JP2012143851A - Surface-coated cutting tool - Google Patents

Abstract

PROBLEM TO BE SOLVED: To provide a surface-coated cutting tool with a hardened coated layer exerting excellent heat and welding resistance in performing the high-speed cutting processing of a difficult-to-cut material.SOLUTION: The surface-coated cutting tool has the hardened coated layer formed on the surface of a tool base body. In the surface-coated cutting tool, the hardened coated layer comprises a two-layer structure composed of an A layer and a B layer or an alternate layer structure of the A and B layers. The A layer is composed of a composite nitride layer of Ti, Al expressed by a compositional formula: (TiAl)N or a nitride layer of Ti, Al and M expressed by a compositional formula: (TiAlM)N (wherein M denotes one or more of additional elements selected from among Si, B and Y, excluding Ti, which are elements in the groups 4a, 5a and 6a in the periodic table) while the layer B is composed of a composite nitride layer of Cr, W and Ag satisfying relations of, by atomic ratio, 0.45≤α≤0.75 and 0.01≤β≤0.25 and a compositional formula: (CrWAg)N (where, by atomic ratio, 0.01≤X≤0.30 and 0.01≤Y≤0.20).

Description

  The present invention relates to a surface-coated cutting tool (hereinafter referred to as a coated tool). More specifically, for example, a difficult-to-cut material such as stainless steel or heat-resistant steel is subjected to high heat generation and intermittently impacted on a cutting edge portion. The present invention relates to a coated tool that exhibits excellent heat resistance and wear resistance when a hard coating layer is cut when subjected to high-speed conditions with a heavy load.

  Generally, coated tools are used for throwaway inserts that are detachably attached to the tip of cutting tools for drilling and cutting of various materials such as steel and cast iron. There are drills and miniature drills used, as well as solid type end mills used for chamfering, grooving and shoulder machining of work materials, etc. A slow-away end mill tool that performs cutting is known.

  In addition, as a coated tool, for example, a composite nitride ((Ti, Al) N) layer of Ti and Al on the surface of the tool base, or in addition, a small amount of Si, B, Y, Zr, V, etc. Also known is a coated tool provided with a composite nitride (hereinafter collectively referred to as (Ti, Al, M) N) containing Ti and Al as additive components. Since Al has high temperature hardness and heat resistance, and Ti has high temperature strength, the (Ti, Al, M) N layer is also known to exhibit excellent high temperature strength, fracture resistance, and wear resistance. ing.

  Furthermore, the conventional coated tool is loaded with a tool base in an arc ion plating apparatus which is one of physical vapor deposition apparatuses shown schematically in FIG. 2, for example, at a temperature of 500 ° C., for example. Arc discharge is performed between the cathode electrode in which an alloy corresponding to the composition of the hard coating layer is set, for example, a Ti-Al-M alloy, and the anode electrode under the condition of current: 90A. At the same time, nitrogen gas is introduced into the apparatus as a reaction gas to create a reaction atmosphere of, for example, 2 Pa. On the other hand, the tool substrate is applied with a bias voltage of, for example, −100 V on the surface of the tool substrate. It is also known to be produced by vapor-depositing a hard coating layer composed of a (Ti, Al, M) N layer.

Japanese Patent No. 2644710 Japanese Patent No. 2793773 Japanese Patent No. 2793696 JP-A-8-199338

  However, in recent years, the FA of cutting machines has been remarkable. On the other hand, there has been a strong demand for labor saving and energy saving and further cost reduction for cutting, and as a result, cutting tools have as much influence on the type of work material as possible. However, in the conventional coated tool, this is applied to a work material such as a Ti alloy or stainless steel. There is no problem when used for cutting at a normal cutting speed, but when these materials are cut under high-speed conditions that cause high heat generation and a high load locally on the cutting edge, Due to the heat generated during cutting, the work piece and the chips are heated to a high temperature and the viscosity increases. As a result, the weldability to the surface of the hard coating layer increases further. Generation of (small chipping) increases rapidly, which is at present, leading to a relatively short time service life due.

  Therefore, a technical problem to be solved by the present invention, that is, an object of the present invention is to provide a coated tool that exhibits excellent heat resistance and wear resistance even when cutting under high-speed conditions with high heat generation. It is.

  In view of the above, the inventors of the present invention have excellent heat resistance with a hard coating layer especially when cutting difficult-to-cut materials such as stainless steel and heat-resistant steel under high-speed cutting conditions. As a result of diligent research to develop a coated tool having excellent wear resistance, the content of W in the total amount of Cr on the surface of the tool base is 1 to 30 atomic%, and the content ratio of Ag is A composite nitride layer of Cr, W, and Ag (hereinafter, referred to as a (Cr, W, Ag) N layer) containing a W component and an Ag component so as to be 1 to 20 atomic% was formed as a hard coating layer. In some cases, it was found that this coated tool exhibits excellent wear resistance in high-speed cutting of difficult-to-cut materials.

  Further, the inventors of the present invention have a (Ti, Al) N layer or (Ti, Al, M) N layer, which is a hard coating layer of the conventional coated tool, on the surface of the tool base as a lower layer of 0.5 to 5 μm. The W component and the Ag component so that the W content in the total amount with Cr is 1 to 30 atomic% and the Ag content is 1 to 20 atomic%. When a composite nitride layer containing Cr, W, and Ag (hereinafter, referred to as a (Cr, W, Ag) N layer) is formed as an upper layer, a (Ti, Al) N layer or (Ti , Al, M) N layer exhibits excellent high temperature hardness, high temperature strength, and heat resistance, and the W component contained in the upper (Cr, W, Ag) N layer exhibits high hardness, Since the Ag component exhibits lubricity, the (Cr, W, Ag) N layer exhibits excellent heat resistance and lubricity, Results, with a high fever, and wear progression of the cutting edge also be used to weld significant speed cutting of the workpiece can be suppressed, so that exhibits wear resistance with excellent long-term. Therefore, in high-speed cutting of difficult-to-cut materials, even if the cutting edge becomes hot, it has excellent heat resistance with the work material. As a result, the occurrence of chipping (small chipping) in the cutting edge is suppressed, and long-term The present inventors have obtained new knowledge that excellent wear resistance is exhibited over a long period of time, and have completed the present invention based on such knowledge.

  Further, a (Ti, Al) N thin layer or (Ti, Al, M) N thin layer having an average layer thickness of 0.01 to 0.1 μm is formed on the surface of the tool base by vapor deposition, and Cr and A composite nitride layer of Cr, W, and Ag containing a W component and an Ag component such that the W content is 1-30 atomic% and the Ag content is 1-20 atomic%. Hereinafter, a (Cr, W, Ag) N thin layer having an average layer thickness of 0.01 to 0.1 μm composed of (Cr, W, Ag) N layer) is formed by vapor deposition. ) N thin layer or (Ti, Al, M) N thin layer and the (Cr, W, Ag) N thin layer are alternately formed to form a hard coating layer having an alternate laminated structure, (Ti, Al ) N thin layer or (Ti, Al, M) N thin layer shows excellent high temperature hardness, high temperature strength and heat resistance. The (Cr, W, Ag) N thin layers alternately laminated with each other exhibit excellent wear resistance, and in particular, the (Cr, W, Ag) N thin layer contains (Cr, W, Ag) N by virtue of the Ag component contained therein. Since the lubricity of the W, Ag) N thin layer is improved, it has been found that the excellent welding resistance of the (Cr, W, Ag) N thin layer is maintained even in cutting with high heat generation.

  Therefore, in high-speed cutting of difficult-to-cut materials such as stainless steel and heat-resistant steel, even if the cutting edge becomes hot, the (Ti, Al) N thin layer or the (Ti, Al, M) N thin layer is insufficient. The (Cr, W, Ag) N thin layers that are alternately laminated complement the welding resistance, and the wear resistance with the work material as the entire hard coating layer is improved. The present inventors have obtained a new finding that chipping (small chipping) is prevented from occurring in a part and excellent wear resistance is exhibited over a long period of time, and the present invention has been achieved based on such a finding.

The present invention has been made based on the research results,
“(1) In a surface-coated cutting tool in which a hard coating layer is formed on the surface of a tool base composed of tungsten carbide-based cemented carbide or titanium carbonitride-based cermet,
The hard coating layer has an average layer thickness of 0.5 to 5 μm, and
Composition formula: (Cr _1-XY W _X Ag _Y ) N (where X represents the content ratio of W, Y represents the content ratio of Ag, and the atomic ratio is 0.01 ≦ X ≦ 0.30. A surface-coated cutting tool comprising a composite nitride layer of Cr, W, and Ag satisfying 0.01 ≦ Y ≦ 0.20.
(2) In a surface-coated cutting tool formed by forming a hard coating layer on the surface of a tool base composed of a tungsten carbide-based cemented carbide or a titanium carbonitride-based cermet,
The hard coating layer is
(A) having an average layer thickness of 0.5-5 μm, and
Composition of Ti and Al satisfying the composition formula: (Ti _1-α Al _α ) N (where α is the Al content ratio and the atomic ratio is 0.45 ≦ α ≦ 0.75) A lower layer made of a nitride layer;
(B) having an average layer thickness of 0.5-5 μm, and
Composition formula: (Cr _1-XY W _X Ag _Y ) N (where X represents the content ratio of W, Y represents the content ratio of Ag, and the atomic ratio is 0.01 ≦ X ≦ 0.30. A surface-coated cutting tool comprising: an upper layer made of a composite nitride layer of Cr, W, and Ag satisfying 0.01 ≦ Y ≦ 0.20.
(3) In a surface-coated cutting tool formed by forming a hard coating layer on the surface of a tool base composed of a tungsten carbide-based cemented carbide or a titanium carbonitride-based cermet,
The hard coating layer is
(A) having an average layer thickness of 0.01 to 0.1 μm, and
Composition of Ti and Al satisfying the composition formula: (Ti _1-α Al _α ) N (where α is the Al content ratio and the atomic ratio is 0.45 ≦ α ≦ 0.75) (Ti, Al) N thin layer made of a nitride layer,
(B) having an average layer thickness of 0.01 to 0.1 μm, and
Composition formula: (Cr _1-XY W _X Ag _Y ) N (where X represents the content ratio of W, Y represents the content ratio of Ag, and the atomic ratio is 0.01 ≦ X ≦ 0.30. (Cr, W, Ag) N thin layer composed of a composite nitride layer of Cr, W and Ag satisfying 0.01 ≦ Y ≦ 0.20
A surface-coated cutting tool comprising the alternating lamination of (a) and (b) and having a total average layer thickness of 1 to 5 μm.
(4) In a surface-coated cutting tool formed by forming a hard coating layer on the surface of a tool base composed of tungsten carbide-based cemented carbide or titanium carbonitride-based cermet,
The hard coating layer is
(A) having an average layer thickness of 0.5-5 μm, and
Composition formula: (Ti _1-α-β Al _α M _β ) N (where M is a member selected from the group 4a, 5a, 6a elements except Si, Si, B, Y) Seeds or two or more kinds of additive components, α is a content ratio of Al, β is a content ratio of M, and atomic ratio is 0.45 ≦ α ≦ 0.75, 0.01 ≦ β ≦ A lower layer composed of a composite nitride layer of Ti, Al, and M satisfying 0.25),
(B) having an average layer thickness of 0.5-5 μm, and
Composition formula: (Cr _1-XY W _X Ag _Y ) N (where X represents the content ratio of W, Y represents the content ratio of Ag, and the atomic ratio is 0.01 ≦ X ≦ 0.30. A surface-coated cutting tool comprising: an upper layer made of a composite nitride layer of Cr, W, and Ag satisfying 0.01 ≦ Y ≦ 0.20.
(5) In a surface-coated cutting tool formed by forming a hard coating layer on the surface of a tool base composed of tungsten carbide-based cemented carbide or titanium carbonitride-based cermet,
The hard coating layer is
(A) having an average layer thickness of 0.01 to 0.1 μm, and
Composition formula: (Ti _1-α-β Al _α M _β ) N (where M is a member selected from the group 4a, 5a, 6a elements except Si, Si, B, Y) Seeds or two or more kinds of additive components, α is a content ratio of Al, β is a content ratio of M, and atomic ratio is 0.45 ≦ α ≦ 0.75, 0.01 ≦ β ≦ (Ti, Al, M) N thin layer composed of a composite nitride layer of Ti, Al, and M satisfying 0.25)
(B) having an average layer thickness of 0.01 to 0.1 μm, and
Composition formula: (Cr _1-XY W _X Ag _Y ) N (where X represents the content ratio of W, Y represents the content ratio of Ag, and the atomic ratio is 0.01 ≦ X ≦ 0.30. (Cr, W, Ag) N thin layer composed of a composite nitride layer of Cr, W and Ag satisfying 0.01 ≦ Y ≦ 0.20
A surface-coated cutting tool comprising the alternating lamination of (a) and (b) and having a total average layer thickness of 1 to 5 μm. "
It is characterized by.

Next, the reason why the numerical values of the constituent layers of the hard coating layer of the coated tool of the present invention are limited as described above will be described.
(A) (Ti, Al) N layer or (Ti) which constitutes one layer of the lower layer in the invention described in (2) and (4) and the alternately laminated layer in the invention described in (3) and (5) Ti, Al, M) N layer composition and average layer thickness or single layer average film thickness:
The Al component, which is a component of the (Ti, Al) N layer or (Ti, Al, M) N layer that constitutes one of the lower layer or the alternately laminated layers, improves the high-temperature hardness of the hard coating layer. The Ti component has the effect of improving the high-temperature strength. Further, among the M components, the elements of the periodic table 4a, 5a, 6a excluding Ti, Si, B, and the wear resistance of the hard coating layer. Y has the effect of improving, and Y has the effect of improving the high temperature oxidation resistance of the hard coating layer, but the α value indicating the proportion of Al accounts for the total amount of Ti or the total amount of Ti and M If the atomic ratio (the same applies hereinafter) is less than 0.45, the predetermined high-temperature hardness cannot be ensured, which causes a decrease in wear resistance, while the α value indicating the Al ratio is the same as that of 0.00. When it exceeds 75, the Ti content is relatively reduced, which is essential for high-speed cutting. The required high-temperature strength cannot be ensured, and it becomes difficult to prevent the occurrence of chipping. Further, the ratio of the β value indicating the content ratio of the M component to the total amount with Ti (atomic ratio, If the β value exceeds 0.25, high temperature strength cannot be expected. Therefore, the α value was set to 0.45 to 0.75, and the β value was set to 0.01 to 0.25.

  In addition, when the average layer thickness of the (Ti, Al) N layer or (Ti, Al, M) N layer constituting the lower layer is less than 0.5 μm, the wear resistance possessed by itself is exhibited over a long period of time. On the other hand, if the average layer thickness exceeds 5 μm, chipping is likely to occur at the cutting edge part in the high-speed cutting, so the average layer thickness is set to 0.5 to 5 μm. .

In addition, when the average thickness of the (Ti, Al) N layer or (Ti, Al, M) N layer constituting one layer of the alternately laminated layer is less than 0.01 μm, the excellent wear resistance of the layer itself is maintained for a long time. On the other hand, if the average layer thickness exceeds 0.1 μm, the high-speed high-feed cutting reveals a lack of welding resistance and causes chipping at the cutting edge. Therefore, the average layer thickness was determined to be 0.01 to 0.1 μm.
(C) (Cr, W, Ag) N layer constituting the upper layer in the invention described in (2) and (4) and one of the alternately laminated layers in the invention described in (3) and (5) Composition and average layer thickness or single layer average film thickness:
A composite nitride (Cr, W, Ag) N layer of Cr, W and Ag constituting one of the (Ti, Al) N layer or the upper layer of the (Ti, Al, M) N layer or the alternately stacked layers is It has predetermined high-temperature hardness, high-temperature strength, and heat resistance, and has excellent lubricity due to its constituent Ag component, and high hardness is complemented by the W component. Therefore, a low friction coefficient is maintained even under high-temperature cutting conditions, and excellent heat resistance is exhibited, but the ratio of the X value indicating the W content ratio to the total amount of Cr and Ag (atomic ratio, below) If the X value indicating the W content exceeds 0.30, the relative hardness cannot be expected because high hardness cannot be secured. In particular, the content ratio of Ag is reduced, and not only the lubricity required for high-speed cutting of difficult-to-cut materials cannot be ensured, but also the wear resistance is lowered and it becomes difficult to prevent the occurrence of chipping. Therefore, the X value was determined to be 0.01 to 0.30 (atomic ratio, the same applies hereinafter). Moreover, although excellent lubricity is exhibited by the Ag component, the Y value indicating the Ag content ratio is less than 0.01 in terms of the ratio of the total amount of Cr and W (atomic ratio, hereinafter the same). Then, since the lubricity cannot be ensured, the effect of suppressing the progress of wear cannot be expected. On the other hand, when the Y value indicating the Ag content ratio exceeds 0.20, relatively W Because the content ratio decreases and not only the high hardness required for high-speed cutting of difficult-to-cut materials cannot be secured, but also heat resistance is reduced, making it difficult to demonstrate wear resistance. It was determined to be 0.01-0.20.

  On the other hand, when the average layer thickness of the (Cr, W, Ag) N layer constituting the upper layer is less than 0.5 μm, it is insufficient to exhibit its excellent wear resistance over a long period of time. When the average layer thickness exceeds 5 μm, chipping tends to occur at the cutting edge portion in the high-speed cutting, so the average layer thickness was set to 0.5 to 5 μm.

  Further, if the average layer thickness of the (Cr, W, Ag) N layers constituting one of the alternately laminated layers is less than 0.01 μm, it is not possible to exhibit the excellent wear resistance of the layers for a long time. On the other hand, if the average layer thickness is more than 0.1 μm, the high-speed high-feed cutting will cause insufficient wear resistance, and chipping is likely to occur at the cutting edge. The average layer thickness was determined to be 0.01 to 0.1 μm.

  The (Ti, Al) N layer, the (Ti, Al, M) N layer, and the (Cr, W, Ag) N layer are, for example, one type of physical vapor deposition apparatus schematically shown in FIG. A base is placed in an arc ion plating apparatus, and the inside of the apparatus is heated to a temperature of, for example, 500 ° C. with a heater, and a cathode electrode (evaporation source) made of a Cr—W—Ag alloy having a predetermined composition is formed in the apparatus. And, if necessary, a cathode electrode (evaporation source) made of a Ti—Al alloy having a predetermined composition or a cathode electrode (evaporation source) made of a Ti—Al—M alloy having a predetermined composition. Between the electrode and the cathode electrode (evaporation source), for example, arc discharge is generated under the condition of current: 110 A, and simultaneously, nitrogen gas is introduced into the apparatus as a reaction gas, for example, a reaction atmosphere of 3 Pa, On the other hand, the group For example, the lower layer composed of the (Ti, Al) layer or the (Ti, Al, M) layer and the (Cr, W, Ag) N layer are formed by vapor deposition under the condition that a bias voltage of −150 V is applied. The hard layer of the present invention is deposited by vapor-depositing two layers of the upper layer consisting of the above, or alternating layers of the (Ti, Al) layer or the (Ti, Al, M) layer and the (Cr, W, Ag) N layer. A coating layer can be deposited.

  According to one aspect of the coated tool of the present invention, the hard coating layer composed of a single (Cr, W, Ag) N layer has excellent wear resistance, and is a (Ti, Al) N layer or (Ti, Al , M) N-layer lower layer and (Cr, W, Ag) N-layer hard coating layer of the upper layer, in addition to this, excellent high temperature hardness, heat resistance, high temperature strength, Since it has wear resistance and high temperature oxidation resistance, the hard coating layer as a whole has excellent high temperature hardness, heat resistance, high temperature strength, etc., as well as excellent welding resistance. High heat resistance of difficult-to-cut materials such as stainless steel and heat-resistant steel, and excellent heat resistance even during high-speed cutting with heavy loads, excellent chipping resistance and wear resistance over a long period of time It demonstrates the nature.

  According to another aspect of the coated tool of the present invention, the hard coating layer is composed of an alternately laminated structure, and one of the layers is made of a (Ti, Al) N thin layer or a (Ti, Al, M) N thin layer. When constructed, it has excellent high-temperature hardness and high-temperature strength, or further excellent wear resistance and high-temperature oxidation resistance, and constitutes the other layer (Cr, W, Ag) N thin layer However, since it has excellent heat resistance and wear resistance, the hard coating layer as a whole has excellent wear resistance in addition to excellent high temperature hardness, high temperature strength, etc. In particular, it shows excellent chipping resistance even during high-speed cutting with high heat generated by difficult-to-cut materials such as stainless steel and heat-resistant steel, and a heavy load on the cutting edge. It exhibits excellent wear resistance.

The arc ion plating apparatus used for forming the hard coating layer which comprises this invention coated tool is shown, (a) is a schematic plan view, (b) is a schematic front view. It is a schematic explanatory drawing of the conventional arc ion plating apparatus used in forming the hard coating layer which comprises a comparative coating tool.

  Next, the coated tool of the present invention will be specifically described with reference to examples.

As raw material powders, WC powder, TiC powder, ZrC powder, VC powder, TaC powder, NbC powder, Cr ₃ C ₂ powder, TiN powder, TaN powder, and Co powder all having an average particle diameter of 1 to 3 μm are used. These raw material powders are mixed in the composition shown in Table 1, wet-mixed by a ball mill for 72 hours, dried, and press-molded into a green compact at a pressure of 100 MPa. Sintered under a vacuum of 1400 ° C. for 1 hour, and after sintering, WC-based cemented carbide tool bases A-1 to A-10 having a chip shape of ISO standard / CNMG120408 were sintered. Formed.

Moreover, as raw material powders, TiCN (mass ratio, TiC / TiN = 50/50) powder, Mo ₂ C powder, ZrC powder, NbC powder, TaC powder, all having an average particle diameter of 0.5 to 2 μm, WC powder, Co powder, and Ni powder are prepared. These raw material powders are blended in the blending composition shown in Table 2, wet-mixed by a ball mill for 24 hours, dried, and then pressed into a compact at a pressure of 100 MPa. This green compact was sintered in a 2 kPa nitrogen atmosphere at a temperature of 1500 ° C. for 1 hour. After sintering, the compact was made of a TiCN-based cermet having a chip shape of ISO standard / CNMG120408. Tool substrates B-1 to B-6 were formed.
(A) Next, each of the tool bases A-1 to A-10 and B-1 to B-6 is ultrasonically cleaned in acetone and dried, and then the arc ion plating apparatus shown in FIG. It is mounted along the outer periphery at a position that is a predetermined distance in the radial direction from the central axis on the inner rotary table, and cathode electrodes (evaporation sources) are arranged on both sides facing each other across the rotary table. Has an upper layer forming Cr—W—Ag alloy of a predetermined composition as a cathode electrode (evaporation source), and the other is Ti—Al for forming a lower layer of a predetermined composition as a cathode electrode (evaporation source). An alloy or a Ti-Al-M alloy,
(B) First, the inside of the apparatus is evacuated and kept at a vacuum of 0.1 Pa or less, and the inside of the apparatus is heated to 500 ° C. with a heater, and then the tool base that rotates while rotating on the rotary table is −1000 V. And applying a current of 100 A between the cathode electrode and the anode electrode to generate an arc discharge, thereby bombarding the surface of the tool base,
(C) Next, nitrogen gas is introduced as a reaction gas into the apparatus to form a reaction atmosphere of 4 Pa, a DC bias voltage of −100 V is applied to the tool base that rotates while rotating on the rotary table, and An arc discharge is generated by causing a current of 120 A to flow between any one of the Cr—W—Ag alloy, Ti—Al alloy or Ti—Al—M alloy of the cathode electrode and the anode electrode, and on the surface of the tool base, The (Ti, Al) N layer or (Ti, Al, M) N layer as the lower layer of the target composition and target layer thickness shown in Tables 3 and 4 was deposited with an average layer thickness of 0.5 to 5 μm. Then, the arc discharge between the cathode electrode (evaporation source) and the anode electrode is stopped,
(D) Subsequently, while maintaining the atmosphere in the apparatus in a nitrogen atmosphere of 2 Pa, an arc discharge is performed by flowing a current of 120 A between the cathode electrode (evaporation source) Cr—W—Ag alloy electrode and the anode electrode. The upper layer consisting of the (Cr, W, Ag) N layer having the target layer thickness shown in Tables 3 and 4 is formed by vapor deposition.
Hard coating layers were formed by vapor deposition according to the above (a) to (d), and surface-coated throwaway tips (hereinafter referred to as the present invention-coated tips) 1 to 24 as the present invention-coated tools were produced, respectively.

  For comparison purposes, these tool bases A-1 to A-10 and B-1 to B-6 were ultrasonically cleaned in acetone and dried, respectively, and the arc ion plating shown in FIG. The device was charged and a Ti-Al alloy or Ti-Al-M alloy having a predetermined composition was mounted as a cathode electrode (evaporation source). First, while evacuating the device and maintaining a vacuum of 0.1 Pa or less, After heating the inside of the apparatus to 500 ° C. with a heater, a DC bias voltage of −1000 V is applied to the tool base, and 150 A is provided between the cathode electrode of Ti—Al alloy or Ti—Al—M alloy and the anode electrode. Current is caused to flow and arc discharge is generated, and the tool base surface is bombarded with the Ti-Al alloy or Ti-Al-M alloy, and then nitrogen gas is introduced into the apparatus as a reaction gas. And a reaction atmosphere of 2 Pa is applied, and a bias voltage applied to the tool base is lowered to −90 V to generate an arc discharge between each cathode electrode and anode electrode of the predetermined composition, thereby the tool base. (Ti, Al) N layers or (Ti, Al, M) having the target compositions and target thicknesses shown in Tables 5 and 6 on the surfaces of A-1 to A-10 and B-1 to B-6. ) Surface coated throwaway tips (hereinafter referred to as comparative coated tips) 1 to 14 as comparative coated tools were produced by vapor deposition of a conventional hard coating layer composed of N layers.

Next, in the state where all the various coated chips are screwed to the tip of the tool steel tool with a fixing jig, the present coated chips 1 to 24 and the comparative coated chips 1 to 14 are as follows.
Work material: JIS / SUS304 (HB200) round bar,
Cutting speed: 140 m / min. ,
Cutting depth: 3 mm,
Feed: 0.2 mm / rev. ,
Cutting time: 5 minutes
Wet continuous high-speed cutting test of stainless steel under the following conditions (cutting condition A) (normal cutting speed and feed are 120 m / min. And 0.2 mm / rev., Respectively),
Work material: Ti-6Al-4V alloy (HB250) round bar,
Cutting speed: 55 m / min. ,
Incision: 2 mm,
Feed: 0.2 mm / rev. ,
Cutting time: 5 minutes
Wet continuous high-speed cutting test of Ti alloy under the following conditions (cutting condition B) (normal cutting speed and feed are 40 m / min. And 0.2 mm / rev., Respectively),
Work material: JIS S45C (HB200) round bar,
Cutting speed: 200 m / min. ,
Cutting depth: 0.2 mm,
Feed: 0.35 mm / rev. ,
Cutting time: 5 minutes
(Continuous cutting speed and feed are 160 m / min. And 0.25 mm / rev., Respectively)
The flank wear width of the cutting edge was measured in any high-speed cutting test. The measurement results are shown in Tables 7 and 8.

As in Example 1, all of WC powder, TiC powder, ZrC powder, VC powder, TaC powder, NbC powder, Cr ₃ C ₂ powder, TiN powder, TaN powder, and Co having an average particle diameter of 1 to 3 μm. A raw material powder composed of powder is blended in the blending composition shown in Table 1, wet mixed by a ball mill for 72 hours, dried, and press-molded into a green compact at a pressure of 100 MPa. In a vacuum of 1400 ° C. for 1 hour, and sintered to form a round tool sintered body for forming a tool base having a diameter of 13 mm. Tool bases (end mills) A-1 to A-10 made of a WC-base cemented carbide having a four-blade square shape with a diameter × length of 10 mm × 22 mm and a twist angle of 30 degrees. Each was manufactured.

  Then, the surfaces of these tool bases (end mills) A-1 to A-10 were ultrasonically cleaned in acetone and dried, and then charged into the arc ion plating apparatus shown in FIG. 1. Hard coating consisting of (Cr, W, Ag) N layer, (Ti, Al) N layer or (Ti, Al, M) N layer having the target composition and target layer thickness shown in Table 9 under the same conditions as in Table 1. The surface-coated carbide end mills (hereinafter referred to as the present invention-coated end mills) 1 to 15 as the present invention-coated tools were produced by depositing layers.

  For comparison purposes, the surfaces of the tool bases (end mills) A-1 to A-10 are ultrasonically cleaned in acetone and dried, and then loaded into the arc ion plating apparatus shown in FIG. Then, under the same conditions as in Example 1, a conventional hard coating layer consisting of a (Ti, Al) N layer or (Ti, Al, M) N layer having the target composition and target layer thickness shown in Table 10 is deposited. Thus, surface coated carbide end mills (hereinafter referred to as comparative coated end mills) 1 to 8 as comparative coated tools were produced, respectively.

Next, for the present invention coated end mills 1-15 and comparative coated end mills 1-8,
Work material—planar dimensions: 100 mm × 250 mm, thickness: 50 mm JIS / SUS304 (HB200) plate material,
Cutting speed: 120 m / min. ,
Groove depth (cut): 15 mm,
Table feed: 290 mm / min,
Wet high-speed grooving test of stainless steel under the following conditions (cutting condition D) (normal cutting speed and table feed are 90 m / min, 280 mm / min, respectively),
Work material—planar dimensions: 100 mm × 250 mm, thickness: 50 mm Ti-6Al-4V alloy (HB250) plate material,
Cutting speed: 60 m / min. ,
Groove depth (cut): 15 mm,
Table feed: 100 mm / min,
Wet high-speed grooving test of Ti alloy under the following conditions (cutting condition E) (normal cutting speed and table feed are 40 m / min. And 90 mm / min, respectively),
Work material-Plane dimensions: 100 mm x 250 mm, thickness: 50 mm JIS S45C (HB200) plate material,
Cutting speed: 230 m / min. ,
Groove depth (cut): 15 mm,
Table feed: 700 mm / min,
Wet high-speed grooving test of carbon steel under the following conditions (cutting conditions F) (normal cutting speed and table feed are 200 m / min. And 600 mm / min, respectively),
In each high-speed groove cutting test, the cutting groove length was measured until the flank wear width of the outer peripheral edge of the cutting edge reached 0.1 mm, which is a guide for the service life. The measurement results are shown in Table 9 and Table 10, respectively.

  Using the round bar sintered body with a diameter of 13 mm produced in Example 2, from this round bar sintered body, the diameter x length of the groove forming portion was 8 mm x 22 mm, respectively, by grinding, In addition, WC-base cemented carbide tool bases (drills) A-1 to A-10 having a two-blade shape with a twist angle of 30 degrees were manufactured.

  Next, the cutting edges of these tool bases (drills) A-1 to A-10 are subjected to honing, ultrasonically cleaned in acetone, and dried to the arc ion plating apparatus shown in FIG. The (Cr, W, Ag) N layer, (Ti, Al) N layer or (Ti, Al, M) with the target composition and target layer thickness shown in Table 11 under the same conditions as in Example 1. By subjecting a hard coating layer composed of N layers to vapor deposition, surface-coated carbide drills (hereinafter referred to as the present invention-coated drills) 1 to 15 as the present invention-coated tools were produced, respectively.

  For the purpose of comparison, honing is performed on the surfaces of the tool bases (drills) A-1 to A-10, ultrasonic cleaning is performed in acetone, and the arc ion plate shown in FIG. Conventionally, it comprises a (Ti, Al) N layer or a (Ti, Al, M) N layer having the target composition and target layer thickness shown in Table 12 under the same conditions as in the first embodiment. Surface-coated carbide drills (hereinafter referred to as comparative coated drills) 1 to 8 as comparative coated tools were produced by vapor-depositing a hard coating layer, respectively.

Next, for the present invention coated drills 1-15 and comparative coated drills 1-8,
Work material—planar dimensions: 100 mm × 250 mm, thickness: 50 mm JIS / SUS304 (HB200) plate material,
Cutting speed: 90 m / min. ,
Feed: 0.3 mm / rev. ,
Hole depth: 5 mm,
Wet high-speed drilling test of stainless steel under the following conditions (cutting condition G) (normal cutting speed and feed are 70 m / min. And 0.2 mm / rev., Respectively),
Work material—planar dimensions: 100 mm × 250 mm, thickness: 50 mm Ti-6Al-4V alloy (HB250) plate material,
Cutting speed: 50 m / min. ,
Feed: 0.2 mm / rev. ,
Hole depth: 5 mm,
Wet high-speed drilling test of Ti alloy under the following conditions (cutting condition H) ((normal cutting speed and feed are 40 m / min. And 0.15 mm / rev., Respectively),
Work material-Plane dimensions: 100 mm x 250 mm, thickness: 50 mm JIS S45C (HB200) plate material,
Cutting speed: 150 m / min. ,
Feed: 0.25 mm / rev. ,
Hole depth: 6 mm,
Wet high-speed drilling test of carbon steel under the following conditions (cutting condition I) (normal cutting speed and feed are 110 m / min. And 0.2 mm / rev., Respectively),
In each wet high-speed drilling test (using water-soluble cutting oil), the number of drilling processes until the flank wear width of the tip cutting edge surface reached 0.3 mm was measured. The measurement results are shown in Tables 11 and 12, respectively.

この結果得られた本発明被覆工具としての本発明被覆チップ１〜２４、本発明被覆エンドミル１〜１５、および本発明被覆ドリル１〜１５の硬質被覆層を構成する下部層である（Ｔｉ，Ａｌ）Ｎ層あるいは（Ｔｉ，Ａｌ，Ｍ）Ｎ層と上部層である（Ｃｒ，Ｗ，Ａｇ）Ｎ層の組成、並びに、比較被覆工具としての比較被覆チップ１〜１４、比較被覆エンドミル１〜８、および比較被覆ドリル１〜８の（Ｔｉ，Ａｌ）Ｎ層あるいは（Ｔｉ，Ａｌ，Ｍ）Ｎ層からなる硬質被覆層の組成を、透過型電子顕微鏡を用いてのエネルギー分散Ｘ線分析法により測定したところ、それぞれ目標組成と実質的に同じ組成を示した。

As a result, the present invention coated tools 1 to 24, the present coated end mills 1 to 15 and the lower layer constituting the hard coating layer of the present coated drill 1 to 15 (Ti, Al) ) N layer or (Ti, Al, M) N layer and upper (Cr, W, Ag) N layer composition, comparative coated tip 1-14 as comparative coated tool, comparative coated end mill 1-8 The composition of the hard coating layer made of the (Ti, Al) N layer or (Ti, Al, M) N layer of the comparative coated drills 1 to 8 is analyzed by energy dispersive X-ray analysis using a transmission electron microscope. When measured, each showed substantially the same composition as the target composition.

  Moreover, when the average layer thickness of each layer which comprises the said hard coating layer was cross-sectional measured using the scanning electron microscope, all showed the average value (average value of five places) substantially the same as target layer thickness.

  From the results shown in Tables 7 to 12, when the present coated tool forms a hard coating layer having a two-layer structure, the (Ti, Al) N layer, which is the lower layer, is firmly bonded to the surface of the tool substrate. In addition to these, the (Ti, Al, M) N layer, which has excellent high-temperature hardness, heat resistance and high-temperature strength, or the lower layer, has further excellent wear resistance and high-temperature oxidation resistance. Therefore, even in high-speed cutting of difficult-to-cut materials such as Ti alloy and stainless steel, excellent welding resistance with chips is ensured, so that chipping does not occur and excellent resistance over a long period of time. The hard coating layer is not provided with a (Cr, W, Ag) N layer, and the hard coating layer is a (Ti, Al) N layer or a (Ti, Al, M) N layer. In the comparative coated tools that are configured, all of the above difficult-to-cut In the high-speed cutting process, since the adhesiveness and reactivity between the work material (difficult-to-cut material) and the chips and the hard coating layer are further increased, chipping occurs at the cutting edge part, It is clear that the service life is reached in a short time.

  As raw material powders, WC powder, TiC powder, ZrC powder, VC powder, TaC powder, NbC powder, V3C2 powder, TiN powder, TaN powder, and Co powder each having an average particle diameter of 1 to 3 μm are prepared. The raw material powder was blended in the composition shown in Table 1, wet mixed by a ball mill for 72 hours, dried, and then pressed into a green compact at a pressure of 100 MPa. The green compact was heated at a temperature of 6 Pa in a vacuum. Sintering was performed at 1400 ° C. for 1 hour, and after sintering, tool bases A-1 to A-10 made of WC-base cemented carbide having a chip shape of ISO standard / CNMG120408 were formed.

Moreover, as raw material powders, TiCN (mass ratio, TiC / TiN = 50/50) powder, Mo2C powder, ZrC powder, NbC powder, TaC powder, WC powder, all having an average particle diameter of 0.5-2 μm, Co powder and Ni powder are prepared, and these raw material powders are blended in the blending composition shown in Table 2, wet mixed by a ball mill for 24 hours, dried, and then pressed into a compact at a pressure of 100 MPa, This green compact was sintered in a nitrogen atmosphere of 2 kPa at a temperature of 1500 ° C. for 1 hour, and after sintering, a tool substrate B-1 made of TiCN-based cermet having an ISO standard / CNMG120408 chip shape was obtained. ~ B-6 was formed.
(A) Next, each of the tool bases A-1 to A-10 and B-1 to B-6 is ultrasonically cleaned in acetone and dried, and then the arc ion plating apparatus shown in FIG. It is mounted along the outer periphery at a position that is a predetermined distance in the radial direction from the central axis on the inner rotary table, and cathode electrodes (evaporation sources) are arranged on both sides facing each other across the rotary table. Arranges a Ti-Al alloy or Ti-Al-M alloy with a predetermined composition as a cathode electrode (evaporation source), and arranges a Cr-W-Ag alloy with a predetermined composition as a cathode electrode (evaporation source) on the other side. And
(B) First, the inside of the apparatus is heated to 500 ° C. with a heater while the inside of the apparatus is evacuated and kept at a vacuum of 0.1 Pa or less. A DC bias voltage is applied, and a current of 100 A is passed between the Ti—Al alloy or Ti—Al—M alloy of the cathode electrode and the anode electrode to generate an arc discharge. Bombard cleaning with Al alloy or Ti-Al-M alloy,
(C) Next, nitrogen gas is introduced as a reaction gas into the apparatus to form a reaction atmosphere of 4 Pa, a DC bias voltage of −100 V is applied to the tool base that rotates while rotating on the rotary table, and An arc discharge is generated by passing a current of 120 A between the Ti—Al alloy or Ti—Al—M alloy of the cathode electrode and the anode electrode, and the targets shown in Tables 13 and 14 are formed on the surface of the tool base. After depositing (Ti, Al) N thin layer or (Ti, Al, M) N thin layer having a composition and a target layer thickness, the cathode electrode (evaporation source) of the Ti-Al alloy or Ti-Al-M alloy is formed. ) And the anode discharge between the anode electrode and
(D) Subsequently, while maintaining the atmosphere in the apparatus in a nitrogen atmosphere of 2 Pa, an arc discharge is performed by flowing a current of 120 A between the cathode electrode (evaporation source) Cr—W—Ag alloy electrode and the anode electrode. To generate a (Cr, W, Ag) N thin layer having a target composition and a target layer thickness shown in Tables 13 and 14,
The operations of (c) and (d) are repeated until a predetermined total average layer thickness is obtained, and a hard coating layer is formed by vapor deposition, and the present surface-coated throwaway tip (hereinafter referred to as the present invention) as the coated tool of the present invention. (Referred to as coated chips) 25 to 48 were produced.

  For comparison purposes, these tool bases A-1 to A-10 and B-1 to B-6 were ultrasonically cleaned in acetone and dried, respectively, and the arc ion plating shown in FIG. The device was charged and a Ti-Al alloy or Ti-Al-M alloy having a predetermined composition was mounted as a cathode electrode (evaporation source). First, while evacuating the device and maintaining a vacuum of 0.1 Pa or less, After heating the inside of the apparatus to 500 ° C. with a heater, a DC bias voltage of −1000 V was applied to the tool base, and 100 A was applied between the cathode electrode of Ti—Al alloy or Ti—Al—M alloy and the anode electrode. An electric current is applied to generate an arc discharge, so that the tool base surface is bombarded with the Ti-Al alloy or Ti-Al-M alloy, and then nitrogen gas is introduced into the apparatus as a reaction gas. And a bias voltage applied to the tool base is lowered to -100 V to generate an arc discharge between the cathode electrode and the anode electrode of the predetermined composition, and the tool base A- (Ti, Al) N thin layer or (Ti, Al, M) of the target compositions and target layer thicknesses shown in Tables 15 and 16 on the surfaces of 1 to A-10 and B-1 to B-6 Surface-coated throwaway tips (hereinafter referred to as comparative coated tips) 15 to 30 as comparative coated tools were produced by vapor deposition of conventional hard coating layers composed of N thin layers.

Next, with the various coated chips, all of the coated chips 25 to 48 and the comparative coated chips 15 to 30 of the present invention with the fixing tool fixed to the tip of the tool steel tool.
Work material: JIS / SUS304 (HB220) round bar,
Cutting speed: 130 m / min. ,
Cutting depth: 3mm,
Feed: 0.3 mm / rev. ,
Cutting time: 5 minutes
(Continuous cutting speed and feed are 110 m / min. And 0.2 mm / rev., Respectively)
Work material: Ti-6Al-4V alloy (HB290) round bar,
Cutting speed: 50 m / min. ,
Cutting depth: 2mm,
Feed: 0.2 mm / rev. ,
Cutting time: 5 minutes
Wet continuous high-speed cutting test of Ti alloy under the following conditions (cutting condition b) (normal cutting speed and feed are 30 m / min. And 0.15 mm / rev., Respectively),
Work material: JIS S45C (HB220) round bar,
Cutting speed: 200 m / min. ,
Cutting depth: 0.2mm,
Feed: 0.3 mm / rev. ,
Cutting time: 5 minutes
Wet continuous high-speed cutting test of carbon steel under the following conditions (cutting condition c) (normal cutting speed and feed are 150 m / min. And 0.25 mm / rev., Respectively),
The flank wear width of the cutting edge was measured in any high-speed cutting test. The measurement results are shown in Tables 17 and 18.

  As in Example 4, all of the raw materials consisting of WC powder, TiC powder, ZrC powder, VC powder, TaC powder, NbC powder, V3C2 powder, TiN powder, TaN powder, and Co powder having an average particle diameter of 1 to 3 μm The powder was blended into the blending composition shown in Table 1, wet-mixed for 72 hours with a ball mill, dried, and then pressed into a green compact at a pressure of 100 MPa. Sintered at 1400 ° C. for 1 hour to form a round tool sintered body for forming a tool base having a diameter of 13 mm. From the round bar sintered body, the diameter of the cutting edge portion × WC-base cemented carbide tool bases (end mills) A-1 to A-10 having a length of 10 mm × 22 mm and a four-blade square shape with a twist angle of 30 degrees were manufactured.

  Then, the surfaces of these tool bases (end mills) A-1 to A-10 were ultrasonically cleaned in acetone and dried, and then charged into the arc ion plating apparatus shown in FIG. Under the same conditions as in Example 1, the target composition shown in Table 19 and the (Ti, Al) N thin layer or (Ti, Al, M) N thin layer having a target layer thickness of one layer and the target composition also shown in Table 19 are used. And a hard coating layer having an alternate laminated structure of (Cr, W, Ag) N thin layers having a target layer thickness by vapor deposition to form a surface-coated carbide end mill (hereinafter referred to as the present invention) as a coated tool of the present invention. Inventive coated end mills (16-30) were produced.

  For comparison purposes, the surfaces of the tool bases (end mills) A-1 to A-10 are ultrasonically cleaned in acetone and dried, and then loaded into the arc ion plating apparatus shown in FIG. Then, under the same conditions as in Example 1, a conventional hard coating layer composed of a (Ti, Al) N thin layer or a (Ti, Al, M) N thin layer having a target composition and a target layer thickness shown in Table 20 was used. By vapor deposition, surface coated carbide end mills (hereinafter referred to as comparative coated end mills) 9 to 16 as comparative coated tools were produced.

Next, for the coated end mills 16 to 30 and the comparative coated end mills 9 to 16 of the present invention,
Work material-Plane dimensions: 100 mm x 250 mm, thickness: 50 mm JIS / SUS304 (HB220) plate material,
Cutting speed: 110 m / min. ,
Groove depth (cut): 15mm,
Table feed: 300mm / min,
Wet high-speed grooving test of stainless steel under the following conditions (cutting condition d) (normal cutting speed and table feed are 80 m / min, 270 mm / min, respectively),
Work material—planar dimensions: 100 mm × 250 mm, thickness: 50 mm Ti-6Al-4V (HB290) plate,
Cutting speed: 65 m / min. ,
Groove depth (cut): 15mm,
Table feed: 80mm / min,
Wet high-speed grooving test of Ti alloy under the following conditions (cutting condition e) (normal cutting speed and table feed are 30 m / min. And 80 mm / min, respectively),
Work material-Plane dimensions: 100 mm x 250 mm, thickness: 50 mm JIS S45C (HB220) plate material,
Cutting speed: 240 m / min. ,
Groove depth (cut): 15mm,
Table feed: 550mm / min,
Wet high-speed grooving test of carbon steel under the following conditions (cutting condition f) (normal cutting speed and table feed are 200 m / min. And 500 mm / min, respectively),
In each high-speed groove cutting test, the cutting groove length was measured until the flank wear width of the outer peripheral edge of the cutting edge reached 0.1 mm, which is a guide for the service life. The measurement results are shown in Table 19 and Table 20, respectively.

  Using the round bar sintered body with a diameter of 13 mm manufactured in Example 5, from this round bar sintered body, the diameter x length of the groove forming portion is 8 mm x 22 mm and twisted by grinding. WC base cemented carbide tool bases (drills) A-1 to A-10 having a two-blade shape with a 30-degree angle were manufactured.

  Next, the cutting edges of these tool bases (drills) A-1 to A-10 are subjected to honing, ultrasonically cleaned in acetone, and dried to the arc ion plating apparatus shown in FIG. Under the same conditions as in Example 4, the (Ti, Al) N thin layer or (Ti, Al, M) N thin layer having the target composition and target layer thickness shown in Table 21 and the same table are used. 21. The surface-coated carbide of the present invention as the coated tool of the present invention is formed by vapor-depositing a hard coating layer comprising an alternately laminated structure of (Cr, W, Ag) N thin layers having a target composition shown in FIG. Drills 16 to 30 (hereinafter referred to as the present invention-coated drills) 16 to 30 were manufactured.

  For the purpose of comparison, honing is performed on the surfaces of the tool bases (drills) A-1 to A-10, ultrasonic cleaning is performed in acetone, and the arc ion plate shown in FIG. (Ti, Al) N thin layer or (Ti, Al, M) N thin layer having the target composition and the target layer thickness shown in Table 22 under the same conditions as in the fourth embodiment. Surface-coated carbide drills (hereinafter referred to as comparative coated drills) 9 to 16 as comparative coated tools were produced by vapor-depositing conventional hard coated layers made of

Next, for the inventive coated drills 16-30 and comparative coated drills 9-16,
Work material-Plane dimensions: 100 mm x 250 mm, thickness: 50 mm JIS / SUS304 (HB220) plate material,
Cutting speed: 90 m / min. ,
Feed: 0.3 mm / rev. ,
Hole depth: 5 mm,
Wet high-speed drilling test of stainless steel under the following conditions (cutting condition g) (normal cutting speed and feed are 60 m / min. And 0.2 mm / rev., Respectively),
Work material-planar dimensions: 100 mm x 250 mm, thickness: 50 mm Ti-6Al-4V alloy (HB290) plate material,
Cutting speed: 50 m / min. ,
Feed: 0.2 mm / rev. ,
Hole depth: 5 mm,
Wet high-speed drilling test of Ti alloy under the following conditions (cutting condition h) (normal cutting speed and feed are 30 m / min. And 0.1 mm / rev., Respectively),
Work material-Plane dimensions: 100 mm x 250 mm, thickness: 50 mm JIS S45C (HB220) plate material,
Cutting speed: 150 m / min. ,
Feed: 0.2 mm / rev. ,
Hole depth: 6mm,
Wet high-speed drilling test of carbon steel under the following conditions (cutting condition i) (normal cutting speed and feed are 100 m / min. And 0.2 mm / rev., Respectively),
In each wet high-speed drilling test (using water-soluble cutting oil), the number of drilling processes until the flank wear width of the tip cutting edge surface reached 0.3 mm was measured. The measurement results are shown in Table 21 and Table 22, respectively.

この結果得られた本発明被覆工具としての本発明被覆チップ２５〜４８、本発明被覆エンドミル１６〜３０、および本発明被覆ドリル１６〜３０の硬質被覆層を構成する（Ｔｉ，Ａｌ）Ｎ薄層あるいは（Ｔｉ，Ａｌ，Ｍ）Ｎ薄層、および（Ｃｒ，Ｗ，Ａｇ）Ｎ薄層の組成、並びに、比較被覆工具としての比較被覆チップ２１〜３６、比較被覆エンドミル９〜１６、および比較被覆ドリル９〜１６の（Ｔｉ，Ａｌ）Ｎ薄層あるいは（Ｔｉ，Ａｌ，Ｍ）Ｎ薄層からなる硬質被覆層の組成を、透過型電子顕微鏡を用いてのエネルギー分散Ｘ線分析法により測定したところ、それぞれ目標組成と実質的に同じ組成を示した。

(Ti, Al) N thin layer constituting the hard coating layer of the present coated tip 25-48, the present coated end mill 16-30, and the present coated drill 16-30 as the present coated tool obtained as a result of this. Alternatively, the composition of (Ti, Al, M) N thin layer and (Cr, W, Ag) N thin layer, and comparative coating tips 21 to 36 as comparative coating tools, comparative coating end mills 9 to 16, and comparative coating The composition of the hard coating layer made of (Ti, Al) N thin layer or (Ti, Al, M) N thin layer of drills 9 to 16 was measured by energy dispersive X-ray analysis using a transmission electron microscope. However, each showed substantially the same composition as the target composition.

  Moreover, when the average layer thickness of each layer which comprises the said hard coating layer was cross-sectional measured using the scanning electron microscope, all showed the average value (average value of five places) substantially the same as target layer thickness.

  From the results shown in Tables 17 to 22, all of the coated tools of the present invention are hard even in high-speed and high-feed cutting that is accompanied by a large heat generation and requires a heavy load, especially for difficult-to-cut materials such as stainless steel and heat-resistant steel. The (Ti, Al) N thin layer or (Ti, Al, M) N thin layer constituting the alternating layer structure of the coating layer has excellent high-temperature hardness, high-temperature strength, or in addition, excellent wear resistance. (Cr, W, Ag) N thin layers that have the same properties and alternate-layer structure, have excellent heat resistance, and are excellent between the work material and chips even under high temperature conditions. As a result, the (Ti, Al) N thin layer or the (Ti, Al, M) N thin layer has insufficient welding resistance which is alternately stacked on this (Cr, W, Ag). ) By supplementing with N thin layer, the entire hard coating layer is The hard coating layer is composed of a thin layer of (Ti, Al) N or a thin layer of (Ti, Al, M) N, while exhibiting excellent wear resistance over a long period of time. In comparative coated tools that do not have a thin layer of Cr, W, Ag) N, the adhesiveness between the work material (difficult-to-cut material) and chips and the hard coating layer in the high-speed cutting of the work material It is clear that since the reactivity is further increased, chipping occurs at the cutting edge and the service life is reached in a relatively short time.

  As described above, the coated tool of the present invention has excellent wear resistance and resistance not only to cutting general work materials but also to high-speed cutting of difficult-to-cut materials such as stainless steel and heat-resistant steel. Since it exhibits weldability and exhibits excellent cutting performance over a long period of time, it can be used satisfactorily to meet FA requirements for cutting equipment, labor saving and energy saving, and cost reduction. is there.

Claims (5)

In a surface-coated cutting tool formed by forming a hard coating layer on the surface of a tool base composed of tungsten carbide-based cemented carbide or titanium carbonitride-based cermet,
The hard coating layer has an average layer thickness of 0.5 to 5 μm, and
Composition formula: (Cr _1-XY W _X Ag _Y ) N (where X represents the content ratio of W, Y represents the content ratio of Ag, and the atomic ratio is 0.01 ≦ X ≦ 0.30. A surface-coated cutting tool comprising a composite nitride layer of Cr, W, and Ag satisfying 0.01 ≦ Y ≦ 0.20. In a surface-coated cutting tool formed by forming a hard coating layer on the surface of a tool base composed of tungsten carbide-based cemented carbide or titanium carbonitride-based cermet,
The hard coating layer is
(A) having an average layer thickness of 0.5-5 μm, and
Composition of Ti and Al satisfying the composition formula: (Ti _1-α Al _α ) N (where α is the Al content ratio and the atomic ratio is 0.45 ≦ α ≦ 0.75) A lower layer made of a nitride layer;
(B) having an average layer thickness of 0.5-5 μm, and
Composition formula: (Cr _1-XY W _X Ag _Y ) N (where X represents the content ratio of W, Y represents the content ratio of Ag, and the atomic ratio is 0.01 ≦ X ≦ 0.30. A surface-coated cutting tool comprising: an upper layer made of a composite nitride layer of Cr, W, and Ag satisfying 0.01 ≦ Y ≦ 0.20. In a surface-coated cutting tool formed by forming a hard coating layer on the surface of a tool base composed of tungsten carbide-based cemented carbide or titanium carbonitride-based cermet,
The hard coating layer is
(A) having an average layer thickness of 0.01 to 0.1 μm, and
Composition of Ti and Al satisfying the composition formula: (Ti _1-α Al _α ) N (where α is the Al content ratio and the atomic ratio is 0.45 ≦ α ≦ 0.75) (Ti, Al) N thin layer made of a nitride layer,
(B) having an average layer thickness of 0.01 to 0.1 μm, and
Composition formula: (Cr _1-XY W _X Ag _Y ) N (where X represents the content ratio of W, Y represents the content ratio of Ag, and the atomic ratio is 0.01 ≦ X ≦ 0.30. (Cr, W, Ag) N thin layer composed of a composite nitride layer of Cr, W and Ag satisfying 0.01 ≦ Y ≦ 0.20
A surface-coated cutting tool comprising the alternating lamination of (a) and (b) and having a total average layer thickness of 1 to 5 μm. In a surface-coated cutting tool formed by forming a hard coating layer on the surface of a tool base composed of tungsten carbide-based cemented carbide or titanium carbonitride-based cermet,
The hard coating layer is
(A) having an average layer thickness of 0.5-5 μm, and
Composition formula: (Ti _1-α-β Al _α M _β ) N (where M is a member selected from the group 4a, 5a, 6a elements except Si, Si, B, Y) Seeds or two or more kinds of additive components, α is a content ratio of Al, β is a content ratio of M, and atomic ratio is 0.45 ≦ α ≦ 0.75, 0.01 ≦ β ≦ A lower layer composed of a composite nitride layer of Ti, Al, and M satisfying 0.25),
(B) having an average layer thickness of 0.5-5 μm, and
Composition formula: (Cr _1-XY W _X Ag _Y ) N (where X represents the content ratio of W, Y represents the content ratio of Ag, and the atomic ratio is 0.01 ≦ X ≦ 0.30. A surface-coated cutting tool comprising: an upper layer made of a composite nitride layer of Cr, W, and Ag satisfying 0.01 ≦ Y ≦ 0.20. In a surface-coated cutting tool formed by forming a hard coating layer on the surface of a tool base composed of tungsten carbide-based cemented carbide or titanium carbonitride-based cermet,
The hard coating layer is
(A) having an average layer thickness of 0.01 to 0.1 μm, and
Composition formula: (Ti _1-α-β Al _α M _β ) N (where M is a member selected from the group 4a, 5a, 6a elements except Si, Si, B, Y) Seeds or two or more kinds of additive components, α is a content ratio of Al, β is a content ratio of M, and atomic ratio is 0.45 ≦ α ≦ 0.75, 0.01 ≦ β ≦ (Ti, Al, M) N thin layer composed of a composite nitride layer of Ti, Al, and M satisfying 0.25)
(B) having an average layer thickness of 0.01 to 0.1 μm, and
Composition formula: (Cr _1-XY W _X Ag _Y ) N (where X represents the content ratio of W, Y represents the content ratio of Ag, and the atomic ratio is 0.01 ≦ X ≦ 0.30. (Cr, W, Ag) N thin layer composed of a composite nitride layer of Cr, W and Ag satisfying 0.01 ≦ Y ≦ 0.20
A surface-coated cutting tool comprising the alternating lamination of (a) and (b) and having a total average layer thickness of 1 to 5 μm.

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