diameter of 0.1 to 2 μm and an average particle diameter of 1.0 to 3.0 μm A mixed powder in which at least one of Co powder and Ni powder having an average particle size of 0.3 to 0.8 μm and optionally MnCO 3 powder having an average particle size of 0.5 to 10 μm are mixed.
ここで、前記第２の混合原料の鉄族金属含有量が前記第１の混合原料の鉄族金属含有量よりも多いか、または前記第２の混合原料の平均粒径が前記第１の混合原料の平均粒径よりも小さいことが望ましい。 Here, the iron group metal content of the second mixed material is larger than the iron group metal content of the first mixed material, or the average particle size of the second mixed material is the first mixed material. It is desirable that it is smaller than the average particle diameter of the raw material.
なお、上記第１および第２の原料中にＴｉＣ粉末やＴｉＮ粉末を添加することもあるが、これらの原料粉末は焼成後のサーメットにおいてＴｉＣＮを構成する。 In addition, although TiC powder and TiN powder may be added to the first and second raw materials, these raw material powders constitute TiCN in the cermet after firing.
次に、上記異なる２種類の混合原料を用いて切削工具形状に成形する。成形方法としては、プレス金型の中に、第２の混合原料を上面、下面、または上下面に配置するとともに、中央部に第１の混合粉末を配置して積層した状態でプレス成形する方法が好適である。その他に、第２の原料粉末のみを用いてプレス成形した成形体の表面に第１の原料粉末を含むスラリーを塗布する方法も挙げられるが、切削工具の切刃における寸法精度を高めるとともに切刃における焼結体の密度を高めるためには、両粉末を積層した状態でプレス成形する方法が好適である。 Next, it shape | molds in the shape of a cutting tool using the said two different types of mixed raw materials. As a forming method, the second mixed raw material is disposed on the upper surface, the lower surface, or the upper and lower surfaces in the press mold, and the first mixed powder is disposed in the center portion and press-molded in a laminated state. Is preferred. In addition, there is a method of applying the slurry containing the first raw material powder to the surface of the compact that is press-molded using only the second raw material powder. In order to increase the density of the sintered body, the method of press molding in a state where both powders are laminated is suitable.
第１の混合粉末の上／下面に第２の混合粉末を配置する方法としては、第１の混合粉末を充填して平らに均した後、第２の混合粉末を投入する方法や、第１の混合粉末を投入して上パンチを降下させて低圧で一旦仮成形し、その後、上パンチを上昇させて第２の混合粉末を投入し、再度、上パンチを降下させて仮成形することを繰り返し、最後に所定圧力で成形する方法が好適に採用できる。 As a method of arranging the second mixed powder on the top / bottom surface of the first mixed powder, the first mixed powder is filled and leveled, and then the second mixed powder is added. And then lowering the upper punch and temporarily forming at low pressure, then raising the upper punch and charging the second mixed powder, and again lowering the upper punch and temporarily forming. It is possible to preferably employ a method of molding at a predetermined pressure repeatedly and finally.
その後、上記成形体を焼成することにより、上述した所定組織のサーメットを作製することができる。具体的な焼成条件の一例としては、
（ａ）１０５０〜１２５０℃まで昇温し、
（ｂ）窒素（Ｎ２）等の不活性ガスを３０〜２０００Ｐａ充填した雰囲気で０．１〜２℃／分の昇温速度で１３００〜１４５０℃まで昇温し、
（ｃ）真空雰囲気で３〜１５℃／分の昇温速度で１５２０〜１６００℃まで昇温するとともに、真空雰囲気のまま、または不活性ガスを充填した雰囲気で０．５〜２時間維持し、
（ｄ）６〜１５℃／分の冷却速度で冷却する工程にて焼成する。なお、焼成温度が１５２０℃より低いと、サーメット焼結体の全体として変形はしないがサーメットの表面に焼結が進行してできる複合炭窒化物固溶体である第２硬質相の存在比率が高いＡ領域が形成されずに、サーメット焼結体の表面における耐摩耗性が低下する。
Then, the cermet of the predetermined structure | tissue mentioned above can be produced by baking the said molded object. As an example of specific firing conditions,
(A) The temperature is raised to 1050 to 1250 ° C.
(B) In an atmosphere filled with an inert gas such as nitrogen (N 2 ) of 30 to 2000 Pa, the temperature is increased to 1300 to 1450 ° C. at a temperature increase rate of 0.1 to 2 ° C./min,
(C) While raising the temperature to 1520 to 1600 ° C. at a temperature increase rate of 3 to 15 ° C./min in a vacuum atmosphere, maintaining the vacuum atmosphere or an atmosphere filled with an inert gas for 0.5 to 2 hours,
(D) Firing is performed at a cooling rate of 6 to 15 ° C./min. When the firing temperature is lower than 1520 ° C., the cermet sintered body is not deformed as a whole, but the abundance ratio of the second hard phase that is a composite carbonitride solid solution formed by sintering on the surface of the cermet is high. The area is not formed, and the wear resistance on the surface of the cermet sintered body is lowered.
そして、所望により、サーメットの表面に被覆層を成膜する。被覆層の成膜方法として、イオンプレーティング法やスパッタリング法等の物理蒸着（ＰＶＤ）法が好適に適応可能である。 Then, if desired, a coating layer is formed on the surface of the cermet. A physical vapor deposition (PVD) method such as an ion plating method or a sputtering method can be suitably applied as the coating layer forming method.
マイクロトラック法による測定で平均粒径（ｄ５０値）が２．０μｍのＴｉＣＮ粉末、平均粒径１．１μｍで表１のＣ量のＷＣ粉末、平均粒径１．５μｍのＴｉＮ粉末、平均粒径２μｍのＴａＣ粉末、平均粒径１．５μｍのＮｂＣ粉末、平均粒径１．８μｍのＺｒＣ粉末、平均粒径１．０μｍのＶＣ粉末、平均粒径２．４μｍのＮｉ粉末、および平均粒径１．９μｍのＣｏ粉末を用いて、表１に示す割合で調製した第１の混合粉末をステンレス製ボールミルと超硬ボールを用いて、イソプロピルアルコール（ＩＰＡ）を添加して湿式混合し、パラフィンを３質量％添加、混合した後、スプレードライヤにて顆粒とした。 TiCN powder having an average particle diameter (d 50 value) of 2.0 μm as measured by the microtrack method, WC powder having an average particle diameter of 1.1 μm and the amount of C shown in Table 1, TiN powder having an average particle diameter of 1.5 μm, an average particle TaC powder having a diameter of 2 μm, NbC powder having an average particle diameter of 1.5 μm, ZrC powder having an average particle diameter of 1.8 μm, VC powder having an average particle diameter of 1.0 μm, Ni powder having an average particle diameter of 2.4 μm, and an average particle diameter Using a 1.9 μm Co powder, the first mixed powder prepared in the ratio shown in Table 1 was wet-mixed using a stainless steel ball mill and a carbide ball to which isopropyl alcohol (IPA) was added, and paraffin was added. After adding 3% by mass and mixing, it was granulated with a spray dryer.
同様に、上記原料粉末を用いて表１に示す第２の混合原料粉末を調製し、バインダを混合して、スプレードライヤにて第２の混合粉末の顆粒を作製した。 Similarly, the 2nd mixed raw material powder shown in Table 1 was prepared using the said raw material powder, the binder was mixed, and the granule of the 2nd mixed powder was produced with the spray dryer.
そして、この成形用の混合粉末を用いて、金型のうすの中に第２の混合粉末を投入して平らに均して上パンチを降下させて手押しで仮成形した後、上パンチを上昇させ、この仮成形した粉末の上に第１の混合粉末を投入して平らに均し、上記同様に仮成形を行い、さらにこの製粒した粉末の上に第２の混合粉末を投入して平らに均し、最後に上パンチを降下させて２００ＭＰａで加圧してＳＥＫＲ１２０３ＡＦＥＮ（チップ厚み３．１８ｍｍ）の工具形状にプレス成形した。 Then, using this mixed powder for molding, the second mixed powder is put into the mold mold, leveled flat, the upper punch is lowered and temporarily formed by hand, and then the upper punch is raised. Then, the first mixed powder is put on the temporarily formed powder and leveled flatly, the temporary mixture is formed in the same manner as described above, and the second mixed powder is put on the granulated powder. It was leveled flat, and finally the upper punch was lowered and pressed at 200 MPa to press-mold into a tool shape of SEKR1203AFEN (chip thickness 3.18 mm).
さらに、この成形体を焼成炉に投入して、（ａ）１０℃／分の昇温速度で１２００℃まで昇温し、（ｂ）窒素（Ｎ２）を１０００Ｐａ充填した雰囲気で０．５℃／分の昇温速度で１４００℃まで昇温し、（ｃ）真空雰囲気で７℃／分の昇温速度で表２に示す温度まで昇温するとともに、その状態で１時間維持し、（ｄ）１０℃／分の冷却速度で冷却する工程にて焼成する焼成条件で焼成した。 Furthermore, this molded body was put into a firing furnace, (a) heated to 1200 ° C. at a heating rate of 10 ° C./min, (b) 0.5 ° C. in an atmosphere filled with 1000 Pa of nitrogen (N 2 ). (C) The temperature was raised to 1400 ° C. at a rate of temperature rise / minute, (c) the temperature was raised to a temperature shown in Table 2 at a rate of temperature rise of 7 ° C./min in a vacuum atmosphere, and maintained in that state for 1 hour, (d ) It baked on the baking conditions baked in the process cooled at the cooling rate of 10 degree-C / min.
得られたサーメットについて、走査型電子顕微鏡（ＳＥＭ）観察を行い、１００００倍の写真にて、表面および内部のそれぞれ任意５箇所について市販の画像解析ソフトを用いて８μｍ×８μｍの領域で画像解析を行い、硬質相の存在状態、表面領域の存在を確認するとともにこれらの面積比率を算出した。結果は表２に示した。 The obtained cermet was observed with a scanning electron microscope (SEM), and image analysis was performed in a region of 8 μm × 8 μm using a commercially available image analysis software for each of the surface and the interior at a 10000 × magnification. And the presence of the hard phase and the presence of the surface region were confirmed, and the area ratios were calculated. The results are shown in Table 2.
次に、得られたサーメット製の切削工具を用いて以下の切削条件にて切削試験を行った。また、金属顕微鏡を用いてサーメットの側面（逃げ面）形状をトレースし、側面の中央部における膨らみ量を算出した。結果は表３に併記した。
被削材：Ｓ４５Ｃ
切削速度：１８０ｍ／分
送り：０．１５ ｍｍ／刃
切込み：１．５ｍｍ
切削状態：湿式（水溶性切削液使用）
評価方法：摩耗量が０．２ｍｍに達するまでの時間
Next, the cutting test was done on the following cutting conditions using the obtained cermet cutting tool. Moreover, the side surface (flank) shape of the cermet was traced using the metal microscope, and the bulge amount in the center part of the side surface was calculated. The results are also shown in Table 3.
Work material: S45C
Cutting speed: 180 m / min Feed: 0.15 mm / blade cutting: 1.5 mm
Cutting condition: wet (use water-soluble cutting fluid)
Evaluation method: Time until the wear amount reaches 0.2 mm
表１〜３より、第１サーメットの結合相量が第２サーメットの結合相量より多い試料Ｎｏ．５では、焼結体の変形量が大きくて工具本体への装着にがたつきが発生した。また、第２サーメットの結合相量が第１サーメットの結合相量よりも少ない試料Ｎｏ．６では、切削加工中にチッピングが発生した。さらに、焼成温度が１５２０℃よりも低く表面の硬質相中の第２硬質相の存在割合が内部より少ない試料Ｎｏ．７では、切削評価において摩耗量が大きいものであった。さらには、第１サーメットが過焼結した試料Ｎｏ．８では変形量が大きくなった。
From Table 1-3, sample binder phase of the first cermet is greater than the binder phase of the second cermet No. In No. 5, the amount of deformation of the sintered body was large, and rattling occurred on the tool body. Further, the sample No. 2 in which the amount of the binder phase of the second cermet is smaller than the amount of the binder phase of the first cermet. In No. 6 , chipping occurred during the cutting process. Further, the sample presence ratio of the second hard phase of the hard phase in the lower surface than the firing temperature is 1520 ° C. is less than the internal No. In No. 7, the amount of wear was large in the cutting evaluation. Furthermore, sample No. 1 in which the first cermet was oversintered. In 8, the amount of deformation increased.
これに対し、本発明の範囲内の組織となったサーメットからなる試料Ｎｏ．１〜４では、優れた耐摩耗性を発揮するとともに耐欠損性も良好であり、工具寿命が長いものであった。 On the other hand, Sample No. consisting of cermet having a structure within the scope of the present invention. Nos. 1 to 4 exhibited excellent wear resistance, good fracture resistance, and long tool life.
１ 工具
２ 第１サーメット
３ 第２サーメット
３Ｘ 第２サーメットの表面領域
３Ｙ 第２サーメットの基体側
５ 硬質相
５ａ 第１硬質相
５ｂ 第２硬質相
６ 結合相
７ 切刃
８ すくい面
９ 逃げ面
１０ 内部
１１ Ａ領域
１２ Ｂ領域
１３ Ｃ領域
１４ ネジ穴
DESCRIPTION OF SYMBOLS 1 Tool 2 1st cermet 3 2nd cermet 3X Surface area | region 3Y of 2nd cermet The base | substrate side 5 of 2nd cermet 5 Hard phase 5a 1st hard phase 5b 2nd hard phase 6 Bonding phase 7 Cutting edge 8 Rake face 9 Flank 10 Inside 11 A region 12 B region 13 C region 14 Screw hole
Claims (13)
前記第１サーメットおよび前記第２サーメットは、周期表第４、５および６族金属のうちの１種以上の炭化物、窒化物、炭窒化物およびこれらの固溶体の中から選ばれた１種以上からなる硬質相と、主として鉄族金属からなる結合相とから構成され、前記硬質相は、ＴｉＣＮを主成分とする第１硬質相と、周期表第４、５および６族金属の少なくとも1種と
Ｔｉとの複合炭窒化物固溶体の第２硬質相とからなり、
前記第２サーメットは前記第１サーメットよりも前記硬質相中の前記第２硬質相の存在割合が多く、前記第１サーメットは前記第２サーメットよりも前記結合相の存在割合が少ないサーメット焼結体。 A first cermet and a second cermet disposed on the surface of the first cermet and constituting at least a cutting blade are laminated,
The first cermet and the second cermet may be one or more selected from one or more carbides, nitrides, carbonitrides, and solid solutions of the metals in Groups 4, 5, and 6 of the periodic table. The hard phase is composed of a first hard phase mainly composed of TiCN and at least one of Group 4, 5 and 6 metals of the periodic table. Comprising a second hard phase of a composite carbonitride solid solution with Ti,
Said second cermet existence ratio of the second hard phase of the hard phase than said first cermet many, the first cermet existing ratio is less cermet sintered the binder phase than the second cermet .
れらの固溶体の中から選ばれた１種以上からなる硬質相と、主として鉄族金属からなる結合相との焼結体から構成され、前記硬質相は、ＴｉＣＮを主成分とする第１硬質相と、周期表第４、５および６族金属の少なくとも1種とＴｉとの複合炭窒化物固溶体の第２硬質
相とからなり、
切刃を含むすくい面およびその近傍領域をＡ領域とし、該Ａ領域以外の領域である前記焼結体の内部および逃げ面の中央部位をＢ領域としたとき、前記Ａ領域では前記Ｂ領域よりも前記硬質相中の前記第２硬質相の存在割合が多く、前記Ｂ領域では前記Ａ領域よりも前記結合相の存在割合が少ない切削工具。 A hard phase composed of one or more carbides, nitrides, carbonitrides, and solid solutions thereof selected from Group 4, 5, and 6 metals of the periodic table, and mainly composed of an iron group metal. It is composed of a sintered body with a binder phase, and the hard phase is a composite carbonitride of Ti with a first hard phase mainly composed of TiCN, at least one of Group 4, 5, and 6 metals of the periodic table and Ti. Consisting of a second hard phase of solid solution,
When the rake face including the cutting edge and the vicinity region thereof are defined as A region, and the inside of the sintered body and the central portion of the flank which are regions other than the A region are defined as B region, the A region is more than the B region. the existence ratio of the second hard phase is large, it said a region cutting tool abundance ratio of the binder phase is less than the B region of the hard phase also.
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