阅读说明：本技术 被覆切削工具 (Coated cutting tool ) 是由 西泽普贤 于 2020-08-20 设计创作，主要内容包括：本发明提供一种与以往相比可以延长工具寿命的被覆切削工具。该被覆切削工具具备由立方晶氮化硼烧结体形成的基材和形成于该基材上的被覆层,被覆层具有由Ti(C_xN_(1-x))形成的Ti的碳氮化物层,Ti的碳氮化物层的平均厚度为0.5μm以上5.0μm以下,在Ti的碳氮化物层中,从基材侧开始的厚度75％的位置的C元素的原子比R75高于从基材侧开始的厚度25％的位置的C元素的原子比R25,在Ti的碳氮化物层中,(111)面的织构系数TC(111)为1.0以上2.0以下,在Ti的碳氮化物层的X射线衍射测定中,当将ψ角度设为0°、30°、50°以及70°而分别进行测定时,2θ的最大值与最小值之差的绝对值在(111)面中为0.1°以下。(The invention provides a coated cutting tool which can prolong the service life of the tool compared with the prior art. The coated cutting tool comprises a substrate formed by cubic boron nitride sintered body and a coating layer formed on the substrate, wherein the coating layer comprises Ti (C) x N 1‑x ) A Ti carbonitride layer formed of a Ti carbonitride layer having an average thickness of 0.5 to 5.0 [ mu ] m, wherein the atomic ratio R75 of the C element at a position 75% thick from the base material side is higher than the atomic ratio R25 of the C element at a position 25% thick from the base material side, and the texture of the (111) plane in the Ti carbonitride layerThe coefficient TC (111) is 1.0-2.0, and the absolute value of the difference between the maximum value and the minimum value of 2 theta is 0.1 DEG or less in the (111) plane when measured by X-ray diffraction measurement of the Ti carbonitride layer with the phi angles set to 0 DEG, 30 DEG, 50 DEG, and 70 deg, respectively.)

1. A coated cutting tool comprising a base material formed of a cubic boron nitride sintered body and a coating layer formed on the base material, wherein,

the coating layer has a carbonitride layer of Ti formed with a composition represented by the following formula (i),

Ti(C_xN_1-x) (i)

wherein x represents an atomic ratio of the C element to the total amount of the C element and the N element in a position 50% thick from the base material side in the carbonitride layer of Ti, and satisfies 0.1< x <0.5,

the average thickness of the Ti carbonitride layer is 0.5 to 5.0 [ mu ] m,

in the carbonitride layer of Ti, an atomic ratio R75 of the C element to the total amount of the C element and the N element at a position 75% thick from the base material side is higher than an atomic ratio R25 of the C element to the total amount of the C element and the N element at a position 25% thick from the base material side,

in the carbonitride layer of Ti, the texture coefficient TC (111) of the (111) plane represented by the following formula (1) is 1.0 to 2.0,

in the X-ray diffraction measurement of the Ti carbonitride layer, when the phi angle is set to 0 DEG, 30 DEG, 50 DEG and 70 DEG, respectively, the absolute value of the difference between the maximum value and the minimum value of 2 theta expressed by the following formula (2) is 0.1 DEG or less in the (111) plane,

[ mathematical formula 1]

In the formula (1), I (h k l) represents the peak intensity of the (h k l) plane in the X-ray diffraction of the Ti carbonitride layer, I₀(h kl) represents the standard diffraction intensity of the (h kl) plane in ICDD card No. 00-042-1488, where (h kl) refers to the six crystal planes (111), (200), (220), (311), (420) and (422),

the absolute value of the difference between the maximum value and the minimum value of 2 θ is |2 θ max-2 θ min | (2)

In the formula (2), 2 θ max represents the maximum value among the positions 2 θ of the peaks of the crystal planes when the ψ angle is 0 °, 30 °, 50 °, and 70 °, and 2 θ min represents the minimum value among the positions 2 θ of the peaks of the crystal planes when the ψ angle is 0 °, 30 °, 50 °, and 70 °.

2. The coated cutting tool of claim 1,

in the X-ray diffraction measurement of the Ti carbonitride layer, when the angle ψ is set to 0 °, 30 °, 50 °, and 70 °, respectively, the absolute value of the difference between the maximum value and the minimum value of 2 θ represented by the above formula (2) is 0.1 ° or less in the (200) plane.

3. The coated cutting tool of claim 1 or 2,

in the carbonitride layer of Ti, the difference (R75-R25) between the atomic ratio R25 of the C element to the total amount of the C element and the N element at a position 25% of the average thickness from the base material side and the atomic ratio R75 of the C element to the total amount of the C element and the N element at a position 75% of the average thickness from the base material side is 0.1 to 0.3.

4. The coated cutting tool according to any one of claims 1 to 3,

the coating layer has a lower layer between the base material and the carbonitride layer of Ti,

the lower layer is a single layer or a stacked layer of at least one selected from the group consisting of the following metal layers and the following compound layers,

the metal layer is formed of at least one metal element selected from the group consisting of Ti, Zr, Hf, V, Nb, Ta, Cr, Mo, W, Al, Si and Y,

the compound layer is formed of at least one metal element selected from the group consisting of Ti, Zr, Hf, V, Nb, Ta, Cr, Mo, W, Al, Si and Y and at least one element selected from the group consisting of C, N, O and B,

the lower layer has an average thickness of 0.1 to 5.0 [ mu ] m.

5. The coated cutting tool according to any one of claims 1 to 3,

the coating layer has a lower layer between the base material and the carbonitride layer of Ti,

the lower layer has an alternating stacked structure in which a1 st compound layer and a 2 nd compound layer are alternately stacked two or more times, the 1 st compound layer being formed of a composition represented by formula (I) below, the 2 nd compound layer being formed of a composition represented by formula (II) below,

the 1 st compound layer has an average thickness of 2nm to 500nm,

the 2 nd compound layer has an average thickness of 2nm to 500nm,

(Ti_yAl_1-y)N (I)

wherein y represents an atomic ratio of the Ti element to the total of the Ti element and the Al element and satisfies 0.1< y <0.5,

(Ti_zAl_1-z)N (II)

wherein z represents an atomic ratio of the Ti element to the total of the Ti element and the Al element, and satisfies 0.5. ltoreq. z.ltoreq.0.8.

6. The coated cutting tool according to any one of claims 1 to 5,

the average thickness of the entire coating layer is 1.5 μm or more and 8.0 μm or less.

Technical Field

The present invention relates to a coated cutting tool.

Background

Conventionally, a cubic boron nitride sintered body has been used as a cutting tool for work-hardened steel, heat-resistant alloy, and the like because of its high hardness and excellent thermal conductivity. In recent years, as a cutting tool, a coated cubic boron nitride sintered body tool in which a coating layer is coated on the surface of a base material formed of a cubic boron nitride sintered body is used in order to improve the machining efficiency.

Therefore, various techniques for improving the characteristics of such a coating layer have been proposed. For example, patent document 1 proposes a cutting tool made of a cubic boron nitride-based sintered material, in which a coating layer is formed by vapor deposition on the surface of a base material made of a cubic boron nitride-based sintered material, and the coating layer is composed of a lower layer formed of a composite nitride layer of titanium and aluminum, a1 st intermediate layer formed of a nitride layer of titanium, a 2 nd intermediate layer formed of a carbonitride layer of titanium, and an upper layer formed of a nitride layer of titanium.

Patent document

Patent document 1: japanese laid-open patent publication No. 2009-255282

Disclosure of Invention

In recent years, cutting at high speed, high feed, and deep feed have become more remarkable, and improvement in the chipping resistance of a tool compared to conventional tools has been demanded. In particular, cutting work in which a load acts on the coated cutting tool, such as hardened steel and heat resistant alloy, is increasing. Under such severe cutting conditions, in the conventional coated cutting tool, the coating layer has insufficient adhesion to the substrate, and therefore peeling occurs, and further, a defect occurs, and therefore, it is difficult to extend the tool life.

The cutting tool described in patent document 1 does not necessarily have sufficient chipping resistance under high-speed cutting conditions, and particularly, the coating layer has insufficient adhesion to a base material under conditions in which hard materials such as hardened steel and heat-resistant alloys are processed at high speeds.

The present invention has been made in view of the above circumstances, and an object thereof is to provide a coated cutting tool having excellent wear resistance and chipping resistance and having a long tool life.

The present inventors have conducted repeated studies on the extension of the tool life of a coated cutting tool, and as a result, have found that: the present inventors have found that, when a coated cutting tool is configured as described below, the adhesion between the base material and the coating layer is improved, whereby the chipping resistance can be improved, and therefore, the tool life of the coated cutting tool can be extended, leading to completion of the present invention.

That is, the gist of the present invention is as follows.

[1] A coated cutting tool comprising a base material formed of a cubic boron nitride sintered body and a coating layer formed on the base material, wherein,

the coating layer has a carbonitride layer of Ti formed with a composition represented by the following formula (i),

Ti(C_xN_1-x) (i)

(wherein x represents the atomic ratio of the C element to the total of the C element and the N element at a position 50% of the thickness of the Ti carbonitride layer from the base material side, and satisfies 0.1< x < 0.5.)

The average thickness of the Ti carbonitride layer is 0.5 to 5.0 μm,

in the above-mentioned Ti carbonitride layer, the atomic ratio R75 of the C element to the total amount of the C element and the N element at a position 75% thick from the base material side is higher than the atomic ratio R25 of the C element to the total amount of the C element and the N element at a position 25% thick from the base material side,

in the above-mentioned Ti carbonitride layer, the texture coefficient TC (111) of the (111) plane represented by the following formula (1) is 1.0 or more and 2.0 or less,

in the X-ray diffraction measurement of the Ti carbonitride layer, when the angle ψ is measured as 0 °, 30 °, 50 °, and 70 °, respectively, the absolute value of the difference between the maximum value and the minimum value of 2 θ represented by the following formula (2) is 0.1 ° or less in the (111) plane.

[ mathematical formula 1]

(in the formula (1), I (h k l) represents the peak intensity of the (h k l) plane in the X-ray diffraction of the Ti carbonitride layer, I₀(h kl) denotes ICDD card number 00-042-1488, (hkl) means six crystal planes of (111), (200), (220), (311), (420) and (422). )

The absolute value of the difference between the maximum value and the minimum value of 2 θ is |2 θ max-2 θ min | (2)

(in the formula (2), 2 θ max represents the maximum value among the positions 2 θ of the peaks of the crystal planes when the ψ angle is 0 °, 30 °, 50 °, and 70 °, and 2 θ min represents the minimum value among the positions 2 θ of the peaks of the crystal planes when the ψ angle is 0 °, 30 °, 50 °, and 70 °)

[2] The coated cutting tool according to [1], wherein, in the X-ray diffraction measurement of the Ti carbonitride layer, when the angle ψ is measured as 0 °, 30 °, 50 °, and 70 °, respectively, the absolute value of the difference between the maximum value and the minimum value of 2 θ represented by the formula (2) is 0.1 ° or less in the plane (200).

[3] The coated cutting tool according to [1] or [2], wherein in the Ti carbonitride layer, a difference (R75-R25) between an atomic ratio R25 of a C element to the total amount of the C element and the N element at a position of 25% of an average thickness from the base material side and an atomic ratio R75 of the C element to the total amount of the C element and the N element at a position of 75% of the average thickness from the base material side is 0.1 to 0.3.

[4] The coated cutting tool according to any one of [1] to [3],

the coating layer has a lower layer between the base material and the Ti carbonitride layer,

the lower layer is a single layer or a stacked layer of at least one selected from the group consisting of the following metal layers and the following compound layers,

the metal layer is formed of at least one metal element selected from the group consisting of Ti, Zr, Hf, V, Nb, Ta, Cr, Mo, W, Al, Si and Y,

the compound layer is formed of at least one metal element selected from the group consisting of Ti, Zr, Hf, V, Nb, Ta, Cr, Mo, W, Al, Si and Y and at least one element selected from the group consisting of C, N, O and B,

the lower layer has an average thickness of 0.1 to 5.0 [ mu ] m.

[5] The coated cutting tool according to any one of [1] to [3],

the coating layer has a lower layer between the base material and the Ti carbonitride layer,

the lower layer has an alternating stack structure in which a1 st compound layer and a 2 nd compound layer are alternately stacked two or more times, the 1 st compound layer is formed with a composition represented by formula (I), the 2 nd compound layer is formed with a composition represented by formula (II),

the average thickness of the 1 st compound layer is 2nm to 500nm,

the 2 nd compound layer has an average thickness of 2nm to 500 nm.

(Ti_yAl_1-y)N (I)

(wherein y represents the atomic ratio of Ti element to the total of Ti element and Al element, and satisfies 0.1< y < 0.5.)

(Ti_zAl_1-z)N (II)

(wherein z represents an atomic ratio of the Ti element to the total of the Ti element and the Al element, and satisfies 0.5. ltoreq. z.ltoreq.0.8.)

[6] The coated cutting tool according to any one of [1] to [5], wherein the average thickness of the entire coating layer is 1.5 μm or more and 8.0 μm or less.

The coated cutting tool of the present invention has excellent wear resistance and chipping resistance, and therefore has the effect of having a longer tool life than conventional tools.

Drawings

Fig. 1 is a schematic view showing an example of a coated cutting tool of the present invention.

Detailed Description

Hereinafter, a mode for carrying out the present invention (hereinafter, simply referred to as "the present embodiment") will be described in detail, but the present invention is not limited to the present embodiment described below. The present invention can be variously modified within a range not exceeding the gist thereof. It should be noted that positional relationships such as up, down, left, and right in the drawings are based on the positional relationships shown in the drawings unless otherwise specified. The dimensional ratios in the drawings are not limited to the illustrated ratios.

The coated cutting tool of the present embodiment comprises a base material formed of a cubic boron nitride sintered body and a coating layer formed on the base material, the coating layer having a Ti carbonitride layer formed with a composition represented by the following formula (i),

Ti(C_xN_1-x) (i)

(wherein x represents the atomic ratio of the C element to the total of the C element and the N element at a position 50% thick from the base material side in the carbonitride layer of Ti, and satisfies 0.1< x < 0.5.)

In the carbonitride layer of Ti, the atomic ratio of the C element to the total amount of the C element and the N element (hereinafter, also referred to as "R75") at a position 75% thick from the base material side is higher than the atomic ratio of the C element to the total amount of the C element and the N element (hereinafter, also referred to as "R25") at a position 25% thick from the base material side,

in the Ti carbonitride layer, the texture coefficient TC (111) of the (111) plane represented by the following formula (1) is 1.0 to 2.0,

in the X-ray diffraction measurement of the Ti carbonitride layer, when the ψ angle is measured as 0 °, 30 °, 50 °, and 70 °, respectively, the absolute value of the difference between the maximum value and the minimum value of 2 θ represented by the following formula (2) is 0.1 ° or less in the (111) plane.

[ mathematical formula 1]

(in the formula (1), I (h k l) represents the peak intensity of the (h k l) plane in X-ray diffraction of the Ti carbonitride layer, I₀(h kl) represents the standard diffraction intensity of the (h kl) plane in ICDD card No. 00-042-1488, where (h kl) refers to the six crystal planes (111), (200), (220), (311), (420) and (422). )

The absolute value of the difference between the maximum value and the minimum value of 2 θ is |2 θ max-2 θ min | (2)

(in the formula (2), 2 θ max represents the maximum value among the positions 2 θ of the peaks of the crystal planes at 0 °, 30 °, 50 ° and 70 °, and 2 θ min represents the minimum value among the positions 2 θ of the peaks of the crystal planes at 0 °, 30 °, 50 ° and 70 °)

In the coated cutting tool of the present embodiment, the base material is formed of a sintered body containing cubic boron nitride, and therefore, for example, the coated cutting tool is excellent in wear resistance and chipping resistance in the processing of hardened steel or heat-resistant alloy. Further, in the coated cutting tool of the present embodiment, if at least one of the coating layers has a carbonitride layer of Ti formed of the composition represented by the above formula (i), the wear resistance will be improved. Further, if the atomic ratio x of the element C in the above formula (i) exceeds 0.1, the hardness of the carbonitride layer of Ti will be increased. Therefore, the wear resistance of the coated cutting tool of the present embodiment will be improved. On the other hand, if the atomic ratio x of the element C in the above formula (i) is less than 0.5, the toughness of the Ti carbonitride layer will be improved. Therefore, the chipping resistance of the coated cutting tool of the present embodiment will be improved. In addition, if the average thickness of the Ti carbonitride layer is 0.5 μm or more, the effect of having the Ti carbonitride layer is exhibited, and the wear resistance of the coated cutting tool is improved. On the other hand, if the average thickness of the carbonitride layer of Ti is 5.0 μm or less, the adhesiveness will be improved, whereby the occurrence of peeling can be suppressed. Therefore, the chipping resistance of the coated cutting tool of the present embodiment will be improved. In addition, in the carbonitride layer of Ti, if the texture coefficient TC (111) of the (111) plane expressed by the above formula (1) is 1.0 or more, the (111) plane is a close-packed plane (close-packed plane), and therefore the ratio thereof becomes high, thereby increasing the hardness. Therefore, the wear resistance of the coated cutting tool of the present embodiment will be improved. On the other hand, in the Ti carbonitride layer, if the texture coefficient TC (111) represented by the above formula (1) is 2.0 or less, the toughness is excellent. Therefore, the chipping resistance of the coated cutting tool of the present embodiment will be improved. In addition, in the Ti carbonitride layer, if R75 is set higher than R25, the increase in deformation between the base material and the lower layer is suppressed, whereby the adhesion can be improved and the hardness on the surface side can be improved. Therefore, the chipping resistance and wear resistance of the coated cutting tool of the present embodiment will be improved. In addition, when the X-ray diffraction measurement of the Ti carbonitride layer was performed with the ψ angles set to 0 °, 30 °, 50 °, and 70 °, respectively, the absolute value of the difference between the maximum value and the minimum value of 2 θ represented by the above formula (2) was 0.1 ° or less in the (111) plane, which indicates that the anisotropic deformation of the Ti carbonitride layer was low. If the anisotropic deformation is reduced, the occurrence of surface defects and slip (slip) can be suppressed, and thus the adhesion between the carbonitride layer of Ti and the substrate or underlying layer will be improved. Therefore, the chipping resistance of the coated cutting tool of the present embodiment will be improved. By combining such a structure, the wear resistance and the chipping resistance of the coated cutting tool according to the present embodiment are improved, and therefore, it is considered that the tool life can be extended.

Fig. 1 is a schematic cross-sectional view showing an example of a coated cutting tool according to the present embodiment. The coated cutting tool 5 has a substrate 1 and a coating layer 4 formed on the surface of the substrate 1, and in the coating layer 4, a lower layer 2 and a carbonitride layer 3 of Ti are sequentially stacked upward. However, the coated cutting tool of the present embodiment is not limited to the above-described structure, and the coating layer may include at least the above-described carbonitride layer of Ti. For example, in the coated cutting tool of the present embodiment, the coating layer may include only the above-described carbonitride layer of Ti, or may further include a lower layer described below in addition thereto.

The coated cutting tool of the present embodiment includes a base material formed of a cubic boron nitride sintered body and a coating layer formed on the base material. In the coated cutting tool of the present embodiment, the base material is formed of a sintered body containing cubic boron nitride, and therefore, for example, the coated cutting tool is excellent in wear resistance and chipping resistance in the processing of hardened steel or heat-resistant alloy.

In the coated cutting tool of the present embodiment, the sintered body containing cubic boron nitride preferably contains 65 vol% to 85 vol% cubic boron nitride and 15 vol% to 35 vol% binder phase. In the coated cutting tool of the present embodiment, if the sintered body containing cubic boron nitride contains 65 vol% or more of cubic boron nitride and 35 vol% or less of binder phase, the chipping resistance tends to be improved. On the other hand, with the coated cutting tool of the present embodiment, if the cubic boron nitride containing sintered body contains 85 vol% or less of cubic boron nitride and 15 vol% or more of a binder phase, the wear resistance tends to be improved.

In the coated cutting tool of the present embodiment, the binder phase preferably contains at least one metal element selected from the group consisting of Ti (titanium), Zr (zirconium), Hf (hafnium), V (vanadium), Nb (niobium), Ta (tantalum), Cr (chromium), Mo (molybdenum), W (tungsten), Al (aluminum), and Co (cobalt). Alternatively, the binder phase preferably contains a compound of at least one metal element selected from the group consisting of Ti, Zr, Hf, V, Nb, Ta, Cr, Mo, W, Al, and Co, and at least one element selected from the group consisting of C (carbon), N (nitrogen), O (oxygen), and B (boron). In the coated cutting tool of the present embodiment, if the binder phase contains such a compound, the balance between the wear resistance and the chipping resistance tends to be excellent.

[ carbonitride layer of Ti ]

In the coated cutting tool of the present embodiment, at least one of the coating layers has a Ti carbonitride layer formed with a composition represented by the following formula (i).

Ti(C_xN_1-x) (i)

(wherein x represents the atomic ratio of the C element to the total of the C element and the N element at a position 50% thick from the base material side in the carbonitride layer of Ti, and satisfies 0.1< x < 0.5.)

In the coated cutting tool of the present embodiment, if at least one of the coating layers has a carbonitride layer of Ti formed of the composition represented by formula (i) above, the wear resistance will be improved. Further, if the atomic ratio x of the element C in the above formula (i) exceeds 0.1, the hardness of the carbonitride layer of Ti will be increased. Therefore, the wear resistance of the coated cutting tool of the present embodiment will be improved. On the other hand, if the atomic ratio x of the element C in the above formula (i) is less than 0.5, the toughness of the Ti carbonitride layer will be improved. Therefore, the chipping resistance of the coated cutting tool of the present embodiment will be improved. From the same viewpoint, the atomic ratio x of the C element in the formula (i) preferably satisfies 0.15< x <0.48, more preferably satisfies 0.2< x <0.45, and still more preferably satisfies 0.21< x < 0.44.

In the coated cutting tool of the present embodiment, for example, the composition of the coating layer is represented by Ti (C)_0.35N_0.65) In the case of (2), the atomic ratio of the C element to the total amount of the C element and the N element was 0.35, and the atomic ratio of the N element to the total amount of the C element and the N element was 0.65. That is, it means that the amount of the C element is 35 at% to the total amount of the C element and the N element, and the amount of the N element is 65 at% to the total amount of the C element and the N element.

In the coated cutting tool of the present embodiment, in the carbonitride layer of Ti, the atomic ratio of the C element to the total amount of the C element and the N element (hereinafter, also referred to as "R75") at a position 75% thick from the base material side is higher than the atomic ratio of the C element to the total amount of the C element and the N element (hereinafter, also referred to as "R25") at a position 25% thick from the base material side. In the carbonitride layer of Ti, if R75 is made higher than R25, the increase in deformation between the carbonitride layer and the base material or the lower layer is suppressed, whereby the adhesion can be improved and the hardness on the surface side can be improved. Therefore, the chipping resistance and wear resistance of the coated cutting tool of the present embodiment will be improved.

In the coated cutting tool of the present embodiment, in the carbonitride layer of Ti, the difference (R75 to R25) between the atomic ratio R25 of the C element to the total amount of the C element and the N element at a position 25% thick from the base material side and the atomic ratio R75 of the C element to the total amount of the C element and the N element at a position 75% thick from the base material side is preferably 0.1 to 0.3. In the carbonitride layer of Ti, if the difference in atomic ratio of the C element (R75 to R25) is 0.1 or more, the above-described effect of improving the adhesion and the effect of improving the wear resistance tend to be further improved. On the other hand, if the difference in atomic ratio of the C element (R75-R25) is 0.3 or less, the deformation in the Ti carbonitride layer can be suppressed to be small. Therefore, the coated cutting tool of the present embodiment tends to have further improved chipping resistance.

In the present embodiment, the atomic ratio of each element in the Ti carbonitride layer can be measured by the method described in the following examples. In the present embodiment, the "positions 25%, 50%, and 75% in thickness from the base material side" refer to positions 25%, 50%, and 75% in order from the base material side toward the surface with respect to 100% in thickness of the Ti carbonitride layer as a measurement position.

In the coated cutting tool of the present embodiment, the average thickness of the Ti carbonitride layer is 0.5 μm or more and 5.0 μm or less. If the average thickness of the Ti carbonitride layer is 0.5 μm or more, the effect of the Ti carbonitride layer is exhibited and the wear resistance of the coated cutting tool is improved. On the other hand, if the average thickness of the carbonitride layer of Ti is 5.0 μm or less, the adhesiveness will be improved, whereby the occurrence of peeling can be suppressed. Therefore, the chipping resistance of the coated cutting tool of the present embodiment will be improved. From the same viewpoint, the average thickness of the Ti carbonitride layer is preferably 0.8 μm or more and 4.8 μm or less, and more preferably 1.0 μm or more and 4.7 μm or less.

In the carbonitride layer of Ti, the texture coefficient TC (111) of the (111) plane represented by the following formula (1) is 1.0 to 2.0.

[ mathematical formula 2]

(in the formula (1), I (h k l) represents the peak intensity of the (h k l) plane in X-ray diffraction of the Ti carbonitride layer, I₀(h kl) represents the standard diffraction intensity of the (h kl) plane in ICDD card No. 00-042-1488, where (h kl) refers to the six crystal planes (111), (200), (220), (311), (420) and (422). )

In the carbonitride layer of Ti, if the texture coefficient TC (111) of the (111) plane represented by the above formula (1) is 1.0 or more, the (111) plane is a closest-packed plane, and therefore the ratio thereof increases, thereby increasing the hardness. Therefore, the wear resistance of the coated cutting tool of the present embodiment will be improved. On the other hand, if the texture coefficient TC (111) represented by the above formula (1) is 2.0 or less in the Ti carbonitride layer, the toughness is excellent. Therefore, the chipping resistance of the coated cutting tool of the present embodiment will be improved. From the same viewpoint, the texture coefficient TC (111) of the (111) plane represented by the above formula (1) is preferably 1.1 to 1.9, and more preferably 1.2 to 1.9.

In the present embodiment, the texture coefficient TC (111) of the (111) plane of the Ti carbonitride layer can be calculated in the following manner. For the coated cutting tool, at the output: 50kV, 250mA, incident side shuttle slit: 5 °, divergent longitudinal slit: 2/3 °, divergent longitudinal limit slit: 5mm, scattering slit: 2/3 °, light receiving side shuttle slit: 5 °, light receiving slit: 0.3mm, BENT monochromator, light-receiving monochromatic slit: 0.8mm, sampling width: 0.01 °, scanning speed: 4 °/min, 2 θ measurement range: x-ray diffraction measurement of an optical system by 2 theta/theta focusing method using Cu-Ka rays was performed under conditions of 25 DEG to 140 deg. As the device, an X-ray diffraction device (model No. 'RINT TTRIII') manufactured by Kabushiki Kaisha リガク was used. The peak intensity of each crystal face of the Ti carbonitride layer and the like is obtained from the X-ray diffraction spectrum. From the peak intensity of each crystal plane obtained by the above formula (1), the texture coefficient TC (111) of the (111) plane in the Ti carbonitride layer or the like is calculated.

In the coated cutting tool of the present embodiment, when the angle ψ is measured as 0 °, 30 °, 50 °, and 70 ° in the X-ray diffraction measurement of the Ti carbonitride layer, the absolute value of the difference between the maximum value and the minimum value of 2 θ represented by the following formula (2) (hereinafter, also referred to as "absolute value of the difference between the maximum value and the minimum value of 2 θ") is 0.1 ° or less in the (111) plane.

The absolute value of the difference between the maximum value and the minimum value of 2 θ is |2 θ max-2 θ min | (2)

(in the formula (2), 2 θ max represents the maximum value among the positions 2 θ of the peaks of the crystal planes when the ψ angle is 0 °, 30 °, 50 °, and 70 °, and 2 θ min represents the minimum value among the positions 2 θ of the peaks of the crystal planes when the ψ angle is 0 °, 30 °, 50 °, and 70 °)

In the X-ray diffraction measurement of the Ti carbonitride layer, if the absolute value of the difference between the maximum value and the minimum value of 2 θ is 0.1 ° or less in the (111) plane, it indicates that the anisotropic deformation of the Ti carbonitride layer is small. If the anisotropic deformation is reduced, the occurrence of surface defects and slip can be suppressed, and thus the adhesion between the Ti carbonitride layer and the substrate or the lower layer will be improved. Therefore, the chipping resistance of the coated cutting tool of the present embodiment will be improved. From the same viewpoint, the absolute value of the difference between the maximum value and the minimum value of 2 θ of the (111) plane is preferably 0.09 ° or less, and more preferably 0.08 ° or less. (111) The lower limit of the absolute value of the difference between the maximum value and the minimum value of the 2 θ of the surface is not particularly limited, and is, for example, 0 ° or more.

In the coated cutting tool of the present embodiment, when the angle ψ is measured as 0 °, 30 °, 50 °, and 70 ° in the X-ray diffraction measurement of the Ti carbonitride layer, the absolute value of the difference between the maximum value and the minimum value of 2 θ represented by the above formula (2) is preferably 0.1 ° or less in the plane (200).

In the X-ray diffraction measurement of the Ti carbonitride layer, if the absolute value of the difference between the maximum value and the minimum value of 2 θ is 0.1 ° or less in the (200) plane, it means that the anisotropic deformation of the Ti carbonitride layer is small. If the anisotropic deformation is reduced, the occurrence of surface defects and slip can be suppressed, and thus the adhesion between the Ti carbonitride layer and the substrate or the lower layer will be improved. Therefore, the chipping resistance of the coated cutting tool of the present embodiment will be improved. From the same viewpoint, the absolute value of the difference between the maximum value and the minimum value of 2 θ of the (200) plane is more preferably 0.09 ° or less. (200) The lower limit of the absolute value of the difference between the maximum value and the minimum value of the 2 θ of the surface is not particularly limited, and is, for example, 0 ° or more.

In the present embodiment, the absolute value of the difference between the maximum value and the minimum value of 2 θ in the X-ray diffraction measurement of the Ti carbonitride layer was measured in the following manner. As the measuring apparatus, an X-ray diffraction analyzer equipped with a two-dimensional detector can be used. The X-ray tube was designated as Cu-K.alpha.and the measurement was designated as 2. theta. -phi. measurement. With respect to the peak position of the (111) plane or the (200) plane of the Ti carbonitride layer, at the ψ angle: the frames were measured at 10 ° intervals in the range of 0 ° to 70 °. In the measurement of each frame, the measurement time is adjusted so that the intensity of the crystal plane (111 plane or (200) plane) becomes 2 to 3 times the background count (count). Since the strength differs depending on the thickness of the layer or the like, the time is adjusted for each sample. For the analysis, the peak positions 2 θ of the (111) plane and the (200) plane can be specified using software attached to the X-ray diffraction analyzer. When the angle ψ is measured as 0 °, 30 °, 50 °, and 70 °, the absolute value of the difference between the maximum value and the minimum value of 2 θ represented by the following formula (2) is calculated.

The absolute value of the difference between the maximum value and the minimum value of 2 θ is |2 θ max-2 θ min | (2)

(in the formula (2), 2 θ max represents the maximum value among the positions 2 θ of the peaks of the crystal plane ((111) plane or (200) plane) when the ψ angle is 0 °, 30 °, 50 °, and 70 °, and 2 θ min represents the minimum value among the positions 2 θ of the peaks of the crystal plane ((111) plane or (200) plane) when the ψ angle is 0 °, 30 °, 50 °, and 70 °)

[ lower layer ]

In the coated cutting tool of the present embodiment, the coating layer preferably has a lower layer between the base material and the carbonitride layer of Ti. If the coating layer has a lower layer between the base material and the carbonitride layer of Ti, the wear resistance and chipping resistance of the coated cutting tool tend to be further improved.

The lower layer preferably contains a single layer or a stacked layer of at least one selected from the group consisting of the metal layers described below and the compound layers described below. If the lower layer contains a single layer or a laminate of at least one selected from the group consisting of the metal layers described below and the compound layers described below, the wear resistance and the chipping resistance of the coated cutting tool tend to be further improved.

(Metal layer)

A metal layer formed of at least one metal element selected from the group consisting of Ti, Zr, Hf, V, Nb, Ta, Cr, Mo, W, Al, Si and Y.

(Compound layer)

A compound layer formed of at least one metal element selected from the group consisting of Ti, Zr, Hf, V, Nb, Ta, Cr, Mo, W, Al, Si and Y, and at least one element selected from the group consisting of C, N, O and B.

The metal layer is further preferably formed of at least one metal element selected from the group consisting of Ti and W.

The compound layer is further preferably formed of at least one metal element selected from the group consisting of Ti, Cr, Mo, W, Al, and Si, and N.

Among them, if the lower layer is a nitride layer, an effect of reducing deformation between the lower layer and the carbonitride layer of Ti can be obtained.

The lower layer preferably has an alternating stacked structure formed by alternately stacking a1 st compound layer formed with a composition represented by formula (I) below and a 2 nd compound layer formed with a composition represented by formula (II) below two or more times. If the lower layer has such an alternate lamination structure, cracks occurring in the coating layer during cutting tend to be suppressed from progressing to the substrate.

(Ti_yAl_1-y)N (I)

(wherein y represents the atomic ratio of Ti element to the total of Ti element and Al element, and satisfies 0.1< y < 0.5.)

(Ti_zAl_1-z)N (II)

(wherein z represents an atomic ratio of the Ti element to the total of the Ti element and the Al element, and satisfies 0.5. ltoreq. z.ltoreq.0.8.)

The average thickness of the 1 st compound layer is preferably 2nm to 500nm, more preferably 3nm to 400nm, and still more preferably 5nm to 300 nm.

The average thickness of the 2 nd compound layer is preferably 2nm to 500nm, more preferably 3nm to 400nm, and further preferably 5nm to 300 nm.

In the alternate lamination structure having the lower layer, the number of repetition of the 1 st compound layer and the 2 nd compound layer is 2 or more, preferably 4 to 100. In this embodiment, when a layer is formed on each of the 1 st compound layer and the 2 nd compound layer, "the number of repetitions" is one.

In the coated cutting tool of the present embodiment, the average thickness of the lower layer is preferably 0.1 μm or more and 5.0 μm or less. If the average thickness of the lower layer is 0.1 μm or more, the surface of the substrate can be uniformly covered, and thus the adhesion between the substrate and the coating layer will be improved. Therefore, the chipping resistance of the coated cutting tool of the present embodiment will be improved. On the other hand, if the average thickness of the lower layer is 5.0 μm or less, the strength of the lower layer can be suppressed from being reduced, and thus the chipping resistance of the coated cutting tool of the present embodiment will be improved. Among these, from the same viewpoint as described above, the average thickness of the lower layer is preferably 0.3 μm to 4.5 μm, and more preferably 1.0 μm to 4.5 μm.

In the coated cutting tool of the present embodiment, the average thickness of the entire coating layer is preferably 1.5 μm or more and 8.0 μm or less. If the average thickness of the entire coating layer is 1.5 μm or more, the wear resistance tends to be further improved. On the other hand, if the average thickness of the entire coating layer is 8.0 μm or less, the defect resistance tends to be further improved. From the same viewpoint, in the coated cutting tool of the present embodiment, the average thickness of the entire coating layer is more preferably 1.5 μm or more and 7.0 μm or less.

In the coated cutting tool of the present embodiment, the method for producing the coating layer is not particularly limited, and examples thereof include physical vapor deposition methods such as ion plating, arc ion plating, sputtering, and ion mixing. If the coating layer is formed by physical vapor deposition, sharp edges can be formed, which is preferable. Among them, arc ion plating is more preferable because the adhesion between the coating layer and the substrate is more excellent.

The method for manufacturing the coated cutting tool according to the present embodiment will be described with reference to specific examples. The method for manufacturing the coated cutting tool according to the present embodiment is not particularly limited as long as the structure of the coated cutting tool can be realized.

In the coated cutting tool of the present embodiment, the substrate formed of the sintered body containing cubic boron nitride is not particularly limited, and can be produced by a method including the following steps (a) to (H), for example.

Step (A): mixing 50 to 90 vol% of cubic boron nitride and 10 to 50 vol% of binder phase powder (wherein the total amount is 100 vol%). The powder of the binder phase preferably contains at least one metal element selected from the group consisting of Ti, Zr, Hf, V, Nb, Ta, Cr, Mo, W, Al, and Co. Alternatively, the powder of the binder phase preferably contains a compound of at least one metal element selected from the group consisting of Ti, Zr, Hf, V, Nb, Ta, Cr, Mo, W, Al, and Co and at least one element selected from the group consisting of carbon, nitrogen, oxygen, and boron.

A step (B): the raw material powder obtained in step (a) is mixed by wet ball milling for 5 to 24 hours using hard alloy balls.

Step (C): the mixture obtained in step (B) is molded into a predetermined shape to obtain a molded body.

A step (D): and (C) sintering the compact obtained in step (C) while holding it for a predetermined time at a sintering temperature in the range of 1300 to 1500 ℃ at a pressure of 4.0 to 7.0GPa in an ultrahigh pressure generator.

Step (E): the sintered body obtained in step (D) is cut out by an electric discharge machine in accordance with the shape of the tool.

A step (F): a base body made of cemented carbide is prepared.

Step (G): the sintered body cut in the step (E) is joined to the base prepared in the step (F) by brazing or the like.

Step (H): the tool obtained in step (G) is subjected to honing.

The coating layer used in the present embodiment is not particularly limited, and can be produced by the following method, for example.

The base material processed into the tool shape is stored in a reaction vessel of a physical vapor deposition apparatus, and a metal evaporation source is provided in the reaction vessel. Then, the inside of the reaction vessel was evacuated until a pressure of 1.0X 10 was reached^-2Heating the substrate by a heater in the reaction vessel under vacuum of Pa or lessUntil the temperature reaches 200-800 ℃. After heating, argon (Ar) gas was introduced into the reaction vessel so that the pressure in the reaction vessel became 0.5Pa to 5.0 Pa. Applying a bias voltage of-500V to-200V to the substrate under an Ar atmosphere having a pressure of 0.5Pa to 5.0Pa, and applying a current of 40A to 50A to the tungsten wire in the reaction vessel to perform an ion bombardment treatment using Ar on the surface of the substrate. After the ion bombardment treatment is carried out on the surface of the base material, the interior of the reaction vessel is vacuumized until the pressure is 1.0 x 10^-2Vacuum below Pa.

Then, the base material is controlled to reach 350-700 ℃, and Ar and N are added₂And acetylene gas (C)₂H₂) Introducing the mixture into a reaction vessel so that the pressure in the reaction vessel is 2.0 to 5.0 Pa. Then, a bias voltage of-150V to-30V is applied to the base material, and arc discharge with a current of 80A to 200A is applied to evaporate the metal evaporation sources corresponding to the metal components of the respective layers, thereby starting to form a Ti carbonitride layer on the surface of the base material. Here, acetylene gas (C) introduced into the reaction vessel is introduced₂H₂) The flow rate of (B) is gradually increased from the start of film formation to the end of film formation.

In the carbonitride layer of Ti used in the present embodiment, the term "carbonitride layer" is used to indicate Ti (C)_xN_1-x) The atomic ratio x of the element C to the total amount of the elements C and N is set to a desired value, and for example, Ar and N introduced into the reaction vessel are controlled in the process of forming the above-mentioned carbonitride layer of Ti₂And C₂H₂The ratio of (A) to (B) is as follows. For example, the larger the amount of C introduced into the reaction vessel₂H₂The atomic ratio x of the C element tends to increase as the ratio (A) is higher. In addition, in the process of forming the above-mentioned carbonitride layer of Ti, acetylene gas (C) introduced into the reaction vessel was used₂H₂) The flow rate of (b) may be gradually increased from the start of film formation to the end of film formation, and the atomic ratio x of the element C may be gradually increased toward the surface opposite to the base material with respect to the composition of the carbonitride layer of Ti. That is, in the carbonitride layer of Ti, the C element may be set to the total of the C element and the N element at a position 75% of the thickness from the base material sideThe atomic ratio of the amount is higher than the atomic ratio of the C element to the total amount of the C element and the N element at a position 25% in thickness from the substrate side. Further, acetylene gas (C) introduced into the reaction vessel₂H₂) The larger the amount of change in the flow rate of (b), the larger the difference in atomic ratio x of the C element (the difference in atomic ratio x of the C element between the position of 75% and the position of 25% in thickness from the substrate side) tends to be, the larger the difference in atomic ratio x of the C element up to the surface on the opposite side from the substrate side tends to be.

In the Ti carbonitride layer used in the present embodiment, in order to set the absolute value of the difference between the maximum value and the minimum value of 2 θ of the (111) plane and the (200) plane to a desired value, for example, acetylene gas (C) introduced into the reaction vessel is controlled in the process of forming the Ti carbonitride layer₂H₂) The amount of change in the flow rate of (a) is sufficient. Acetylene gas (C) introduced into the reaction vessel₂H₂) The smaller the amount of change in flow rate of (2), the lower the anisotropic deformation, and the smaller the absolute value of the difference between the maximum value and the minimum value of 2 θ in the (111) plane and the (200) plane.

In the Ti carbonitride layer used in the present embodiment, in order to set the texture coefficient TC (111) of the (111) plane to a desired value, for example, acetylene gas (C) introduced into the reaction vessel is controlled in the process of forming the Ti carbonitride layer₂H₂) And nitrogen (N)₂) The ratio of the mixed gas (2) to (3). In addition, for example, in the process of forming the above-described Ti carbonitride layer, the texture coefficient TC (111) of the (111) plane can be controlled to a desired value by adjusting the current value of arc discharge when evaporating the metal evaporation source corresponding to the metal component of each layer. Specifically, the texture coefficient TC (111) of the (111) plane tends to increase as the current value of arc discharge decreases.

The coating layer used in the present embodiment can be produced, for example, by the following method when a lower layer is formed between the base material and the Ti carbonitride layer.

First, a base material processed into a tool shape is stored in a reaction vessel of a physical vapor deposition apparatus, and a metal evaporation source is provided in the reaction vessel. Followed byThe reaction vessel was evacuated until a pressure of 1.0X 10 was reached^-2Heating the substrate by a heater in the reaction vessel under the vacuum of Pa until the temperature reaches 200-800 ℃. After heating, argon (Ar) gas is introduced into the reaction vessel so that the pressure in the reaction vessel becomes 0.5Pa to 5.0 Pa. Applying a bias voltage of-500V to-200V to the substrate in an Ar atmosphere at a pressure of 0.5Pa to 5.0Pa, and applying a current of 40A to 50A to the tungsten wire in the reaction vessel to subject the surface of the substrate to ion bombardment treatment using Ar. After the ion bombardment treatment is carried out on the surface of the base material, the interior of the reaction vessel is vacuumized until the pressure is 1.0 x 10^-2Vacuum below Pa.

Then, the substrate is controlled to a temperature of 350 ℃ to 700 ℃, and nitrogen (N) is introduced into the substrate₂) And/or Ar is introduced into the reaction vessel, and the pressure in the reaction vessel is set to 2.0 to 5.0 Pa. Then, a bias voltage of-120V to-30V is applied to the substrate, and arc discharge with a current of 80A to 200A is applied to evaporate the metal evaporation sources corresponding to the metal components of the respective layers, thereby starting the formation of the lower layer on the surface of the substrate.

As the lower layer, in order to form an alternate stacked structure of the 1 st compound layer and the 2 nd compound layer, under the above conditions, two or more kinds of metal evaporation sources are alternately evaporated by arc discharge, and each compound layer may be alternately formed. The thickness of each compound layer constituting the alternately laminated structure can be controlled by adjusting the arc discharge time of each metal evaporation source.

After the lower layer is formed, the base material is controlled to reach 350-700 deg.C, Ar and N are added₂And acetylene gas (C)₂H₂) Introducing the mixture into a reaction vessel, and controlling the pressure in the reaction vessel to be 2.0-5.0 Pa. Then, a bias voltage of-150V to-30V is applied to the base material, and arc discharge with a current of 80A to 200A is performed to evaporate the metal evaporation sources corresponding to the metal components of the respective layers, thereby starting to form a Ti carbonitride layer on the surface of the lower layer. Here, acetylene gas (C) introduced into the reaction vessel is introduced₂H₂) The flow rate of (B) is gradually increased from the start of film formation to the end of film formation.

The thickness of each layer constituting the coating layer used in the coated cutting tool of the present embodiment can be measured from the cross-sectional structure of the coated cutting tool using an optical microscope, a Scanning Electron Microscope (SEM), a Transmission Electron Microscope (TEM), or the like. The average thickness of each layer used in the coated cutting tool of the present embodiment can be obtained by the following method: the thickness of each layer was measured at 3 or more cross sections near a position 50 μm from the edge line of the cutting edge of the surface facing the metal evaporation source toward the center of the surface, and the average value (arithmetic average) thereof was calculated. Specifically, it can be obtained by the method described in the examples below.

The composition of each layer constituting the coating layer used in the coated cutting tool of the present embodiment can be measured from the cross-sectional structure of the coated cutting tool of the present embodiment using an energy dispersive X-ray analyzer (EDX), a wavelength dispersive X-ray analyzer (WDS), or the like. In the present embodiment, the composition of each layer constituting the coating layer can be measured by the method described in the examples below.

The coated cutting tool of the present embodiment is considered to have excellent wear resistance and chipping resistance, and therefore, the effect of extending the tool life as compared with the conventional one is exhibited (although the factor of extending the tool life is not limited to the above). The type of the coated cutting tool of the present embodiment is not particularly limited, and specific examples thereof include a replaceable tip cutting insert for milling or turning, a drill (drill), and an end mill (end mill).

[ examples ]

The present invention will be described in more detail with reference to the following examples, but the present invention is not limited to these examples.

(example 1)

As the substrate, a substrate formed of a sintered body containing cubic boron nitride was produced according to the following steps (1) to (8). At this point, the substrate was processed into an ISO standard CNGA120408 shape.

Step (1): powders of 66 volume percent cubic boron nitride and 34 volume percent binder phase were mixed.

Step (2): the raw material powder obtained in step (1) was mixed by wet ball milling for 12 hours using cemented carbide balls.

Step (3): the mixture obtained in step (2) is molded into a predetermined shape to obtain a molded body.

Step (4): the compact obtained in step (3) was sintered by holding it inside an ultrahigh pressure generator at a sintering temperature of 1300 ℃ under a pressure of 6.0GPa for 1 hour.

Step (5): the sintered body obtained in step (4) is cut out by an electric discharge machine in accordance with the tool shape.

Step (6): a base body made of cemented carbide is prepared.

Step (7): the sintered body cut out in step (5) is joined to the base prepared in step (6) by brazing.

Step (8): honing the tool obtained in step (7).

In the base material produced as described above, the composition of the binder phase contained in the sintered body containing cubic boron nitride was identified by an X-ray diffraction apparatus. The composition of the binder phase contained in the sintered body containing cubic boron nitride is TiN or Al₂O₃、AlN。

In a reaction vessel of the arc ion plating apparatus, metal evaporation sources shown in table 1 were disposed. The substrate thus produced was fixed to a fixing member of a turntable in the reaction vessel.

Then, the inside of the reaction vessel was evacuated until a pressure of 5.0X 10 was reached^-3Vacuum below Pa. After evacuation, the substrate was heated by a heater in the reaction vessel until its temperature reached 450 ℃. After heating, argon (Ar) gas was introduced into the reaction vessel so that the pressure thereof became 2.7 Pa.

A bias voltage of-400V was applied to the substrate in an Ar atmosphere at a pressure of 2.7Pa, and a current of 40A was passed through the tungsten wire in the reaction vessel, thereby subjecting the surface of the substrate to ion bombardment treatment using Ar for 30 minutes. Treating junctions by ion bombardmentAfter completion of the reaction, the reaction vessel was evacuated until a pressure of 5.0X 10 was reached^-3Vacuum below Pa.

After evacuation, the substrate was adjusted to a temperature shown in table 1 (temperature at the start of film formation), and Ar and nitrogen (N) were added₂) And acetylene gas (C)₂H₂) The reaction mixture was introduced into the reaction vessel at a flow rate shown in table 1, and the pressure in the reaction vessel was adjusted to a pressure shown in table 1.

Next, a bias voltage shown in table 1 was applied to the substrate, and a metal evaporation source was evaporated by arc discharge with a current shown in table 1 to have a composition shown in table 2, thereby forming a coating layer on the surface of the substrate. The acetylene gas (C) introduced into the reaction vessel was introduced₂H₂) As shown in table 1, the flow rate of (d) was gradually changed from the start of film formation to the end of film formation. Further, as the coating layer, products 1 to 10 and comparative products 1 to 7 formed a carbonitride layer of Ti, comparative product 8 formed a TiN layer, and comparative product 9 formed a TiAlN layer.

After the coated cutting tool was produced by forming each layer on the surface of the substrate until the average thickness was the predetermined thickness shown in table 2, the power supply of the heater was cut off, and the sample (coated cutting tool) was taken out from the reaction vessel after the temperature of the sample (coated cutting tool) reached 100 ℃. Thus, coated cutting tools of invention products 1 to 10 and comparative products 1 to 9 were obtained.

The average thickness of the Ti carbonitride layer and the like of the obtained sample (coated cutting tool) was determined by the following method: SEM observation was performed on 3 cross sections near a position 50 μm from the edge line portion of the cutting edge of the surface facing the metal evaporation source of the coated cutting tool toward the center of the surface, and the thickness of each layer was measured and the average value (arithmetic mean) thereof was calculated. The results are shown in Table 2. With respect to the composition of the Ti carbonitride layer and the like of the obtained sample (coated cutting tool), among the measurement positions of 3 cross sections in the vicinity of the position from the edge line portion of the cutting tip of the surface of the coated cutting tool facing the metal evaporation source to the center portion by 50 μm, the positions at which the thickness of the Ti carbonitride layer and the like from the base material side was 25%, 50%, and 75%, respectively, were measured using an energy dispersive X-ray analyzer (EDX). The average of the measurement results at 3 was taken as each composition. These results are also shown in Table 2. The atomic ratio of the element C in the Ti carbonitride layer in table 2 represents the atomic ratio of the element C to the total amount of the elements C and N at a position 50% thick from the base material side in the Ti carbonitride layer. In addition, the atomic ratios of the C element to the total amount of the C element and the N element (also referred to as "R25" and "R75" in this order) at positions 25% and 75% thick from the base material side in the Ti carbonitride layer were also measured. The results are also shown in Table 3.

[ Table 1]

In table 1, "-" indicates that C was not used₂H₂And (4) qi. Further, "C" is₂H₂The "amount of change in gas" means that C is caused within one minute₂H₂Amount of change of quantity, positive value indicating an increase in C₂H₂Amount, negative value indicates decrease. The case of "certain" means that C is not changed₂H₂The amount of (c).

[ Table 2]

As the coating layer, a TiN layer was formed in comparative example 8, and a TiAlN layer was formed in comparative example 9, and in table 2, the average thickness of the coating layer of comparative example 8 indicated the average thickness of the TiN layer, and the average thickness of the coating layer of comparative example 9 indicated the average thickness of the TiAlN layer.

[ Table 3]

The "-" in the table indicates that no C element is contained.

[ Absolute value of difference between maximum value and minimum value of 2 θ ]

The absolute value of the difference between the maximum value and the minimum value of 2 θ in the X-ray diffraction measurement of the Ti carbonitride layer was measured for the obtained sample (coated cutting tool) in the following manner. As the measuring apparatus, an X-ray diffraction analyzer equipped with a two-dimensional detector was used. The X-ray tube was designated as Cu-K.alpha.and the measurement was designated as 2. theta. -phi. measurement. With respect to the peak position of the (111) plane of the Ti carbonitride layer, the peak position was measured at the ψ angle: the frames were measured at 10 ° intervals in the range of 0 ° to 70 °. In the measurement of each frame, the measurement time is adjusted so that the intensity of the crystal plane (111 plane or (200) plane) is 2 to 3 times the background. Since the strength varies depending on the thickness of the layer, etc., the time is adjusted for each sample. In the analysis, the position 2 θ of the peak of the (111) plane was specified by using software attached to the X-ray diffraction analyzer. When the angle ψ is measured as 0 °, 30 °, 50 °, and 70 °, the absolute value of the difference between the maximum value and the minimum value of 2 θ represented by the following formula (2) is calculated.

The absolute value of the difference between the maximum value and the minimum value of 2 θ is |2 θ max-2 θ min | (2)

(in the formula (2), 2 θ max represents the maximum value among the positions 2 θ of the peaks of the (111) plane when the ψ angle is 0 °, 30 °, 50 °, and 70 °, and 2 θ min represents the minimum value among the positions 2 θ of the peaks of the (111) plane when the ψ angle is 0 °, 30 °, 50 °, and 70 °)

The same measurement was performed for the absolute value of the difference between the maximum value and the minimum value of the peak position 2 θ of the (200) plane of the Ti carbonitride layer. The measurement results are shown in table 4.

[ texture coefficient TC (111) ]

With respect to the obtained sample (coated cutting tool), at the output: 50kV, 250mA, incident side shuttle slit: 5 °, divergent longitudinal slit: 2/3 °, divergent longitudinal limit slit: 5mm, scattering slit: 2/3 °, light receiving side shuttle slit: 5 °, light receiving slit: 0.3mm, BENT monochromator, light-receiving monochromatic slit: 0.8mm, sampling width: 0.01 °, scanning speed: 4 °/min, 2 θ measurement range: x-ray diffraction measurement of an optical system by 2 theta/theta focusing method using Cu-Ka rays was performed under conditions of 25 DEG to 140 deg. An X-ray diffraction apparatus (model No. 'RINT TTRIII') manufactured by リガク was used as the apparatus. The peak intensity of each crystal face of the Ti carbonitride layer and the like is obtained from the X-ray diffraction spectrum. The texture coefficient TC (111) of the (111) plane in the Ti carbonitride layer or the like is calculated from the peak intensity of each crystal plane obtained by the following formula (1). The results are shown in Table 4.

[ mathematical formula 3]

(in the formula (1), I (h k l) represents the peak intensity of the (h k l) plane in X-ray diffraction of a Ti carbonitride layer or the like, I₀(h kl) represents the standard diffraction intensity of the (h kl) plane in ICDD card No. 00-042-1488, where (h kl) refers to the six crystal planes (111), (200), (220), (311), (420) and (422). )

[ Table 4]

Using the obtained sample (coated cutting tool), the following cutting test was performed. The results are shown in Table 5.

[ cutting test ]

The shape of the blade is as follows: the CNGA120408 is a group of codes,

material to be cut: SCM420H (60HRC),

shape of material to be cut:the cylindrical shape of the cylinder (a) is,

cutting speed: the concentration of the carbon dioxide is 130 m/min,

feeding amount: 0.15mm/rev of the sample,

cutting depth: the diameter of the hole is 0.15mm,

cooling agent: in use, the adhesive tape is put into use,

evaluation items: wear the nose (VB)_C) The time until reaching 0.15mm was taken as the tool life, and the machining time until the tool life was measured.

[ Table 5]

In the cutting test, the working time up to the tool life of the invention product was 141 minutes or more, which was longer than that of all the comparative products. The longer working time is evaluated as excellent wear resistance and defect resistance because wear progresses more slowly and defects are less likely to occur.

From the above results, it is understood that the tool life of the invention product is prolonged by improving the wear resistance and the chipping resistance.

(example 2)

As the substrate, a substrate formed of a sintered body containing cubic boron nitride was produced in the same manner as in example 1. In this case, the substrate was processed into ISO standard CNGA120408 shape.

In the base material produced as described above, the composition of the binder phase contained in the sintered body containing cubic boron nitride was identified by an X-ray diffraction apparatus. The composition of the binder phase contained in the sintered body containing cubic boron nitride is TiN or Al₂O₃、AlN。

A metal evaporation source was disposed in a reaction vessel of an arc ion plating apparatus so as to have the compositions of the respective layers shown in Table 9. The substrate thus produced was fixed to a fixing member of a turntable in the reaction vessel.

Then, the inside of the reaction vessel was evacuated until a pressure of 5.0X 10 was reached^-3Vacuum below Pa. After evacuation, the substrate was heated by a heater in the reaction vessel until its temperature reached 450 ℃. After heating, argon (Ar) gas was introduced into the reaction vessel so that the pressure thereof became 2.7 Pa.

A bias voltage of-400V was applied to the substrate in an Ar atmosphere at a pressure of 2.7Pa, a current of 40A was passed through the tungsten filament in the reaction vessel, and ion bombardment treatment using Ar was performed on the surface of the substrate for 30 minutes. After the ion bombardment treatment is finished, vacuumizing the reaction container until the reaction container is shapedTo a pressure of 5.0X 10^-3Vacuum below Pa.

After evacuation, the substrate is adjusted to 550 ℃ and N is added₂The reaction mixture was introduced into the reaction vessel at a flow rate shown in Table 6, and the pressure in the reaction vessel was adjusted to a pressure shown in Table 6.

Then, the substrate was subjected to bias voltage shown in table 6, and the metal evaporation source was evaporated by arc discharge with current shown in table 6 to form the composition shown in table 9, thereby forming the 1 st layer (compound layer) as the lower layer on the surface of the substrate.

For the inventions 11, 13 and 14, the 2 nd layer (metal layer) of the lower layer was formed in the following manner. First, after the formation of the 1 st layer (compound layer) as the lower layer, the base material was adjusted to 550 ℃, Ar was introduced into the reaction vessel at a flow rate shown in table 7, and the pressure in the reaction vessel was adjusted to a pressure shown in table 7.

Next, the bias voltage shown in table 7 was applied to the base material, and the metal evaporation source was evaporated by arc discharge with a current shown in table 7 to form the composition shown in table 9, thereby forming the 2 nd layer (metal layer) of the lower layer on the surface of the 1 st layer (compound layer) of the lower layer.

[ Table 6]

[ Table 7]

After the lower layer was formed, the temperature of the substrate was adjusted to the temperature shown in table 8 (temperature at the start of film formation), and Ar and nitrogen (N) were added₂) And acetylene gas (C)₂H₂) The reaction mixture was introduced into the reaction vessel at a flow rate shown in Table 8, and the pressure in the reaction vessel was adjusted to a pressure shown in Table 8.

Then, the substrate was biased as shown in Table 8, and the metal evaporation source was evaporated by arc discharge with a current as shown in Table 8 to have a composition as shown in Table 9A carbonitride layer of Ti is formed on the surface of the lower layer. The acetylene gas (C) introduced into the reaction vessel was introduced₂H₂) As shown in table 8, the flow rate of (d) was gradually changed from the start of film formation to the end of film formation.

Each layer was formed on the surface of the base material until the average thickness was the predetermined average thickness shown in table 9, to thereby produce a coated cutting tool. Then, the power supply of the heater was cut off, and after the temperature of the sample (coated cutting tool) reached 100 ℃ or lower, the sample (coated cutting tool) was taken out from the reaction vessel. Thus, coated cutting tools of invention products 11 to 19 were obtained.

The average thickness and composition of the Ti carbonitride layer and the like of the obtained sample (coated cutting tool) were measured by the same methods as in example 1. The results are shown in Table 9. In addition, in the Ti carbonitride layer of the obtained sample (coated cutting tool), the atomic ratio of the C element to the total amount of the C element and the N element at the positions of 25% and 75% of the thickness from the base material side was also measured by the same method as in example 1. The results are shown in Table 10.

[ Table 8]

[ Table 9]

"-" indicates an unformed layer.

[ Table 10]

[ Absolute value of difference between maximum value and minimum value of 2 θ ]

The absolute value of the difference between the maximum value and the minimum value of 2 θ in the X-ray diffraction measurement of the Ti carbonitride layer was measured for the obtained sample (coated cutting tool) by the same method as in example 1. The measurement results are shown in table 11.

[ texture coefficient TC (111) ]

With respect to the sample (coated cutting tool), the texture coefficient TC (111) of the (111) plane in the Ti carbonitride layer or the like was calculated by the same method as in example 1. The results are shown in Table 11.

[ Table 11]

Using the obtained sample (coated cutting tool), the following cutting test was performed. The results are shown in Table 12.

[ cutting test ]

The shape of the blade is as follows: the CNGA120408 is a group of codes,

material to be cut: SCM420H (60HRC),

shape of material to be cut:the cylindrical shape of the cylinder (a) is,

cutting speed: the concentration of the carbon dioxide is 130 m/min,

feeding amount: 0.15mm/rev of the sample,

cutting depth: the diameter of the hole is 0.15mm,

cooling agent: in use, the adhesive tape is put into use,

evaluation items: wear the knife tip (VB)_C) The time until reaching 0.15mm was taken as the tool life, and the machining time until the tool life was measured.

[ Table 12]

In the cutting test, the machining time for the tool life of the invention products 11 to 19 was 173 minutes or more.

From the above results, it is understood that the tool life of the invention product is prolonged by improving the wear resistance and the chipping resistance.

(example 3)

As the substrate, a substrate formed of a sintered body containing cubic boron nitride was produced by the same method as in example 1. In this case, the substrate was processed into an ISO standard CNGA120408 shape.

In the base material produced as described above, the composition of the binder phase contained in the sintered body containing cubic boron nitride was identified by an X-ray diffraction apparatus. The composition of the binder phase contained in the sintered body containing cubic boron nitride is TiN or Al₂O₃、AlN。

A metal evaporation source was disposed in a reaction vessel of the arc ion plating apparatus so as to have the compositions of the respective layers shown in Table 15. The substrate thus produced was fixed to a fixing member of a turntable in the reaction vessel.

Then, the inside of the reaction vessel was evacuated until a pressure of 5.0X 10 was reached^-3Vacuum below Pa. After evacuation, the substrate was heated by a heater in the reaction vessel until its temperature reached 450 ℃. After heating, argon (Ar) gas was introduced into the reaction vessel so that the pressure thereof became 2.7 Pa.

A bias voltage of-400V was applied to the substrate in an Ar atmosphere at a pressure of 2.7Pa, a current of 40A was passed through the tungsten wire in the reaction vessel, and ion bombardment treatment using Ar was applied to the surface of the substrate for 30 minutes. After the ion bombardment treatment is finished, the reaction container is vacuumized until the pressure is 5.0 x 10^-3Vacuum below Pa.

After evacuation, the substrate is adjusted to 550 ℃ and N is added₂The reaction mixture was introduced into the reaction vessel at a flow rate shown in Table 13, and the pressure in the reaction vessel was adjusted to a pressure shown in Table 13. Then, the bias voltage shown in table 13 was applied to the base material, and the metal evaporation sources of the 1 st compound layer and the 2 nd compound layer in the lower layer having the compositions shown in table 15 were sequentially and alternately evaporated by arc discharge with the arc current shown in table 13, thereby sequentially and alternately forming the 1 st compound layer and the 2 nd compound layer in the lower layer on the surface of the base material. In this case, control was performed so as to attain the pressures in the reaction vessels shown in Table 13. In addition, of the 1 st compound layer and the 2 nd compound layer of the lower layerThe thicknesses were controlled by adjusting the respective arc discharge times to the thicknesses shown in table 15.

[ Table 13]

After the lower layer was formed, the temperature of the substrate was adjusted to the temperature shown in table 14 (temperature at the start of film formation), and Ar and nitrogen (N) were added₂) And acetylene gas (C)₂H₂) The reaction mixture was introduced into the reaction vessel at a flow rate shown in Table 14, and the pressure in the reaction vessel was adjusted to a pressure shown in Table 14.

Next, a bias voltage shown in table 14 was applied to the base material, and a metal evaporation source was evaporated by arc discharge with a current shown in table 14 so as to have a composition shown in table 15, thereby forming a Ti carbonitride layer on the surface of the lower layer. The acetylene gas (C) introduced into the reaction vessel was introduced₂H₂) As shown in table 14, the flow rate of (d) was gradually changed from the start of film formation to the end of film formation.

Each layer was formed on the surface of the base material until the average thickness was the predetermined average thickness shown in table 15, to thereby produce a coated cutting tool. Then, the power supply of the heater was cut off, and after the temperature of the sample (coated cutting tool) reached 100 ℃ or lower, the sample (coated cutting tool) was taken out from the reaction vessel. Thus, coated cutting tools of invention products 20 to 25 were obtained.

The average thickness and composition of the Ti carbonitride layer and the like of the obtained sample (coated cutting tool) were measured by the same methods as in example 1. The results are shown in Table 15. In addition, in the Ti carbonitride layer of the obtained sample (coated cutting tool), the atomic ratio of the C element to the total amount of the C element and the N element at the positions of 25% and 75% of the thickness from the base material side was also measured by the same method as in example 1. The results are shown in Table 16.

[ Table 14]

[ Table 15]

[ Table 16]

[ Absolute value of difference between maximum value and minimum value of 2 θ ]

The absolute value of the difference between the maximum value and the minimum value of 2 θ in the X-ray diffraction measurement of the Ti carbonitride layer was measured for the obtained sample (coated cutting tool) by the same method as in example 1. The measurement results are shown in table 17.

[ texture coefficient TC (111) ]

With respect to the obtained sample (coated cutting tool), the texture coefficient TC (111) of the (111) plane in the Ti carbonitride layer or the like was calculated by the same method as in example 1. The results are shown in Table 17.

[ Table 17]

Using the obtained sample (coated cutting tool), the following cutting test was performed. The results are shown in Table 18.

[ cutting test ]

The shape of the blade is as follows: the CNGA120408 is a group of codes,

material to be cut: SCM420H (60HRC),

shape of material to be cut:the cylindrical shape of the cylinder (a) is,

cutting speed: the concentration of the carbon dioxide is 130 m/min,

feeding amount: 0.15mm/rev of the sample,

cutting depth: the diameter of the hole is 0.15mm,

cooling agent: in use, the adhesive tape is put into use,

evaluation items: wear the knife tip (VB)_C) The time until reaching 0.15mm was taken as the tool life, and the machining time until the tool life was measured.

[ Table 18]

In the cutting test, the machining time up to the tool life of the invention products 20 to 25 was 188 minutes or more.

From the above results, it is understood that the tool life of the invention product is prolonged by improving the wear resistance and the chipping resistance.

[ industrial applicability ]

The coated cutting tool of the present invention has a longer tool life than conventional coated cutting tools, and therefore has high industrial applicability.

Description of the symbols

1 base material

2 lower layer

3 Ti carbonitride layer

4 coating layer

5 coated cutting tool