JP4788892B2 - Manufacturing method of surface-coated cermet cutting tool that exhibits excellent chipping resistance in high-speed cutting of difficult-to-cut materials - Google Patents

Manufacturing method of surface-coated cermet cutting tool that exhibits excellent chipping resistance in high-speed cutting of difficult-to-cut materials Download PDF

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JP4788892B2
JP4788892B2 JP2006015191A JP2006015191A JP4788892B2 JP 4788892 B2 JP4788892 B2 JP 4788892B2 JP 2006015191 A JP2006015191 A JP 2006015191A JP 2006015191 A JP2006015191 A JP 2006015191A JP 4788892 B2 JP4788892 B2 JP 4788892B2
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西田  真
文雄 対馬
斉 功刀
剛 石井
亨 長谷川
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Mitsubishi Materials Corp
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この発明は、自身が高い粘性を有し、かつ切削時の切削工具表面部の硬質被覆層に対する粘着性も高く、この結果切削抵抗のきわめて高いものとなる軟鋼やステンレス鋼、さらに高マンガン鋼などの難削材の高速切削加工で、硬質被覆層がすぐれた耐チッピング性を示し、長期に亘ってすぐれた耐摩耗性を発揮する表面被覆サーメット製切削工具(以下、被覆サーメット工具という)の製造方法に関するものである。 This invention has a high viscosity and high adhesion to the hard coating layer on the surface of the cutting tool during cutting. As a result, soft steel, stainless steel, and high manganese steel that have extremely high cutting resistance. in high-speed cutting of difficult-to-cut materials, shows the chipping resistance of the hard coating layer has excellent, manufacture of surface-coated cermet cutting tool which exhibits excellent wear resistance over a long period (hereinafter, referred to as coated cermet tools) It is about the method .

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)基サーメットで構成された基体(以下、これらを総称して工具基体という)の表面に、
(1)下部層が、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)層のうちの1層または2層以上からなり、かつ3〜20μmの合計平均層厚を有するTi化合物層、
(2)上部層が、化学蒸着した状態でα型の結晶構造を有し、電界放出型走査電子顕微鏡を用い、図2に概略説明図で示される通り、上記工具基体表面と平行な研磨面の測定範囲内に存在する六方晶結晶格子を有する結晶粒個々に電子線を照射して、前記研磨面の法線に対して、前記結晶粒の結晶面である(0001)面の法線がなす傾斜角を測定し、前記測定傾斜角のうち、0〜45度の範囲内にある測定傾斜角を0.25度のピッチ毎に区分すると共に、各区分内に存在する度数を集計してなる傾斜角度数分布グラフにおいて、図4に例示される通り、0〜15度の範囲内の傾斜角区分に最高ピークが存在すると共に、前記0〜15度の範囲内に存在する度数の合計が、傾斜角度数分布グラフにおける度数全体の50%以上の割合を占める傾斜角度数分布グラフを示し、かつ1.5〜6μmの平均層厚を有する酸化アルミニウム層(以下、改質α型Al23層という)、
以上(1)および(2)で構成された硬質被覆層を蒸着形成してなる被覆サーメット工具が知られており、この被覆サーメット工具は、上記改質α型Al23層がα型Al23自身のもつすぐれた高温硬さおよび耐熱性に加えて、すぐれた高温強度を具備することから、例えば各種の一般鋼や普通鋳鉄などの高速切削加工などに用いた場合にも、すぐれた耐チッピング性を発揮し、長期に亘ってすぐれた切削性能を発揮することも知られている。
Conventionally, generally on the surface of a substrate (hereinafter collectively referred to as a tool substrate) composed of a tungsten carbide (hereinafter referred to as WC) -based cemented carbide or titanium carbonitride (hereinafter referred to as TiCN) -based cermet. ,
(1) The lower layer is a Ti carbide (hereinafter referred to as TiC) layer, a nitride (hereinafter also referred to as TiN) layer, a carbonitride (hereinafter referred to as TiCN) layer, a carbon oxide (hereinafter referred to as TiCO). A Ti compound layer having a total average layer thickness of 3 to 20 μm, including one or two or more of a layer and a carbonitride oxide (hereinafter referred to as TiCNO) layer,
(2) The upper layer has an α-type crystal structure in the state of chemical vapor deposition, and using a field emission scanning electron microscope, as shown schematically in FIG. 2, is a polished surface parallel to the tool base surface. Each of the crystal grains having a hexagonal crystal lattice existing within the measurement range is irradiated with an electron beam, and the normal line of the (0001) plane that is the crystal plane of the crystal grain is relative to the normal line of the polished surface. Measure the inclination angle to be made, divide the measurement inclination angle within the range of 0-45 degrees out of the measurement inclination angle for each pitch of 0.25 degree, and totalize the frequency existing in each division In the inclination angle number distribution graph, as shown in FIG. 4, the highest peak exists in the inclination angle section in the range of 0 to 15 degrees, and the sum of the frequencies existing in the range of 0 to 15 degrees is as follows. , Accounting for 50% or more of the total frequency in the slope angle distribution graph It shows an inclination angle frequency distribution graph, and an aluminum oxide layer having an average layer thickness of 1.5~6Myuemu (hereinafter, referred to as modified α type the Al 2 O 3 layer),
There is known a coated cermet tool formed by vapor-depositing a hard coating layer composed of the above (1) and (2), and the modified α-type Al 2 O 3 layer is an α-type Al. 2 O 3 itself has excellent high-temperature hardness and heat resistance, as well as excellent high-temperature strength, so it is excellent even when used for high-speed cutting such as various general steels and ordinary cast iron. It is also known to exhibit excellent chipping resistance and excellent cutting performance over a long period of time.

また、一般に、上記の被覆サーメット工具の硬質被覆層を構成する改質α型Al23層が、通常の化学蒸着装置を用い、
反応ガス組成:容量%で、AlCl3:1〜5%、CO2:0.1〜2%、HCl:0.3〜3%、H2S:0.5〜1%、Ar:20〜35%、H2:残り、
反応雰囲気温度:1050〜1100℃、
反応雰囲気圧力:6〜10kPa、
の条件で蒸着形成されることも知られている。
さらに、同じく硬質被覆層を構成するTi化合物層や改質α型Al23層が粒状結晶組織を有し、さらに、前記Ti化合物層を構成するTiCN層を、層自身の強度向上を目的として、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して縦長成長結晶組織をもつようにすることも知られている。
特開2005−205586号公報 特開平6−8010号公報
In general, the modified α-type Al 2 O 3 layer constituting the hard coating layer of the above-mentioned coated cermet tool uses a normal chemical vapor deposition apparatus,
Reaction gas composition: by volume%, AlCl 3: 1~5%, CO 2: 0.1~2%, HCl: 0.3~3%, H 2 S: 0.5~1%, Ar: 20~ 35%, H 2 : remaining,
Reaction atmosphere temperature: 1050 to 1100 ° C.
Reaction atmosphere pressure: 6 to 10 kPa,
It is also known that vapor deposition is performed under the following conditions.
Furthermore, the Ti compound layer and the modified α-type Al 2 O 3 layer that also constitute the hard coating layer have a granular crystal structure, and the TiCN layer that constitutes the Ti compound layer is intended to improve the strength of the layer itself. In a normal chemical vapor deposition apparatus, a gas mixture containing organic carbonitrides is used as a reaction gas, and it is formed by chemical vapor deposition at an intermediate temperature range of 700 to 950 ° C. so that it has a vertically grown crystal structure. It is also known to do.
JP-A-2005-205586 Japanese Patent Laid-Open No. 6-8010

近年の切削装置の高性能化はめざましく、一方で切削加工に対する省力化および省エネ化、さらに低コスト化の要求は強く、これに伴い、切削加工は一段と高速化の傾向にあるが、上記の従来被覆サーメット工具においては、これを低合金鋼や炭素鋼などの一般鋼、さらにねずみ鋳鉄などの普通鋳鉄の高速切削に用いた場合には問題はないが、特にこれを軟鋼やステンレス鋼、さらに高マンガン鋼などの難削材の高速切削加工に用いた場合には、前記難削材自身が高い粘性を有し、かつ切削時の切削工具表面部の硬質被覆層に対する粘着性も高く、この傾向は高速切削時に発生する高熱によって一段と増大することと相俟って、切削抵抗のきわめて高いものとなり、一方硬質被覆層を構成する改質α型Al23層の高温強度はこれに耐えるに十分なものではなく、この結果切刃部にチッピング(微少欠け)が発生し易くなり、これが原因で比較的短時間で使用寿命に至るのが現状である。 In recent years, the performance of cutting machines has been remarkable. On the other hand, there is a strong demand for labor saving, energy saving, and cost reduction for cutting work, and along with this, cutting work tends to be further accelerated. For coated cermet tools, there is no problem when used for high-speed cutting of general steel such as low alloy steel and carbon steel, and ordinary cast iron such as gray cast iron. When used for high-speed cutting of difficult-to-cut materials such as manganese steel, the difficult-to-cut material itself has a high viscosity, and the adhesiveness to the hard coating layer on the surface of the cutting tool during cutting is also high. Combined with a further increase due to high heat generated during high-speed cutting, the cutting resistance becomes extremely high, while the high-temperature strength of the modified α-type Al 2 O 3 layer constituting the hard coating layer can withstand this. This is not sufficient, and as a result, chipping (slight chipping) is likely to occur at the cutting edge, and this causes the service life to be reached in a relatively short time.

そこで、本発明者等は、上述のような観点から、上記の改質α型Al23層が硬質被覆層の上部層を構成する被覆サーメット工具に着目し、特に前記改質α型Al23層の耐チッピング性向上を図るべく研究を行った結果、
(a)上記の従来被覆サーメット工具の硬質被覆層を構成するTi化合物層(下部層)と改質α型Al23層(上部層)の間に、通常の化学蒸着装置を用い、
反応ガス組成:容量%で、AlCl3:1〜5%、CO2:3〜7%、HCl:0.3〜3%、H2S:0.02〜0.4%、H2:残り、
反応雰囲気温度:750〜900℃、
反応雰囲気圧力:20〜30kPa、
の条件で酸化アルミニウム(以下、Al23で示す)層を0.1〜1.9μmの平均層厚で形成すると、この結果形成されたAl23層は、同じくα型の結晶構造を有し、電界放出型走査電子顕微鏡を用い、図1(a),(b)に示される通り、同じく上記工具基体表面と平行な研磨面の測定範囲内に存在する六方晶結晶格子を有する結晶粒個々に電子線を照射して、前記研磨面の法線に対して、前記結晶粒の結晶面である(0001)面の法線がなす傾斜角を測定し、前記測定傾斜角のうち、45〜90度の範囲内にある測定傾斜角を0.25度のピッチ毎に区分すると共に、各区分内に存在する度数を集計してなる傾斜角度数分布グラフで現した場合、図3に例示される通り、傾斜角区分の特定位置にシャープな最高ピークが現れ、試験結果によれば、化学蒸着装置における反応雰囲気圧力を、上記の通り20〜30kPaの範囲内で変化させると、上記シャープな最高ピークの現れる位置が傾斜角区分の75〜90度の範囲内で変化すると共に、前記75〜90度の範囲内に存在する度数の合計が、傾斜角度数分布グラフにおける度数全体の50%以上の割合を占めるようになり、この結果の傾斜角度数分布グラフにおいて75〜90度の範囲内に傾斜角区分の最高ピークが現れるAl23層(以下、補強α型Al23層という)は、上記の改質α型Al23層(上部層)とTi化合物層(下部層)の間にあって、前記改質α型Al23層を十分に補強し、切削抵抗の高い上記の難削材の高速切削加工においても前記改質α型Al23層にチッピングが発生するのを一段と抑制し、耐摩耗性向上に寄与すること。
In view of the above, the present inventors focused on the coated cermet tool in which the modified α-type Al 2 O 3 layer constitutes the upper layer of the hard coating layer, and in particular, the modified α-type Al As a result of research to improve chipping resistance of 2 O 3 layer,
(A) Between the Ti compound layer (lower layer) and the modified α-type Al 2 O 3 layer (upper layer) constituting the hard coating layer of the conventional coated cermet tool, using a normal chemical vapor deposition apparatus,
Reaction gas composition: by volume%, AlCl 3: 1~5%, CO 2: 3~7%, HCl: 0.3~3%, H 2 S: 0.02~0.4%, H 2: remainder ,
Reaction atmosphere temperature: 750 to 900 ° C.
Reaction atmosphere pressure: 20-30 kPa,
When an aluminum oxide (hereinafter referred to as Al 2 O 3 ) layer is formed with an average layer thickness of 0.1 to 1.9 μm under the conditions of the above, the resulting Al 2 O 3 layer has the same α-type crystal structure. Using a field emission scanning electron microscope, as shown in FIGS. 1 (a) and 1 (b), it has a hexagonal crystal lattice that is also present in the measurement range of the polished surface parallel to the tool substrate surface. Each crystal grain is irradiated with an electron beam, an inclination angle formed by a normal line of the (0001) plane that is a crystal plane of the crystal grain is measured with respect to the normal line of the polished surface, When the measured inclination angle in the range of 45 to 90 degrees is divided into pitches of 0.25 degrees and the frequency existing in each of the divisions is represented by an inclination angle number distribution graph, FIG. As shown in Fig. 4, a sharp peak appears at a specific position in the tilt angle section, and According to the results, when the reaction atmosphere pressure in the chemical vapor deposition apparatus is changed within the range of 20 to 30 kPa as described above, the position where the sharpest peak appears changes within the range of 75 to 90 degrees of the inclination angle section. In addition, the sum of the frequencies existing within the range of 75 to 90 degrees occupies a ratio of 50% or more of the entire frequencies in the inclination angle distribution graph, and 75 to 75 in the inclination angle distribution graph as a result. An Al 2 O 3 layer (hereinafter referred to as a reinforced α-type Al 2 O 3 layer) in which the highest peak of the tilt angle section appears in the range of 90 degrees is referred to as the above-mentioned modified α-type Al 2 O 3 layer (upper layer). be between Ti compound layer (lower layer), the modified α type the Al 2 O 3 layer were sufficiently reinforced, the reforming α-type Al 2 O even at high cutting with high cutting resistance above hard-to-cut materials One step of chipping on 3 layers And to contribute to improved wear resistance.

(b)一方、上記の被覆サーメット工具の硬質被覆層の上部層を構成する改質α型Al23層は、相対的に蒸着表面が粗いのが現状である。そこで、前記改質α型Al23層の全面に、
(b−1)まず、下側層として、反応ガス組成を、体積%で、
TiCl4:0.2〜10%、
CO2:0.1〜10%、
Ar:5〜60%、
2:残り、
とし、かつ、
反応雰囲気温度:800〜1100℃、
反応雰囲気圧力:4〜70kPa(30〜525torr)、
とした条件で、0.1〜3μmの平均層厚を有し、かつ、オージェ分光分析装置で測定して、Tiに対する酸素の割合が原子比で1.25〜1.90、即ち、
組成式:TiOW
で表わした場合、
W:原子比で1.25〜1.90、
を満足する酸化チタン層を形成し、
(b−2)ついで、上記酸化チタン層(下側層)の上に、上側層として、通常の条件、即ち、反応ガス組成を、体積%で、
TiCl4:0.2〜10%、
2:4〜60%、
2:残り、
とし、かつ、
反応雰囲気温度:800〜1100℃、
反応雰囲気圧力:4〜90kPa(30〜675torr)、
とした条件で、0.05〜2μmの平均層厚を有するTiN層を形成すると、
(b−3)上記TiN層(上側層)形成時に、上記下側層を構成する酸化チタン層の酸素が拡散してきて前記上側層(TiN層)が、窒酸化チタン層で構成されるようになるが、この場合上記上側層(前記窒酸化チタン層)形成後の上記下側層である酸化チタン層は、厚さ方向中央部をオージェ分光分析装置で測定して、酸素の割合がTiに対する原子比で1.2〜1.7、即ち、
組成式:TiOX
で表わした場合、
X:原子比で1.2〜1.7、
を満足する酸化チタン層となり、
(b−4)また、上記窒酸化チタン層で構成された上側層は、同じく厚さ方向中央部をオージェ分光分析装置で測定して、拡散酸素の割合が窒素(N)に対する原子比で0.01〜0.4、即ち、
組成式:TiN1-Y(O)Y
で表わした場合(ただし、(O)は上側層の蒸着形成時における上記下側層である酸化チタン層からの拡散酸素を示す)、
Y:原子比で0.01〜0.4、
を満足する窒酸化チタン層となること。
(B) On the other hand, the modified α-type Al 2 O 3 layer constituting the upper layer of the hard coating layer of the above-described coated cermet tool has a relatively rough deposition surface. Therefore, on the entire surface of the modified α-type Al 2 O 3 layer,
(B-1) First, as the lower layer, the reaction gas composition is in volume%,
TiCl 4 : 0.2 to 10%,
CO 2 : 0.1 to 10%,
Ar: 5 to 60%,
H 2 : Remaining
And
Reaction atmosphere temperature: 800-1100 ° C.
Reaction atmosphere pressure: 4 to 70 kPa (30 to 525 torr),
And having an average layer thickness of 0.1 to 3 μm and a ratio of oxygen to Ti of 1.25 to 1.90 as measured by an Auger spectrometer,
Composition formula: TiO W ,
In the case of
W: 1.25 to 1.90 in atomic ratio,
Forming a titanium oxide layer that satisfies
(B-2) Next, on the titanium oxide layer (lower layer), as an upper layer, the normal conditions, that is, the reaction gas composition in volume%,
TiCl 4 : 0.2 to 10%,
N 2 : 4-60%,
H 2 : Remaining
And
Reaction atmosphere temperature: 800-1100 ° C.
Reaction atmosphere pressure: 4 to 90 kPa (30 to 675 torr),
When a TiN layer having an average layer thickness of 0.05 to 2 μm is formed under the conditions described above,
(B-3) When forming the TiN layer (upper layer), oxygen in the titanium oxide layer constituting the lower layer is diffused so that the upper layer (TiN layer) is composed of a titanium nitride oxide layer. In this case, the titanium oxide layer, which is the lower layer after the formation of the upper layer (the titanium oxynitride layer), is measured by an Auger spectroscopic analyzer at the center in the thickness direction. 1.2 to 1.7 in atomic ratio,
Composition formula: TiO x ,
In the case of
X: 1.2 to 1.7 in atomic ratio,
Titanium oxide layer that satisfies
(B-4) Further, the upper layer composed of the above titanium oxynitride layer was also measured at the center in the thickness direction with an Auger spectroscopic analyzer, and the proportion of diffused oxygen was 0 in terms of atomic ratio with respect to nitrogen (N). .01-0.4, i.e.
Composition formula: TiN 1-Y (O) Y ,
(Where, (O) represents diffused oxygen from the titanium oxide layer as the lower layer when the upper layer is deposited ),
Y: 0.01 to 0.4 in atomic ratio
Titanium nitride oxide layer that satisfies

(c)上記窒酸化チタン層(上側層)および酸化チタン層(下側層)を蒸着形成した状態で、
ウエットブラストにて、噴射研磨材として、水との合量に占める割合で15〜60質量%の酸化アルミニウム微粒(以下、Al23微粒で示す)を配合した研磨液を噴射すると、前記窒酸化チタン層および酸化チタン層は、前記Al23微粒によって粉砕微粒化し、窒酸化チタン微粒および酸化チタン微粒となって前記Al23微粒の共存下で研磨材として作用し、硬質被覆層の上部層を構成する改質α型Al23層の表面を研磨することになり、この結果研磨後の前記改質α型Al23層の表面は、準拠規格JIS・B0601−1994に基いた測定(以下の表面粗さは全てかかる準拠規格に基いた測定値を示す)で、Ra:0.2μm以下の表面粗さにまで平滑化されるようになり、この上部層である改質α型Al23層の表面がRa:0.2μm以下の表面粗さに平滑化した上記の被覆サーメット工具を用いて、難削材の高速切削加工を行った場合、350m/min.を越える切削速度でも前記表面粗さの平滑化によって前記改質α型Al23層の摩耗進行が抑制されるようになり、この結果工具の使用寿命の一段の延命化が可能となること。
なお、この場合、上記改質α型Al23層の表面に、上記の窒酸化チタン層(上側層)および酸化チタン層(下側層)からなる研磨材層を形成することなく、これに同じくウエットブラストにて、噴射研磨材として、水との合量に占める割合で15〜60質量%のAl23微粒を配合した研磨液を直接噴射して、研磨しても、前記改質α型Al23層の表面は、Ra:0.3〜0.6μmの表面粗さにしか研磨されず、この結果の表面粗さがRa:0.3〜0.6μmの改質α型Al23層で上部層を構成した被覆サーメット工具を用いても、切削速度が350m/min.を越えた難削材の高速切削加工では表面平滑化による十分な摩耗抑制効果は発揮されず、満足な使用寿命の延命化は図れないこと。
(C) In a state where the titanium nitride oxide layer (upper layer) and the titanium oxide layer (lower layer) are formed by vapor deposition,
When a polishing liquid containing 15 to 60% by mass of aluminum oxide fine particles (hereinafter referred to as Al 2 O 3 fine particles) as a spraying abrasive in a proportion of the total amount with water is sprayed by wet blasting, the nitrogen The titanium oxide layer and the titanium oxide layer are pulverized and pulverized by the Al 2 O 3 fine particles, become titanium oxynitride fine particles and titanium oxide fine particles, and act as an abrasive in the presence of the Al 2 O 3 fine particles. of constituting the upper layer will be polishing the surface of the modified α type the Al 2 O 3 layer, the surface of the reformed α-type the Al 2 O 3 layer after the results polishing compliance JIS · B0601-1994 (The following surface roughness is a measured value based on such a compliant standard.) Ra: Smoothed to a surface roughness of 0.2 μm or less. This is the upper layer. surface of the modified α type the Al 2 O 3 layer Ra: 0.2 [mu] m using the above coated cermet tool obtained by smoothing the surface roughness of not more than, in the case of performing high-speed cutting of difficult-to-cut materials, 350 meters / min. Even at cutting speeds exceeding 1, the progress of wear of the modified α-type Al 2 O 3 layer can be suppressed by smoothing the surface roughness, and as a result, the life of the tool can be further increased. .
In this case, without forming the abrasive layer composed of the titanium nitride oxide layer (upper layer) and the titanium oxide layer (lower layer) on the surface of the modified α-type Al 2 O 3 layer, In the same way, even if wet polishing is performed by directly spraying and polishing a polishing liquid containing 15 to 60% by mass of Al 2 O 3 fine particles as a proportion of the total amount with water as the spray abrasive, The surface of the α-type Al 2 O 3 layer is polished only to a surface roughness of Ra: 0.3 to 0.6 μm, and the resulting surface roughness is modified to Ra: 0.3 to 0.6 μm. Even when a coated cermet tool having an upper layer composed of an α-type Al 2 O 3 layer is used, the cutting speed is 350 m / min. In high-speed cutting of difficult-to-cut materials that exceed the range, sufficient wear suppression effect due to surface smoothing cannot be demonstrated, and satisfactory service life cannot be extended.

(d)以上の通り、硬質被覆層の上部層が上記改質α型Al23層で構成されると共に、前記改質α型Al23層の少なくとも切刃稜線部を含むすくい面部分および逃げ面部分を研磨して、これら研磨面の表面粗さをRa:0.2μm以下とした被覆サーメット工具は、特に切刃部にきわめて高い切削抵抗が加わる難削材の高速切削加工でも、前記硬質被覆層の高温強度が向上し、かつ前記上部層の改質α型Al23層がすぐれた表面平滑性を具備することから、すぐれた耐チッピング性を発揮し、長期に亘ってすぐれた耐摩耗性を示すようになること。
以上(a)〜(d)に示される研究結果を得たのである。
(D) As described above, together with the upper layer of the hard coating layer is composed of the reformed α-type the Al 2 O 3 layer, the rake face including at least cutting ridge of the reformed α-type the Al 2 O 3 layer The coated cermet tool in which the portion and the flank portion are polished and the surface roughness of these polished surfaces is set to Ra: 0.2 μm or less is particularly suitable for high-speed cutting of difficult-to-cut materials in which extremely high cutting resistance is applied to the cutting edge. Since the high temperature strength of the hard coating layer is improved and the modified α-type Al 2 O 3 layer of the upper layer has excellent surface smoothness, it exhibits excellent chipping resistance and can be used for a long time. To show excellent wear resistance.
The research results shown in (a) to (d) above were obtained.

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、()工具基体の表面に、
a−1)下部層として、TiC層、TiN層、TiCN層、TiCO層、およびTiCNO層のうちの1層または2層以上からなり、かつ3〜20μmの合計平均層厚を有するTi化合物層、
a−2)上記の下部層であるTi化合物層と上部層である改質α型Al23層の間に、補強層として介在させた、電界放出型走査電子顕微鏡を用い、上記工具基体表面と平行な研磨面の測定範囲内に存在する六方晶結晶格子を有する結晶粒個々に電子線を照射して、前記研磨面の法線に対して、前記結晶粒の結晶面である(0001)面の法線がなす傾斜角を測定し、前記測定傾斜角のうち、45〜90度の範囲内にある測定傾斜角を0.25度のピッチ毎に区分すると共に、各区分内に存在する度数を集計してなる傾斜角度数分布グラフにおいて、75〜90度の範囲内の傾斜角区分に最高ピークが存在すると共に、前記75〜90度の範囲内に存在する度数の合計が、傾斜角度数分布グラフにおける度数全体の50%以上の割合を占める傾斜角度数分布グラフを示し、かつ0.1〜1.9μmの平均層厚を有する補強α型Al23層、
a−3)上部層として、電界放出型走査電子顕微鏡を用い、上記工具基体表面と平行な研磨面の測定範囲内に存在する六方晶結晶格子を有する結晶粒個々に電子線を照射して、前記研磨面の法線に対して、前記結晶粒の結晶面である(0001)面の法線がなす傾斜角を測定し、前記測定傾斜角のうち、0〜45度の範囲内にある測定傾斜角を0.25度のピッチ毎に区分すると共に、各区分内に存在する度数を集計してなる傾斜角度数分布グラフにおいて、0〜15度の範囲内の傾斜角区分に最高ピークが存在すると共に、前記0〜15度の範囲内に存在する度数の合計が、傾斜角度数分布グラフにおける度数全体の50%以上の割合を占める傾斜角度数分布グラフを示し、かつ1.5〜5.9μmの平均層厚を有する改質α型Al23層、
以上(a−1)〜(a−3)で構成された硬質被覆層を化学蒸着形成し
ついで、上記硬質被覆層の上部層である改質α型Al23層の全面に、
(b−1)下側層として、0.1〜3μmの平均層厚を有し、かつ、
組成式:TiOX
で表わした場合、厚さ方向中央部をオージェ分光分析装置で測定して、原子比で、
X:1.2〜1.7、
を満足する酸化チタン層、
(b−2)上側層として、0.05〜2μmの平均層厚を有し、かつ、
組成式:TiN1-Y(O)Y
で表わした場合(ただし、(O)は上側層の蒸着形成時における上記下側層である酸化チタン層からの拡散酸素を示す)、同じく厚さ方向中央部をオージェ分光分析装置で測定して、同じく原子比で、
Y:0.01〜0.4、
を満足する窒酸化チタン層、
以上(b−1)および(b−2)で構成された研磨材層を化学蒸着形成した状態で、
ウエットブラストにて、噴射研磨材として、水との合量に占める割合で15〜60質量%のAl23微粒を配合した研磨液を噴射し、
上記の研磨材層が噴射研磨材であるAl 2 3 微粒の噴射により粉砕微粒化してなる粉砕化酸化チタン微粒および粉砕化窒酸化チタン微粒と、噴射研磨材としてのAl23微粒の共存下で、上記硬質被覆層の上部層を構成する改質α型Al23層の少なくとも切刃稜線部を含むすくい面部分および逃げ面部分を研磨して、これら研磨面の表面粗さをRa:0.2μm以下としてなる、
難削材の高速切削加工で硬質被覆層がすぐれた耐チッピング性を発揮する被覆サーメット工具の製造方法に特徴を有するものである。
The present invention has been made based on the above research results, and ( 1 ) on the surface of the tool base,
(A -1 ) As a lower layer, a Ti compound layer composed of one or more of a TiC layer, a TiN layer, a TiCN layer, a TiCO layer, and a TiCNO layer, and having a total average layer thickness of 3 to 20 μm ,
(A -2 ) Using a field emission scanning electron microscope interposed as a reinforcing layer between the Ti compound layer as the lower layer and the modified α-type Al 2 O 3 layer as the upper layer, the tool An electron beam is irradiated to each crystal grain having a hexagonal crystal lattice existing within a measurement range of a polished surface parallel to the substrate surface, and is a crystal plane of the crystal grain with respect to a normal line of the polished surface ( The tilt angle formed by the normal line of the (0001) plane is measured, and among the measured tilt angles, the measured tilt angles within the range of 45 to 90 degrees are divided for each pitch of 0.25 degrees, and within each section In the inclination angle frequency distribution graph obtained by collecting the existing frequencies, the highest peak exists in the inclination angle section within the range of 75 to 90 degrees, and the total of the frequencies existing within the range of 75 to 90 degrees is Occupies 50% or more of the total frequency in the slope angle distribution graph That the inclination angle frequency distribution shows a graph, and the average layer thickness reinforcement α type the Al 2 O 3 layer having the 0.1~1.9Myuemu,
(A -3 ) A field emission scanning electron microscope is used as the upper layer, and each crystal grain having a hexagonal crystal lattice existing in the measurement range of the polished surface parallel to the tool base surface is irradiated with an electron beam. The inclination angle formed by the normal line of the (0001) plane, which is the crystal plane of the crystal grain, is measured with respect to the normal line of the polished surface, and is within the range of 0 to 45 degrees of the measured inclination angle. In the inclination angle distribution graph obtained by dividing the measured inclination angle for each pitch of 0.25 degrees and totaling the frequencies existing in each section, the highest peak is in the inclination angle section within the range of 0 to 15 degrees. An inclination angle distribution graph that is present and occupies a ratio of 50% or more of the entire frequencies in the inclination angle distribution graph, and the total number of frequencies existing in the range of 0 to 15 degrees is 1.5 to 5 Modified α-type Al 2 O having an average layer thickness of 9 μm 3 layers,
Chemical vapor deposition of the hard coating layer composed of (a-1) to (a-3) above ,
( 2 ) Next , on the entire surface of the modified α-type Al 2 O 3 layer, which is the upper layer of the hard coating layer,
(B-1) The lower layer has an average layer thickness of 0.1 to 3 μm, and
Composition formula: TiO x ,
, The central part in the thickness direction is measured with an Auger spectrometer, and the atomic ratio is
X: 1.2 to 1.7,
Satisfying titanium oxide layer,
(B-2) The upper layer has an average layer thickness of 0.05 to 2 μm, and
Composition formula: TiN 1-Y (O) Y ,
(However, (O) indicates the diffused oxygen from the titanium oxide layer, which is the lower layer when the upper layer is formed by vapor deposition ). Similarly, the central portion in the thickness direction is measured with an Auger spectrometer. , Also in atomic ratio,
Y: 0.01 to 0.4
Satisfying titanium oxynitride layer,
In the state where the abrasive layer composed of (b-1) and (b-2) is formed by chemical vapor deposition,
In wet blasting, as a spraying abrasive, a polishing liquid containing 15 to 60% by mass of Al 2 O 3 fine particles in a proportion of the total amount with water is sprayed,
Abrasive layer and the Al 2 O 3 by atomization of injection formed by grinding atomized pulverized titanium oxide fine particles and pulverized oxynitride titanium particulate is injected abrasive above, coexistence of Al 2 O 3 fine as injection abrasive Below, the rake face portion and the flank face portion including at least the cutting edge ridge line portion of the modified α-type Al 2 O 3 layer constituting the upper layer of the hard coating layer are polished, and the surface roughness of these polished surfaces is reduced. Ra: 0.2 μm or less
It has a feature in a method for producing a coated cermet tool that exhibits excellent chipping resistance in a hard coating layer in high-speed cutting of difficult-to-cut materials.

以下に、この発明の被覆サーメット工具の製造方法において、硬質被覆層、研磨材層、さらにウエットブラストで用いられる研磨液のAl23微粒に関して、上記の通りに数値限定した理由を説明する。
(A)硬質被覆層
(a−1)Ti化合物層(下部層)
Ti化合物層は、基本的には改質α型Al23層の下部層として存在し、自身の具備するすぐれた高温強度によって硬質被覆層が高温強度を具備するようにするほか、工具基体と補強α型Al23層のいずれにも強固に密着し、よって硬質被覆層の工具基体に対する密着性向上に寄与する作用を有するが、その合計平均層厚が3μm未満では、前記作用を十分に発揮させることができず、一方その合計平均層厚が20μmを越えると、特に高熱発生を伴なう高速切削では熱塑性変形を起し易くなり、これが偏摩耗の原因となることから、その合計平均層厚を3〜20μmと定めた。
Hereinafter, the reason why the hard coating layer, the abrasive layer, and the Al 2 O 3 fine particles of the polishing liquid used in the wet blasting in the method for producing the coated cermet tool of the present invention are numerically limited as described above will be described.
(A) Hard coating layer (a-1) Ti compound layer (lower layer)
The Ti compound layer basically exists as a lower layer of the modified α-type Al 2 O 3 layer, and allows the hard coating layer to have high-temperature strength by its excellent high-temperature strength. And the reinforcing α-type Al 2 O 3 layer firmly adhere to each other, and thus have an effect of improving the adhesion of the hard coating layer to the tool substrate. However, when the total average layer thickness is less than 3 μm, On the other hand, when the total average layer thickness exceeds 20 μm, it becomes easy to cause thermoplastic deformation particularly in high-speed cutting accompanied by high heat generation, which causes uneven wear. The total average layer thickness was determined to be 3-20 μm.

(a−2)改質α型Al23層(上部層)
改質α型Al23層の傾斜角度数分布グラフにおける測定傾斜角の最高ピーク位置は、化学蒸着装置における反応雰囲気圧力を変化させることによって変化するが、試験結果によれば、上記蒸着条件のうちの反応雰囲気圧力を6〜10kpaとすると、最高ピークが、0〜15度の範囲内の傾斜角区分に現れると共に、前記0〜15度の範囲内に存在する度数の合計が、傾斜角度数分布グラフにおける度数全体の50%以上の割合を占める傾斜角度数分布グラフを示すようになるものであり、したがって、前記反応雰囲気圧力が前記範囲から低い方に外れても、また高い方に外れても、前記0〜15度の範囲内に測定傾斜角の最高ピークが現れなくなり、このような場合には所望のすぐれた高温強度を具備することができないものである。
また、改質α型Al23層は、α型Al23自身のもつすぐれた高温硬さおよび耐熱性に加えて、高温強度も具備するようになるが、その平均層厚が1.5μm未満では、前記特性を硬質被覆層に十分に具備せしめることができず、また、その平均層厚が5.9μmを越えると、難削材の高速切削加工ではチッピングが発生し易くなることから、その平均層厚を1.5〜5.9μmと定めた。
(A-2) Modified α-type Al 2 O 3 layer (upper layer)
The maximum peak position of the measured inclination angle in the inclination angle number distribution graph of the modified α-type Al 2 O 3 layer is changed by changing the reaction atmosphere pressure in the chemical vapor deposition apparatus. When the reaction atmosphere pressure is 6 to 10 kpa, the highest peak appears in the inclination angle section in the range of 0 to 15 degrees, and the total of the frequencies existing in the range of 0 to 15 degrees is the inclination angle. An inclination angle number distribution graph occupying a ratio of 50% or more of the entire frequency in the number distribution graph is shown. Therefore, even if the reaction atmosphere pressure is out of the range, it is out of the range. However, the highest peak of the measured tilt angle does not appear within the range of 0 to 15 degrees, and in such a case, the desired excellent high-temperature strength cannot be provided.
The modified α-type Al 2 O 3 layer also has high-temperature strength in addition to the excellent high-temperature hardness and heat resistance of the α-type Al 2 O 3 itself, but the average layer thickness is 1 If the thickness is less than 5 μm, the above properties cannot be sufficiently provided in the hard coating layer, and if the average layer thickness exceeds 5.9 μm, chipping is likely to occur in high-speed cutting of difficult-to-cut materials. Therefore, the average layer thickness was determined to be 1.5 to 5.9 μm.

(a−3)補強α型Al23層(補強層)
上記の通り、補強α型Al23層の傾斜角度数分布グラフにおける測定傾斜角の最高ピーク位置は、化学蒸着装置における反応雰囲気圧力を変化させることによって変化するが、試験結果によれば、上記蒸着条件のうちの反応雰囲気圧力を、20〜30kPaとすると、最高ピークが75〜90度の範囲内の傾斜角区分に現れると共に、前記75〜90度の範囲内に存在する度数の合計が、傾斜角度数分布グラフにおける度数全体の50%以上の割合を占める傾斜角度数分布グラフを示すようになるものであり、したがって、前記反応雰囲気圧力が前記範囲から低い方に外れても、また高い方に外れても、75〜90度の範囲内に測定傾斜角の最高ピークが現れなくなり、このような場合には所望のすぐれた補強作用を発揮することができないものである。
また、その平均層厚が0.1μm未満では、上記改質α型Al23層に対する補強作用が不十分であり、一方、その平均層厚が1.9μmを越えると、難削材の高速切削加工ではチッピングが発生し易くなることから、その平均層厚を0.1〜1.9μmと定めた。
(A-3) Reinforced α-type Al 2 O 3 layer (reinforcing layer)
As described above, the highest peak position of the measured inclination angle in the inclination angle number distribution graph of the reinforced α-type Al 2 O 3 layer changes by changing the reaction atmosphere pressure in the chemical vapor deposition apparatus, but according to the test results, When the reaction atmosphere pressure in the above deposition conditions is 20 to 30 kPa, the maximum peak appears in the tilt angle section in the range of 75 to 90 degrees, and the total of the frequencies existing in the range of 75 to 90 degrees is The inclination angle number distribution graph occupies a ratio of 50% or more of the entire frequency in the inclination angle number distribution graph. Therefore, even if the reaction atmosphere pressure is out of the range, it is high. Even if it deviates, the maximum peak of the measured inclination angle does not appear within the range of 75 to 90 degrees, and in this case, the desired excellent reinforcing action cannot be exhibited. It is a thing.
Further, if the average layer thickness is less than 0.1 μm, the reinforcing action on the modified α-type Al 2 O 3 layer is insufficient, while if the average layer thickness exceeds 1.9 μm, the difficult-to-cut material Since high-speed cutting tends to cause chipping, the average layer thickness is set to 0.1 to 1.9 μm.

(B)研磨材層
上側層を構成する窒酸化チタン層は、上記の通り、まず、酸素の割合をTiに対する原子比で1.25〜1.90(W値)とした酸化チタン層を形成し、ついで、前記酸化チタン層の上に通常の条件でTiN層を蒸着することにより形成されるものであり、したがって前記TiN層形成時における前記酸化チタン層からの酸素の拡散が不可欠となるが、前記酸化チタン層のW値が1.25未満であると、前記TiN層への酸素の拡散反応が急激に低下し、上側層における拡散酸素の割合(Y値)を原子比で0.01以上にすることができず、一方同W値が1.90を越えると、前記上側層における拡散酸素の割合(Y値)が原子比で0.40を越えて多くなってしまうことから、W値を1.25〜1.90と定めたものであり、この場合上側層形成後の下側層(酸化チタン層)における酸素の割合(X値)は原子比で1.2〜1.7の範囲内の値をとるようになる、言い換えれば上側層形成後の下側層のX値が1.2〜1.7を満足する場合に、前記上側層のY値は0.01〜0.40を満足するものとなる。
また、この場合、下側層のX値および上側層のY値をそれぞれ1.2〜1.7および0.01〜0.40と定めたのは、前記X値およびY値が前記の値をとった場合に、これら研磨材層のウエットブラスト時における粉砕微粒化が好適な状態で行なわれ、すぐれた研磨機能を十分に発揮することが多くの試験結果から得られ、これらの試験結果に基いて定めたものである。したがって、前記X値およびY値がそれぞれ1.2〜1.7および0.01〜0.40の範囲から外れると、前記研磨材層のウエットブラスト時における粉砕微粒化が満足に行なわれず、すぐれた研磨機能を期待することができない。
さらに、上側層および下側層の平均層厚を、それぞれ0.05〜2μmおよび0.1〜3μmとしたのは、その平均層厚が0.05μm未満および0.1μm未満では、ウエットブラスト時における下側層の粉砕化酸化チタン微粒、上側層の粉砕化窒酸化チタン微粒の割合が少な過ぎて、研磨機能を十分に発揮することができず、一方、その平均層厚がそれぞれ2μmおよび3μmを越えても、研磨機能が急激に低下するようになり、いずれの場合もα型Al23層の表面をRa:0.2μm以下の表面粗さに研磨することができなくなるという理由にもとづくものである。
(B) Abrasive material layer As described above, the titanium oxynitride layer constituting the upper layer first forms a titanium oxide layer in which the oxygen ratio is 1.25 to 1.90 (W value) in terms of atomic ratio to Ti. Then, it is formed by depositing a TiN layer on the titanium oxide layer under normal conditions. Therefore, diffusion of oxygen from the titanium oxide layer during the formation of the TiN layer is indispensable. When the W value of the titanium oxide layer is less than 1.25, the diffusion reaction of oxygen into the TiN layer is drastically reduced, and the ratio of diffused oxygen (Y value) in the upper layer is 0.01 by atomic ratio. On the other hand, if the same W value exceeds 1.90, the ratio of diffused oxygen (Y value) in the upper layer will increase beyond 0.40 in terms of atomic ratio. The value is defined as 1.25 to 1.90 In this case, the oxygen ratio (X value) in the lower layer (titanium oxide layer) after forming the upper layer takes a value in the range of 1.2 to 1.7 in terms of atomic ratio, in other words, the upper layer. When the X value of the lower layer after formation satisfies 1.2 to 1.7, the Y value of the upper layer satisfies 0.01 to 0.40.
In this case, the X value of the lower layer and the Y value of the upper layer are set to 1.2 to 1.7 and 0.01 to 0.40, respectively. It is obtained from many test results that these abrasive layers are pulverized and atomized in a suitable state at the time of wet blasting, and exhibit an excellent polishing function sufficiently. Based on this. Therefore, if the X value and Y value are out of the range of 1.2 to 1.7 and 0.01 to 0.40, respectively, the pulverization and atomization at the time of wet blasting of the abrasive layer is not satisfactorily performed, which is excellent. The polishing function cannot be expected.
Further, the average layer thicknesses of the upper layer and the lower layer were set to 0.05 to 2 μm and 0.1 to 3 μm, respectively, when the average layer thickness was less than 0.05 μm and less than 0.1 μm. The ratio of the pulverized titanium oxide fine particles in the lower layer and the fine pulverized titanium oxynitride fine particles in the upper layer is too small to perform the polishing function sufficiently, while the average layer thickness is 2 μm and 3 μm, respectively. The reason is that the polishing function suddenly deteriorates even if the thickness exceeds the range, and in any case, the surface of the α-type Al 2 O 3 layer cannot be polished to a surface roughness of Ra: 0.2 μm or less. It is based.

(C)研磨液のAl23微粒
研磨液のAl23微粒には、ウエットブラスト時に研磨材層を構成する下側層の粉砕化酸化チタン微粒および上側層の粉砕化窒酸化チタン微粒と共存した状態で、改質α型Al23層の表面を研磨する作用があるが、その割合が水との合量に占める割合で15質量%未満でも、また60質量%を越えても研磨機能が急激に低下するようになることから、その割合を15〜60質量%と定めた。
(C) Polishing Al 2 O 3 Fine Particles In the polishing liquid Al 2 O 3 fine particles, the lower layer pulverized titanium oxide fine particles and the upper layer pulverized titanium oxynitride fine particles that constitute the abrasive layer during wet blasting In the coexisting state, the surface of the modified α-type Al 2 O 3 layer is polished, but even if the ratio is less than 15% by mass or more than 60% by mass with respect to the total amount with water, However, since the polishing function suddenly decreases, the ratio is determined to be 15 to 60% by mass.

この発明の方法で製造された被覆サーメット工具は、硬質被覆層の上部層を構成する改質α型Al23層を、前記改質α型Al23層とTi化合物層との間に介在させた補強α型Al23層が十分に補強し、さらに前記改質α型Al23層の表面をRa:0.2μm以下の表面粗さに研磨することにより、特に切粉の粘性が高く、かつ工具表面に溶着し易いステンレス鋼や高マンガン鋼、さらに軟鋼などの難削材(被削材)の切削加工を高熱発生を伴う高速切削条件で行ない、前記被削材および切粉が高温に加熱されて粘性および溶着性が一段と増大し、これに伴なって硬質被覆層表面に対する切削抵抗が増すようになっても、前記硬質被覆層のもつすぐれた高温強度および平滑な表面粗さによって前記硬質被覆層のチッピング発生が著しく抑制され、かつ摩耗抑制効果も発揮され、この結果長期に亘ってすぐれた耐摩耗性を示すようになるものである。 The coated cermet tool manufactured by the method of the present invention includes a modified α-type Al 2 O 3 layer constituting an upper layer of a hard coating layer, and a gap between the modified α-type Al 2 O 3 layer and the Ti compound layer. the surface of the interposed allowed reinforcement α type the Al 2 O 3 layer is sufficiently reinforced, further wherein the modified α type the Al 2 O 3 layer to Ra: by polishing the surface roughness of less than 0.2 [mu] m, in particular switching Cutting of difficult-to-cut materials (work materials) such as stainless steel, high manganese steel, and mild steel, which have high powder viscosity and easily welded to the tool surface, under high-speed cutting conditions with high heat generation. Even if the chips are heated to a high temperature and the viscosity and weldability are further increased, and as a result, the cutting resistance to the surface of the hard coating layer increases, the excellent high-temperature strength and smoothness of the hard coating layer can be obtained. The chipping of the hard coating layer is noticeable due to the rough surface roughness. It is suppressed, and abrasion suppressing effect is also exerted, in which the result is shown excellent wear resistance for a long time.

つぎに、この発明の被覆サーメット工具の製造方法を実施例により具体的に説明する。 Next, the method for producing a coated cermet tool according to the present invention will be specifically described with reference to examples.

原料粉末として、いずれも1〜3μmの平均粒径を有するWC粉末、TiC粉末、ZrC粉末、VC粉末、TaC粉末、NbC粉末、Cr32粉末、TiN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、さらにワックスを加えてアセトン中で24時間ボールミル混合し、減圧乾燥した後、98MPaの圧力で所定形状の圧粉体にプレス成形し、この圧粉体を5Paの真空中、1370〜1470℃の範囲内の所定の温度に1時間保持の条件で真空焼結し、焼結後、切刃部にR:0.07mmのホーニング加工を施すことにより、中心部に工具取り付け用ボルト貫通孔を有する形式で、ISO規格にCNMG120412として規定されるスローアウエイチップ形状をもったWC基超硬合金製の工具基体A〜Fをそれぞれ製造した。 As raw material powders, WC powder, TiC powder, ZrC powder, VC powder, TaC powder, NbC powder, Cr 3 C 2 powder, TiN powder, and Co powder each having an average particle diameter of 1 to 3 μm are prepared. The raw material powder is blended in the blending composition shown in Table 1, added with wax, ball mill mixed in acetone for 24 hours, dried under reduced pressure, and press-molded into a green compact of a predetermined shape at a pressure of 98 MPa. The green compact is vacuum-sintered in a vacuum of 5 Pa at a predetermined temperature within a range of 1370 to 1470 ° C. for 1 hour. After sintering, the cutting edge is subjected to a honing process of R: 0.07 mm. Thus, a tool base made of a WC-based cemented carbide having a throwaway tip shape defined as CNMG12041 in the ISO standard in the form of having a tool mounting bolt through hole in the center. Each of the bodies A to F was produced.

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、ZrC粉末、NbC粉末、TaC粉末、WC粉末、Co粉末、およびNi粉末を用意し、これら原料粉末を、表2に示される配合組成に配合し、ボールミルで24時間湿式混合し、乾燥した後、98MPa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:1540℃に1時間保持の条件で焼結し、焼結後、切刃部分にR:0.07mmのホーニング加工を施すことにより、工具本体にクランプ駒による挟み締めにより取り付けられる穴なし形式で、ISO規格にCNMN120412として規定されるスローアウエイチップ形状をもったTiCN基サーメット製の工具基体a〜fを形成した。 Further, as raw material powders, TiCN (mass ratio, TiC / TiN = 50/50) powder, Mo 2 C powder, ZrC powder, NbC powder, TaC powder, WC, all having an average particle diameter of 0.5 to 2 μm. Prepare powder, Co powder, and Ni powder, blend these raw material powders into the composition shown in Table 2, wet mix with a ball mill for 24 hours, dry, and press-mold into a green compact at 98 MPa pressure The green compact is sintered in a nitrogen atmosphere of 1.3 kPa at a temperature of 1540 ° C. for 1 hour, and after sintering, the cutting edge portion is subjected to a honing process of R: 0.07 mm. Made of TiCN-based cermet with a throwaway tip shape that is defined as CNMN12041 in the ISO standard, with no holes attached to the tool body by clamping with clamp pieces To form a tool substrate a~f.

ついで、これらの工具基体A〜Fおよび工具基体a〜fのそれぞれを、通常の化学蒸着装置に装入し、
(a)まず、表3(表3中のl−TiCNは特開平6−8010号公報に記載される縦長成長結晶組織をもつTiCN層の形成条件を示すものであり、これ以外は通常の粒状結晶組織の形成条件を示すものである)に示される条件にて、表6に示される目標層厚のTi化合物層を硬質被覆層の下部層として蒸着形成し、
(b)ついで、反応ガス組成:容量%で、AlCl3:2.2%、CO2:5%、HCl:2%、H2S:0.15%、H2:残り、
反応雰囲気温度:850℃、
反応雰囲気圧力:20〜30kPaの範囲内の所定の圧力、
の条件で表6に示される目標層厚で、補強α型Al23層を蒸着形成し、
(c)引き続いて、反応ガス組成:容量%で、AlCl3:2.2%、CO2:1.5%、HCl:2%、H2S:0.75%、Ar:26.5%、H2:残り、
反応雰囲気温度:1070℃、
反応雰囲気圧力:6〜10kPaの範囲内の所定の圧力、
の条件で同じく表6に示される目標層厚で、同じく上部層として改質α型Al23層を蒸着形成し、
(d)さらに、研磨材層の下側層形成用酸化チタン層[TiO(1)〜(6)のいずれか]を表4に示される条件で、表6に示される目標層厚で蒸着形成した後、上側層形成用窒化チタン層(TiN層)を同じく表3に示される条件で、表6に示される目標層厚で蒸着形成して、表6に示される組成、すなわち厚さ方向中央部をオージェ分光分析装置で測定して、それぞれ表6に示されるX値およびY値の下側層および上側層からなる研磨材層を形成し、
(e)引き続いて、表5に示されるブラスト条件で、かつ表6に示される組み合わせでウエットブラストを施して、上記工具基体A〜Fについては、中心部の工具取り付け用ボルト貫通孔周辺部の上記研磨材層は除去せずに残した状態、また、上記の工具基体a〜fについては、クランプ駒当接面部分(すくい面中心部)の上記研磨材層は除去せずに残した状態で、前記改質α型Al23層(上部層)の切刃稜線部を含むすくい面および逃げ面を、同じく表6に示される表面粗さに研磨することにより本発明被覆サーメット工具1〜13をそれぞれ製造した。
Then, each of these tool bases A to F and tool bases a to f is charged into a normal chemical vapor deposition apparatus,
(A) First, Table 3 (l-TiCN in Table 3 indicates the conditions for forming a TiCN layer having a vertically elongated crystal structure described in JP-A-6-8010, and the other conditions are ordinary granularity. Under the conditions shown in Table 6), the Ti compound layer having the target layer thickness shown in Table 6 is deposited as the lower layer of the hard coating layer,
(B) Next, reaction gas composition: volume%, AlCl 3 : 2.2%, CO 2 : 5%, HCl: 2%, H 2 S: 0.15%, H 2 : remaining,
Reaction atmosphere temperature: 850 ° C.
Reaction atmosphere pressure: a predetermined pressure in the range of 20-30 kPa,
A reinforced α-type Al 2 O 3 layer is formed by vapor deposition at the target layer thickness shown in Table 6 under the conditions of
(C) Subsequently, reaction gas composition: volume%, AlCl 3 : 2.2%, CO 2 : 1.5%, HCl: 2%, H 2 S: 0.75%, Ar: 26.5% , H 2 : remaining,
Reaction atmosphere temperature: 1070 ° C.
Reaction atmosphere pressure: a predetermined pressure within a range of 6 to 10 kPa,
The modified α-type Al 2 O 3 layer is also formed by vapor deposition with the target layer thickness shown in Table 6 under the same conditions as above,
(D) Further, a titanium oxide layer for forming the lower layer of the abrasive layer [any one of TiO W (1) to (6)] is deposited at the target layer thickness shown in Table 6 under the conditions shown in Table 4. After the formation, an upper layer forming titanium nitride layer (TiN layer) is vapor-deposited at the target layer thickness shown in Table 6 under the same conditions as shown in Table 3, and the composition shown in Table 6, ie, the thickness direction The central part is measured with an Auger spectroscopic analyzer, and an abrasive layer composed of a lower layer and an upper layer of the X value and Y value shown in Table 6 is formed.
(E) Subsequently, wet blasting is performed under the blasting conditions shown in Table 5 and in the combinations shown in Table 6, and the tool bases A to F are arranged at the periphery of the tool attachment bolt through-holes at the center. The state where the abrasive layer is left without being removed, and the state where the abrasive layer is left without being removed at the clamp piece abutting surface portion (the center portion of the rake face) for the tool bases a to f. Then, the rake face and flank face including the cutting edge ridge line portion of the modified α-type Al 2 O 3 layer (upper layer) are polished to the surface roughness shown in Table 6 to obtain the coated cermet tool 1 of the present invention. ~ 13 were produced respectively.

また、比較の目的で、表7に示される通り、硬質被覆層の上部層である改質α型Al23層と同下部層であるTi化合物層の間に補強α型Al23層の形成を行なわず、かつ、上記の研磨材層の形成およびウエットブラストによる表面研磨処理を行わない以外は同一の条件で、従来被覆サーメット工具1〜13をそれぞれ製造した。 For comparison purposes, as shown in Table 7, a reinforced α-type Al 2 O 3 is provided between the modified α-type Al 2 O 3 layer as the upper layer of the hard coating layer and the Ti compound layer as the lower layer. Conventionally coated cermet tools 1 to 13 were respectively manufactured under the same conditions except that the layer was not formed and the formation of the abrasive layer and the surface polishing treatment by wet blasting were not performed.

ついで、上記の本発明被覆サーメット工具1〜13と従来被覆サーメット工具1〜13の硬質被覆層の上部層を構成する改質α型Al23層、および上記の本発明被覆サーメット工具1〜13の補強α型Al23層について、電界放出型走査電子顕微鏡を用いて、傾斜角度数分布グラフをそれぞれ作成した。
すなわち、上記傾斜角度数分布グラフは、上記の本発明被覆サーメット工具1〜13と従来被覆サーメット工具1〜13の改質α型Al23層、および本発明被覆サーメット工具1〜13の補強α型Al23層について、それぞれ工具基体表面と平行な面をそれぞれ研磨面とした状態で、電界放出型走査電子顕微鏡の鏡筒内にセットし、前記研磨面に70度の入射角度で15kVの加速電圧の電子線を1nAの照射電流で、それぞれの前記研磨面の測定範囲内に存在する六方晶結晶格子を有する結晶粒個々に照射して、電子後方散乱回折像装置を用い、30×50μmの領域を0.1μm/stepの間隔で、前記研磨面の法線に対して、前記結晶粒の結晶面である(0001)面の法線がなす傾斜角を測定し、この測定結果に基づいて、前記測定傾斜角のうち、前記改質α型Al23層については0〜45度、前記補強α型Al23層については45〜90度の範囲内にある測定傾斜角を0.25度のピッチ毎に区分すると共に、各区分内に存在する度数を集計することにより作成した。
Subsequently, the modified α-type Al 2 O 3 layer constituting the upper layer of the hard coating layer of the present invention coated cermet tool 1-13 and the conventional coated cermet tool 1-13, and the present invention coated cermet tool 1-1 With respect to the 13 reinforced α-type Al 2 O 3 layers, inclination angle number distribution graphs were respectively prepared using a field emission scanning electron microscope.
That is, the inclination angle number distribution graph shows the modified α-type Al 2 O 3 layer of the present invention coated cermet tools 1 to 13 and the conventional coated cermet tools 1 to 13 and the reinforcement of the present coated cermet tools 1 to 13. The α-type Al 2 O 3 layer is set in a lens barrel of a field emission scanning electron microscope with each surface parallel to the surface of the tool base being a polished surface, and incident on the polished surface at an incident angle of 70 degrees. An electron backscatter diffraction image apparatus is used to irradiate an electron beam having an acceleration voltage of 15 kV with an irradiation current of 1 nA on each crystal grain having a hexagonal crystal lattice existing within the measurement range of each polished surface, The inclination angle formed by the normal line of the (0001) plane, which is the crystal plane of the crystal grain, is measured with respect to the normal line of the polished surface at an interval of 0.1 μm / step in a region of × 50 μm. Based on before Among the measurement inclination angle, the 0-45 degrees for reforming α type the Al 2 O 3 layer, the measurement inclination angle is in the range of 45 to 90 degrees for the reinforcement α type the Al 2 O 3 layer 0.25 This was created by dividing the pitch for each degree and counting the frequencies existing in each division.

この結果得られた各種の改質α型Al23層および補強α型Al23層の傾斜角度数分布グラフにおいて、表8,9にそれぞれ示される通り、本発明被覆サーメット工具1〜13および従来被覆サーメット工具1〜13の改質α型Al23層は、(0001)面の測定傾斜角の分布が、それぞれ0〜15度の範囲内の傾斜角区分に最高ピークが現れる傾斜角度数分布グラフを示し、一方本発明被覆サーメット工具1〜13の補強α型Al23層においては、75〜90度の範囲内の傾斜角区分に最高ピークが現れる傾斜角度数分布グラフを示すものであった。
また表8,9には、上記の各種の改質α型Al23層および補強α型Al23層の傾斜角度数分布グラフにおいて、それぞれ0〜15度および75〜90度の範囲内の傾斜角区分に存在する全傾斜角度数の傾斜角度数分布グラフ全体に占める割合を示した。
なお、図3は、本発明被覆サーメット工具4の補強α型Al23層の傾斜角度数分布グラフ、図4は同改質α型Al23層の傾斜角度数分布グラフを示すものである。
In the gradient angle distribution graphs of the various modified α-type Al 2 O 3 layers and reinforced α-type Al 2 O 3 layers obtained as a result, as shown in Tables 8 and 9, respectively, the coated cermet tools 1 to 1 of the present invention are used. 13 and the modified α-type Al 2 O 3 layer of the conventional coated cermet tools 1 to 13, the distribution of the measured inclination angle of the (0001) plane shows the highest peak in the inclination angle section within the range of 0 to 15 degrees, respectively. An inclination angle number distribution graph is shown. On the other hand, in the reinforcing α-type Al 2 O 3 layer of the coated cermet tools 1 to 13 of the present invention, an inclination angle number distribution graph in which the highest peak appears in the inclination angle section within the range of 75 to 90 degrees. Was shown.
Tables 8 and 9 show the ranges of 0 to 15 degrees and 75 to 90 degrees in the inclination angle number distribution graphs of the various modified α-type Al 2 O 3 layers and reinforced α-type Al 2 O 3 layers, respectively. The ratio of the total number of tilt angles existing in the tilt angle section to the entire tilt angle distribution graph is shown.
3 is a graph showing the inclination angle distribution of the reinforced α-type Al 2 O 3 layer of the coated cermet tool 4 of the present invention, and FIG. 4 is a graph showing the inclination angle distribution of the modified α-type Al 2 O 3 layer. It is.

また、この結果得られた本発明被覆サーメット工具1〜13および従来被覆サーメット工具1〜13の硬質被覆層の構成層の厚さを、走査型電子顕微鏡を用いて測定(縦断面測定)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。   Moreover, when the thickness of the constituent layer of the hard coating layer of the present coated cermet tools 1 to 13 and the conventional coated cermet tools 1 to 13 obtained as a result was measured using a scanning electron microscope (longitudinal section measurement). , Each showed an average layer thickness (average value of 5-point measurement) substantially the same as the target layer thickness.

つぎに、上記の本発明被覆サーメット工具1〜13および従来被覆サーメット工具1〜13各種の被覆サーメット工具について、いずれも工具鋼製バイトの先端部にボルト止めまたはクランプ駒による挟み締め止めした状態で、
被削材:JIS・SUS304の丸棒、
切削速度:360m/min.、
切り込み:1.5mm、
送り:0.35mm/rev.、
の条件(切削条件Aという)でのステンレス鋼の乾式連続高速切削試験(通常の切削速度150m/min.)、
被削材:JIS・SS400の長さ方向等間隔4本縦溝入り丸棒、
切削速度:390m/min.、
切り込み:1.5mm、
送り:0.3mm/rev.、
の条件(切削条件Bという)での軟鋼の乾式断続高速切削試験(通常の切削速度は200m/min.)、さらに、
被削材:JIS・SCMnH1の丸棒、
切削速度:380m/min.、
切り込み:2.5mm、
送り:0.35mm/rev.、
の条件(切削条件Cという)での高マンガン鋼の乾式連続高速切削試験(通常の切削速度は250m/min.)を行い、いずれの切削試験でも切刃の逃げ面摩耗幅が、一般に切削工具の使用寿命の目安とされている0.3mmに至るまでの切削時間を測定した。この測定結果を表10に示した。
Next, with respect to the above-described coated cermet tools 1 to 13 of the present invention and the various coated cermet tools 1 to 13 of the present invention, all of them are clamped and clamped to the tip of the tool steel tool by a bolt or a clamp piece. ,
Work material: JIS / SUS304 round bar,
Cutting speed: 360 m / min. ,
Incision: 1.5mm,
Feed: 0.35 mm / rev. ,
Dry continuous high-speed cutting test (normal cutting speed 150 m / min.) Of stainless steel under the following conditions (referred to as cutting conditions A),
Work material: JIS / SS400 lengthwise equidistant 4 round bars with flutes,
Cutting speed: 390 m / min. ,
Incision: 1.5mm,
Feed: 0.3 mm / rev. ,
Dry interrupted high-speed cutting test (normal cutting speed is 200 m / min.) Of mild steel under the conditions (referred to as cutting conditions B),
Work material: JIS / SCMnH1 round bar,
Cutting speed: 380 m / min. ,
Incision: 2.5mm,
Feed: 0.35 mm / rev. ,
The dry continuous high-speed cutting test (normal cutting speed is 250 m / min.) Of high manganese steel under the above conditions (referred to as cutting condition C), and the flank wear width of the cutting edge is generally a cutting tool in any cutting test. The cutting time up to 0.3 mm, which is regarded as a standard for the service life of the steel, was measured. The measurement results are shown in Table 10.

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Figure 0004788892
Figure 0004788892

表6〜10に示される結果から、本発明被覆サーメット工具1〜13は、いずれも硬質被覆層の下部層であるTi化合物層と上部層である改質α型Al23層の間に介在させた補強α型Al23層が、(0001)面の傾斜角度数分布グラフで75〜90度の範囲内の傾斜角区分で最高ピークを示し、これの作用で前記改質α型Al23層が十分に補強されて一段とすぐれた高温強度をもつようになり、さらに、前記改質α型Al23層の少なくとも切刃稜線部を含むすくい面部分および逃げ面部分の表面がRa:0.2μm以下の表面粗さに研磨され、摩耗進行抑制効果が発揮されることと相俟って、特に切刃部にきわめて高い切削抵抗が加わる難削材の高速切削加工でも、切刃部におけるチッピング発生が著しく抑制され、すぐれた耐摩耗性を長期に亘って示すのに対して、硬質被覆層に前記補強α型Al23層の介在形成がなく、かつ上部層が表面平滑性の低い改質α型Al23層で構成された従来被覆サーメット工具1〜13においては、いずれも難削材の高速切削加工では硬質被覆層の高温強度が不十分であるために、表面平滑性の低い上部層と相俟って、切刃部にチッピングが発生し、比較的短時間で使用寿命に至ることが明らかである。 From the results shown in Tables 6 to 10, each of the coated cermet tools 1 to 13 of the present invention is between the Ti compound layer that is the lower layer of the hard coating layer and the modified α-type Al 2 O 3 layer that is the upper layer. The intervening reinforced α-type Al 2 O 3 layer shows the highest peak in the inclination angle section within the range of 75 to 90 degrees in the inclination angle number distribution graph of the (0001) plane, and this action makes the modified α type the Al 2 O 3 layer is sufficiently reinforced now with more excellent high temperature strength, furthermore, the rake face portion and flank portions including at least the cutting edge line portion of the reforming α type the Al 2 O 3 layer Combined with the fact that the surface is polished to a surface roughness of Ra: 0.2 μm or less and the effect of suppressing the progress of wear is exerted, especially in high-speed cutting of difficult-to-cut materials in which extremely high cutting resistance is applied to the cutting edge. Chipping at the cutting edge is remarkably suppressed and excellent resistance Whereas shown over a long period of time耗性, without intervening formation of the reinforcing α type the Al 2 O 3 layer to the hard coating layer, and a low reforming α-type surface smoothness upper layer the Al 2 O 3 layer In the conventional coated cermet tools 1 to 13 constituted by the above, since the high temperature strength of the hard coating layer is insufficient in high-speed cutting of difficult-to-cut materials, combined with the upper layer having low surface smoothness It is clear that chipping occurs at the cutting edge and the service life is reached in a relatively short time.

上述のように、この発明の方法によって製造された被覆サーメット工具は、各種鋼や鋳鉄などの高速切削加工は勿論のこと、特に自身が高い粘性を有し、かつ切削時の切削工具表面部の硬質被覆層に対する粘着性も高く、この結果切削抵抗のきわめて高いものとなる軟鋼やステンレス鋼、さらに高マンガン鋼などの難削材の高速切削加工でも、チッピングの発生なく、すぐれた耐摩耗性を示し、長期に亘ってすぐれた切削性能を発揮するものであるから、切削装置の高性能化並びに切削加工の省力化および省エネ化、さらに低コスト化に十分満足に対応できるものである。 As described above, the coated cermet tool manufactured by the method of the present invention has a high viscosity in addition to high-speed cutting such as various steels and cast iron, and the cutting tool surface portion at the time of cutting is particularly high. High adhesion to hard coating layer, resulting in excellent wear resistance without chipping even in high-speed cutting of difficult-to-cut materials such as mild steel, stainless steel, and high manganese steel that have extremely high cutting resistance. Since it exhibits excellent cutting performance over a long period of time, it can sufficiently satisfactorily cope with higher performance of the cutting device, labor saving and energy saving of cutting, and lower cost.

本発明被覆サーメット工具の硬質被覆層を構成する補強α型Al23層における結晶粒の(0001)面を測定する場合の傾斜角の測定範囲を示す概略説明図である。Is a schematic diagram illustrating a measurement range of the inclination angle in the case of measuring the crystal grains (0001) plane in the reinforcement α type the Al 2 O 3 layer constituting the hard layer of the present invention coated cermet tool. 硬質被覆層を構成する改質α型Al23層における結晶粒の(0001)面を測定する場合の傾斜角の測定範囲を示す概略説明図である。It is a schematic explanatory drawing which shows the measurement range of the inclination angle in the case of measuring the (0001) plane of the crystal grain in the modified α-type Al 2 O 3 layer constituting the hard coating layer. 本発明被覆サーメット工具4の硬質被覆層を構成する補強α型Al23層の45〜90度の傾斜角区分を示す傾斜角度数分布グラフである。The inclination angle frequency distribution graph showing the tilt angle sections of 45 to 90 degrees to the present invention coated cermet reinforced α type constituting the hard layer of the tool 4 Al 2 O 3 layer. 本発明被覆サーメット工具4の硬質被覆層を構成する改質α型Al23層の0〜45度の傾斜角区分を示す傾斜角度数分布グラフである。The inclination angle frequency distribution graph showing the tilt angle sections of 0 to 45 degrees of the modified α type the Al 2 O 3 layer constituting the hard layer of the present invention coated cermet tool 4.

Claims (1)

)炭化タングステン基超硬合金または炭窒化チタン基サーメットで構成された工具基体の表面に、
a−1)下部層として、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のうちの1層または2層以上からなり、かつ3〜20μmの合計平均層厚を有するTi化合物層、
a−2)上記の下部層であるTi化合物層と下記の上部層である改質α型酸化アルミニウム層の間に、補強層として介在させた、化学蒸着した状態でα型の結晶構造を有し、電界放出型走査電子顕微鏡を用い、上記工具基体表面と平行な研磨面の測定範囲内に存在する六方晶結晶格子を有する結晶粒個々に電子線を照射して、前記研磨面の法線に対して、前記結晶粒の結晶面である(0001)面の法線がなす傾斜角を測定し、前記測定傾斜角のうち、45〜90度の範囲内にある測定傾斜角を0.25度のピッチ毎に区分すると共に、各区分内に存在する度数を集計してなる傾斜角度数分布グラフにおいて、75〜90度の範囲内の傾斜角区分に最高ピークが存在すると共に、前記75〜90度の範囲内に存在する度数の合計が、傾斜角度数分布グラフにおける度数全体の50%以上の割合を占める傾斜角度数分布グラフを示し、かつ0.1〜1.9μmの平均層厚を有する補強α型酸化アルミニウム層、
a−3)上部層として、化学蒸着した状態でα型の結晶構造を有し、電界放出型走査電子顕微鏡を用い、上記工具基体表面と平行な研磨面の測定範囲内に存在する六方晶結晶格子を有する結晶粒個々に電子線を照射して、前記研磨面の法線に対して、前記結晶粒の結晶面である(0001)面の法線がなす傾斜角を測定し、前記測定傾斜角のうち、0〜45度の範囲内にある測定傾斜角を0.25度のピッチ毎に区分すると共に、各区分内に存在する度数を集計してなる傾斜角度数分布グラフにおいて、0〜15度の範囲内の傾斜角区分に最高ピークが存在すると共に、前記0〜15度の範囲内に存在する度数の合計が、傾斜角度数分布グラフにおける度数全体の50%以上の割合を占める傾斜角度数分布グラフを示し、かつ1.5〜5.9μmの平均層厚を有する改質α型酸化アルミニウム層、
以上(a−1)〜(a−3)で構成された硬質被覆層を化学蒸着形成し
ついで、上記硬質被覆層の上部層である改質α型酸化アルミニウム層の全面に、
(b−1)下側層として、0.1〜3μmの平均層厚を有し、かつ、
組成式:TiOX
で表わした場合、厚さ方向中央部をオージェ分光分析装置で測定して、原子比で、
X:1.2〜1.7、
を満足する酸化チタン層、
(b−2)上側層として、0.05〜2μmの平均層厚を有し、かつ、
組成式:TiN1-Y(O)Y
で表わした場合[ただし、(O)は上側層の蒸着形成時における上記下側層である酸化チタン層からの拡散酸素を示す]、同じく厚さ方向中央部をオージェ分光分析装置で測定して、同じく原子比で、
Y:0.01〜0.4、
を満足する窒酸化チタン層、
以上(b−1)および(b−2)で構成された研磨材層を化学蒸着形成した状態で、
ウエットブラストにて、噴射研磨材として、水との合量に占める割合で15〜60質量%の酸化アルミニウム微粒を配合した研磨液を噴射し、
上記の研磨材層が噴射研磨材である酸化アルミニウム微粒の噴射により粉砕微粒化してなる粉砕化酸化チタン微粒および粉砕化窒酸化チタン微粒と、噴射研磨材としての酸化アルミニウム微粒の共存下で、上記硬質被覆層の上部層を構成する改質α型酸化アルミニウム層の少なくとも切刃稜線部を含むすくい面部分および逃げ面部分を研磨して、これら研磨面の表面粗さを準拠規格JIS・B0601−1994に基いた測定で、Ra:0.2μm以下としたこと、
を特徴とする難削材の高速切削加工で硬質被覆層がすぐれた耐チッピング性を発揮する表面被覆サーメット製切削工具の製造方法
( 1 ) On the surface of a tool base made of tungsten carbide-based cemented carbide or titanium carbonitride-based cermet,
(A -1 ) As a lower layer, it is composed of one or more of Ti carbide layer, nitride layer, carbonitride layer, carbonate layer, and carbonitride layer, and 3 to 20 μm. A Ti compound layer having a total average layer thickness;
(A -2 ) An α-type crystal structure in a state of chemical vapor deposition interposed between the Ti compound layer as the lower layer and the modified α-type aluminum oxide layer as the upper layer described below as a reinforcing layer. And using a field emission scanning electron microscope, irradiating an electron beam to each crystal grain having a hexagonal crystal lattice existing within the measurement range of the polished surface parallel to the surface of the tool substrate. The inclination angle formed by the normal line of the (0001) plane which is the crystal plane of the crystal grain is measured with respect to the line, and the measurement inclination angle within the range of 45 to 90 degrees out of the measurement inclination angles is set to 0. In the slope angle distribution graph obtained by dividing the pitch every 25 degrees and by counting the frequencies existing in each section, the highest peak exists in the slope angle section within the range of 75 to 90 degrees, and the 75 The sum of the frequencies existing in the range of ~ 90 degrees is the inclination angle The number distribution shows an inclination angle frequency distribution graph in a proportion of 50% or more of the total power in the graph, and the average layer thickness reinforcement α-type aluminum oxide layer having a 0.1~1.9Myuemu,
(A -3 ) Hexagonal crystal having an α-type crystal structure in the state of chemical vapor deposition as an upper layer and existing in a measurement range of a polished surface parallel to the tool substrate surface using a field emission scanning electron microscope By irradiating each crystal grain having a crystal lattice with an electron beam, the inclination angle formed by the normal line of the (0001) plane which is the crystal plane of the crystal grain is measured with respect to the normal line of the polished surface. In the inclination angle number distribution graph formed by dividing the measured inclination angles within the range of 0 to 45 degrees out of the inclination angles for each pitch of 0.25 degrees and totaling the frequencies existing in each section, 0 The highest peak exists in the inclination angle section within the range of -15 degrees, and the total of the frequencies existing within the range of 0-15 degrees occupies a ratio of 50% or more of the entire degrees in the inclination angle frequency distribution graph. An inclination angle number distribution graph is shown, and 1.5-5. A modified α-type aluminum oxide layer having an average layer thickness of 9 μm;
Chemical vapor deposition of the hard coating layer composed of (a-1) to (a-3) above ,
( 2 ) Next , on the entire surface of the modified α-type aluminum oxide layer which is the upper layer of the hard coating layer,
(B-1) The lower layer has an average layer thickness of 0.1 to 3 μm, and
Composition formula: TiO x ,
, The central part in the thickness direction is measured with an Auger spectrometer, and the atomic ratio is
X: 1.2 to 1.7,
Satisfying titanium oxide layer,
(B-2) The upper layer has an average layer thickness of 0.05 to 2 μm, and
Composition formula: TiN 1-Y (O) Y ,
[However, (O) indicates the diffused oxygen from the titanium oxide layer, which is the lower layer during the deposition of the upper layer ], and the central part in the thickness direction is also measured with an Auger spectrometer. , Also in atomic ratio,
Y: 0.01 to 0.4
Satisfying titanium oxynitride layer,
In the state where the abrasive layer composed of (b-1) and (b-2) is formed by chemical vapor deposition,
In wet blasting, as a spraying abrasive, a polishing liquid containing 15 to 60% by mass of aluminum oxide fine particles in a proportion of the total amount with water is sprayed,
In the coexistence of pulverized titanium oxide fine particles and pulverized titanium oxynitride fine particles obtained by pulverizing and atomizing the above-mentioned abrasive layer by spraying aluminum oxide fine particles that are spray abrasives, and the aluminum oxide fine particles as spray abrasives, The rake face portion and the flank face portion including at least the cutting edge ridge line portion of the modified α-type aluminum oxide layer constituting the upper layer of the hard coating layer are polished, and the surface roughness of these polished surfaces is compliant with JIS B0601- According to the measurement based on 1994, Ra: 0.2 μm or less,
A method of manufacturing a surface-coated cermet cutting tool that exhibits excellent chipping resistance in a high-speed cutting of difficult-to-cut materials characterized by
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