Coated cutting tool

Abstract

The present invention relates to a coated cutting tool (1) comprising a substrate (5) and a coating (6), the coating (6) being Ti 1-x Al x N, a first nano-layer (9) with 0.55 < x ≦ 0.70, and Ti 1-y-z Al y Si z N, a second nano-layer (10) with 0.20 ≦ y ≦ 0.50, 0.13 ≦ z ≦ 0.25, 0.46 ≦ y + z ≦ 0.65, and includes a nano-multilayer (8) of alternating layers, a series of one first nano-layer (9) and one second nano-layer (10) form a layer period, and the average layer period thickness of the nano-multilayer (8) is 20 nm or less.

Description

Technical Field

[0001] The present invention relates to a coated cutting tool including a nano multilayer of (Ti,Al)N and (Ti,Al,Si)N.

Background Art

[0002] Generally, cutting tools for metal machining include a hard base material such as cemented carbide having a thin hard wear-resistant coating. The cutting tool generally has at least one rake face and at least one flank face. The cutting edge exists at the place where the rake face and the flank face intersect.

[0003] In the field of cutting tools for metal machining, nano multilayer coatings are generally used. In these coatings, at least two sub-layers that are different in some points are alternately arranged to form a coating of a nano-layer stack. Various metal nitrides are generally used for the wear-resistant coating of the cutting tool.

[0004] Examples of metal machining operations include turning, milling, and drilling.

[0005]

[0006] ​Various metal machining operations affect coated cutting tools in various ways. For example, turning is a continuous metal machining operation, while milling is, in essence, more intermittent. In milling, the thermal and mechanical loads change over time. Thermal stresses that can induce so-called thermal cracks, referred to herein as "comb cracks", are induced in the coating, and comb cracks can cause fatigue at the cutting edge, leading to chipping, i.e., small pieces of the cutting edge breaking off from the rest of the substrate. Therefore, the common types of wear of coated cutting tools in milling are cracks and chipping. Thus, enhancing comb crack resistance is very important for extending tool life.

[0007] In particular, a high level of toughness of the coating at the cutting edge, i.e., a high level of edge toughness, is also beneficial for reducing chipping.

[0008] Flank wear occurs mainly from the wear mechanism and is clearly visible on the flank of the cutting edge. Since the flank receives the movement of the workpiece, if there is too much flank wear, the surface texture of the workpiece will be insufficient, the cutting process will be inaccurate, and friction will increase in the cutting process. When better flank wear resistance is provided, a longer tool life is provided for a certain metal machining operation.

[0009] The coating must also remain adhered to the substrate during the machining operation, i.e., it must not peel off. Some types of workpiece materials, such as ISO-M (stainless steel) and ISO-S (heat-resistant superalloys, e.g., titanium), are so-called sticky materials and induce more flaking than other types of workpiece materials. These types of materials also have a smearing behavior, which means that the workpiece material can be smeared on the cutting tool surface and ultimately lead to the formation of a built-up edge (BUE) of the workpiece material on the cutting edge. Such a BUE can sometimes peel off the coating or even part of the cutting edge of the cutting tool.

[0010] In order to provide a cutting tool having characteristics superior to those of currently commercially available cutting tools, a coated cutting tool having excellent coating characteristics in terms of flank wear resistance, chipping crack resistance, flaking resistance, edge toughness, etc. has been constantly demanded. When one or more of the above characteristics are improved, a longer tool life is provided.

[0011] An object of the present invention is to provide a coated cutting tool that exhibits high flank wear resistance during at least turning operations and high resistance to chipping cracks during milling operations.

[0012] Furthermore, a further object of the present invention is to provide a coated cutting tool having high flaking resistance during machining of smearing materials such as stainless steel.

[0013] Definition The term "average layer period thickness" means the average thickness of the combination A-B in a nano multilayer coating of the first nano layer A and the second nano layer B in the nano multilayer A-B-A-B-A... When the deposition process is known, the calculation can be performed by dividing the total thickness of the nano multilayer by the number of A-B depositions (corresponding to the number of rotations when depositing the substrate by rotation).

[0014] Alternatively, the calculation is performed by using TEM analysis of the cross-section of the nano multilayer to count the number of combinations of consecutive A-B nano layers over a length of at least 200 nm and calculating the average value.

[0015] When the total thickness of the nano multilayer is only 0.5 μm, the measurement location is located directly below the outer surface of the nano multilayer. Suitable analysis methods include transmission electron microscopy (TEM).

[0016] The term "FWHM" means "full width at half maximum", which is the X-ray diffraction peak width in degrees (2θ) that is half of the peak intensity of the X-ray diffraction peak (for a specific (hkl) diffraction peak).

SUMMARY OF THE INVENTION

[0017] Here, a nano-multilayer coating in which (Ti,Si)N layers and (Ti,Al,Si)N layers alternate, with extremely high chipping resistance and flank wear resistance, is provided.

[0018] The present invention relates to a coated cutting tool including a substrate and a coating, the coating including a nano-multilayer of alternating layers of a first nano-layer of Ti 1-x Al x N with 0.55 < x ≦ 0.70 and a second nano-layer of Ti 1-y-z Al y Si z N with 0.20 ≦ y ≦ 0.50, 0.13 ≦ z ≦ 0.25, and 0.46 ≦ y + z ≦ 0.65, where a series of one first nano-layer and one second nano-layer form a layer period, and the average layer period thickness of the nano-multilayer is 20 nm or less.

[0019] For the Ti 1-x Al x N of the first nano-layer, preferably 0.56 ≦ x ≦ 0.65, more preferably 0.58 ≦ x ≦ 0.63, and most preferably 0.58 ≦ x ≦ 0.61.

[0020] For the Ti 1-y-z Al y Si z N of the second nano-layer, preferably 0.25 ≦ y ≦ 0.45 and 0.13 ≦ z ≦ 0.20, more preferably 0.28 ≦ y ≦ 0.40 and 0.14 ≦ z ≦ 0.18, and most preferably 0.33 ≦ y ≦ 0.40 and 0.14 ≦ z ≦ 0.17.

[0021] For the Ti 1-y-z Al y Si z N of the second nano-layer, preferably 0.46 ≦ y + z ≦ 0.60, more preferably 0.47 ≦ y + z ≦ 0.55.

[0022] The average layer period thickness of the nano-multilayer is preferably 2 - 15 nm, such as 3 - 10 nm, or 3 - 7 nm.

[0023] In one embodiment, the nano-multilayer has a columnar microstructure. This means that columnar crystallites, i.e., "crystal grains" that are elongated in the growth direction as a whole, are present in the nano-multilayer.

[0024] In one embodiment, the nano-multilayer has 200 crystal selection orientations. In this embodiment, the intensity ratio I(200) / I(111) in theta-2theta X-ray diffraction analysis is preferably greater than 5, for example, greater than 10 or greater than 20.

[0025] In one embodiment, the nano-multilayer has a FWHM value of the cubic (200) peak in X-ray diffraction that is 0.4 to 1 degree (2theta), for example, 0.5 to 0.9 degree (2theta), or 0.6 to 0.8 degree (2theta).

[0026] The (200) peak of the XRD used to determine the FWHM value is the exfoliated Cu-K α2 is.

[0027] The thickness of the nano-multilayer is preferably about 0.5 to about 15 μm, preferably about 1 to about 10 μm, more preferably about 1 to about 7 μm, and most preferably about 1.5 to about 4 μm.

[0028] The nano-multilayer is preferably a cathodic arc deposition layer.

[0029] In one embodiment, the coating includes a layer of TiN, (Ti,Al)N, or (Cr,Al)N under the nano-multilayer, preferably closest to the substrate.

[0030] Preferably, the innermost layer is (Ti,Al)N. When (Ti,Al)N is used, (Ti,Al)N is preferably Ti 1-v Al v N, where 0.35 ≦ v ≦ 0.70, preferably 0.45 ≦ v ≦ 0.65, and most preferably 0.55 < v ≦ 0.65. In a preferred embodiment, the Ti-Al relationship in (Ti,Al)N is for the first nano-layer of the nano-multilayer, i.e., Ti 1-v Alv It is the same as the Ti-Al relationship in N, preferably 0.55 ≦ v ≦ 0.70, for example 0.56 ≦ v ≦ 0.65, or 0.58 < v ≦ 0.63, or 0.58 < v ≦ 0.61. The thickness of this innermost layer can be about 0.1 to about 3 μm, about 0.2 to about 2 μm, and most preferably about 0.5 to about 1.5 μm.

[0031] In a preferred embodiment, the coating is Ti 1-x Al x N, a first nanolayer with 0.55 < x ≦ 0.65, and Ti 1-y-z Al y Si z N, a second nanolayer with 0.25 ≦ y ≦ 0.45 and 0.13 ≦ z ≦ 0.20, 0.46 ≦ y + z ≦ 0.65, including a nanomultilayer of alternating layers, the average layer periodic thickness of the nanomultilayer is 3 to 10 nm, the thickness of the nanomultilayer is about 1 to about 7 μm, and under the nanomultilayer closest to the substrate, there is an innermost layer of (Ti,Al)N having a thickness of about 0.5 to about 1.5 μm.

[0032] In a more preferred embodiment, the coating is Ti 1-x Al x N, a first nanolayer with 0.55 < x ≦ 0.63, and Ti 1-y-z Al y Si z N, a second nanolayer with 0.28 ≦ y ≦ 0.40 and 0.13 ≦ z ≦ 0.17, 0.47 ≦ y + z ≦ 0.55, including a nanomultilayer of alternating layers, the average layer periodic thickness of the nanomultilayer is 3 to 10 nm, the thickness of the nanomultilayer is about 1 to about 7 μm, and under the nanomultilayer closest to the substrate, there is an innermost layer of (Ti,Al)N having a thickness of about 0.5 to about 1.5 μm.

[0033] The substrate of the coated cutting tool can be selected from the group consisting of cemented carbide, cermet, ceramic, cubic boron nitride, and high-speed steel. In one embodiment, the substrate is a cemented carbide containing 5 to 18 wt% Co and 0 to 10 wt% carbide nitride, or carbonitride of Groups 4 to 5 in the periodic table of elements.

[0034] Additional components such as Cr are possible in the cemented carbide substrate.

[0035] The coated cutting tool is preferably a cutting tool insert for metal machining, a drill, or a solid end mill. The cutting tool insert is, for example, a turning insert or a milling insert.

Brief Description of the Drawings

[0036]

Figure 1

Figure 2

Figure 3

Modes for Carrying Out the Invention

[0037] FIG. 1 shows a schematic view of an embodiment of a cutting tool (1) having a rake face (2), a flank face (3), and a cutting edge (4). The cutting tool (1) is a milling insert in this embodiment. FIG. 2 shows a schematic view of an embodiment of a cutting tool (1) having a rake face (2), a flank face (3), and a cutting edge (4). The cutting tool (1) is a turning insert in this embodiment.

[0038] FIG. 3 shows a schematic cross-sectional view of an embodiment of the coated cutting tool of the present invention having a substrate body (5) and a coating (6). The coating consists of a first (Ti,Al)N innermost layer (7), followed by a nano-multilayer (8) in which nano-layers (9) of Ti 1-x Al x N and nano-layers (10) of Ti 1-y-z Al y Si z N alternate.

Examples

[0039] Example 1: Different nanolayers of (Ti,Al)N and (Ti,Al,Si)N were deposited on the blanks of sintered carbide cutting tool inserts of the shapes SNMA120408, CNMG120408MM, and R390-11. The composition of the carbide alloy was 10 wt% Co, 0.4 wt% Cr, and the balance WC. The carbide alloy blanks were coated by cathodic arc evaporation in a vacuum chamber equipped with four arc flanges. The Ti-Al-Si targets were attached to two of the flanges facing each other. The Ti-Al targets were attached to the remaining two flanges facing each other. The targets were circular and flat, 100 mm in diameter, and were available on the open market. Target technology packages suitable for arc evaporation were available from suppliers in the market, such as IHI Hauzer Techno Coating B.V., Kobelco, and Oerlikon Balzers.

[0040] The uncoated blanks were attached to pins that received three-fold rotation in the PVD chamber.

[0041] Samples 1 - 4: The chamber was pumped down to a high vacuum (less than 10 -2 Pa) and heated to 450 - 550 °C by a heater placed inside the chamber. The blanks were then etched in Ar plasma for 60 minutes.

[0042] First, only the Ti 0.40 Al 0.60 target, the Ti-Al target, was used to deposit the innermost layer of Ti 0.40 Al 0.60 N with a thickness of approximately 1 μm. The process conditions for depositing the innermost (Ti,Al)N layer were a chamber pressure (reaction pressure) of 4 Pa of N 2 gas and a DC bias voltage of -70 V applied to the blank assembly (with respect to the chamber wall). The cathodes were operated in arc discharge mode with a current of 150 A each.

[0043] Next, both a Ti-Al target and a Ti-Al-Si target were used. The chamber pressure (reaction pressure) was set to 4 Pa of N 2 gas, and a -70 V DC bias voltage (with respect to the chamber wall) was applied to the blank assembly. The cathodes were operated in arc discharge mode at 150 A of current each for 75 minutes (for four flanges). A nano-multilayer coating with a thickness of approximately 3 μm was deposited on the blank.

[0044] Ti 0.50 Al 0.35 Si 0.15 、Ti 0.50 Al 0.30 Si 0.20 、Ti 0.35 Al 0.55 Si 0.10 、およびTi 0.30 Al 0.60 Si 0.10 That is, deposition was carried out in combination with a Ti-Al-Si target and a Ti-Al target which is Ti 0.40 Al 0.60 . The total thickness of the deposited nano-multilayer was approximately 3 μm (when measured at the flank face). The rotation speed correlates with a constant periodic thickness. In the specific apparatus used, a rotation speed of 5 rpm used correlates with a nano-layer periodic thickness of approximately 5 nm.

[0045] The fabricated samples are called "Sample 1 (the present invention)", "Sample 2 (the present invention)", "Sample 3 (comparative example)", and "Sample 4 (comparative example)".

[0046] Sample 5 As a further comparison, coatings containing nano-multilayers of (Ti,Al)N and (Ti,Si)N were deposited on the blanks of sintered carbide cutting tool inserts of the shapes SNMA120408, CNMG120408MM, and R390-11. The composition of the carbide alloy was the same as that of Samples 1 to 4. The carbide alloy blanks were coated by cathodic arc evaporation in a vacuum chamber equipped with four arc flanges. Ti-Si targets were attached to two of the flanges facing each other. Ti-Al targets were attached to the remaining two flanges facing each other. The targets were circular and flat, 100 mm in diameter, and available on the open market. Target technology packages suitable for arc evaporation were available from suppliers in the market, such as IHI Hauzer Techno Coating B.V., Kobe Steel, Ltd., and Oerlikon Balzers.

[0047] The uncoated blanks were attached to pins that received three-fold rotation in the PVD chamber.

[0048] The chamber was pumped down to a high vacuum (less than 10 -2 Pa) and heated to 450 - 550 °C by heaters placed in the chamber. The blanks were then etched in Ar plasma for 60 minutes.

[0049] First, only the Ti 0.40 Al 0.60 target, which was the Ti-Al target, was used to deposit the innermost layer with a thickness of approximately 1 μm of Ti 0.40 Al 0.60 N. The process conditions for depositing the innermost (Ti,Al)N layer were a chamber pressure (reaction pressure) of 4 Pa of N 2 gas, and a DC bias voltage of -70 V applied to the blank assembly (with respect to the chamber wall). The cathodes were operated in arc discharge mode with a current of 150 A (each).

[0050] Next, both the Ti-Al target and the Ti-Si target were utilized. The chamber pressure (reaction pressure) was set to 4 Pa of N 2 gas, and a DC bias voltage of -70 V (with respect to the chamber wall) was applied to the blank assembly. The cathodes were operated in arc discharge mode at a current of 150 A each for 75 minutes (for four flanges). A nano-multilayer coating with a thickness of approximately 3 μm was deposited on the blank.

[0051] The rotation speed correlates with a constant periodic thickness. In the specific apparatus used, a rotation speed of 5 rpm used correlates with a nano-layer periodic thickness of approximately 5 nm.

[0052] The fabricated sample is referred to as "Sample 5 (comparative example)".

[0053] The fabricated Samples 1 to 5 are listed in Table 1. TIFF2025518128000002.tif65170

[0054] As a result of measuring the actual elemental composition in the (Ti,Al)N and (Ti,Al,Si)N coatings using energy-dispersive X-ray spectroscopy (EDS), it was shown that a deviation of only 1 to 2 percentage units from the theoretical composition based on the target composition was confirmed. These small deviations are within the accuracy of the EDS method. Therefore, it is concluded that the actual elemental composition of Ti, Al, and Si in the layers deposited here substantially corresponds well to the respective target compositions used.

[0055] Example 2 (Analysis): From the SEM imaging of Samples 1 to 5, it was confirmed that the nano-multilayer had a columnar structure.

[0056] Furthermore, X-ray diffraction (XRD) analysis was performed on the relief surface of the coated insert using a PANalytical CubiX3 diffractometer equipped with a PIXcel detector. The coated cutting tool insert was attached to a sample holder such that the relief surface of the sample was parallel to the reference surface of the sample holder and the relief surface was at an appropriate height. With a voltage of 45 kV and a current of 40 mA, Cu-K α irradiation was used for the measurement. A 1 / 2 degree anti-scattering slit and a 1 / 4 degree divergence slit were used. The diffraction intensity from the coated cutting tool was measured at an angle of about 2θ at which the relevant peaks occurred.

[0057] Data analysis including background subtraction and Cu-K α2 stripping was performed using PANalytical's X'Pert HighScore Plus software. The Pseudo-Voigt-Fit function was used for peak analysis. No thin film correction was performed on the obtained peak intensities. Any diffraction peaks not belonging to the PVD layer, for example, possible peak overlaps of (111) or (200) peaks having substrate reflections such as WC, were compensated by the software (deconvolution of overlapping peaks) during the determination of peak intensity and peak width. The XRD of the nanomultilayer of the present invention shows 200 crystal preferred orientations. Since there is no significant (111) peak, the intensity ratio I(200) / I(111) far exceeds 20. The full width at half maximum (FWHM) value of the (200) peak of the sample was calculated. The results are shown in Table 2. TIFF2025518128000003.tif40170

[0058] The FWHM value reflects both the grain size and the point defect density of the crystallites during coating in that the smaller the grain size and / or the larger the point defect density, the larger the FWHM value. In this case, the coating of the present invention has a very small FWHM value.

[0059] Example 3: To determine the performance of the fabricated samples, cutting tests were conducted.

[0060] Explanation of Terms Used The following expressions / terms are commonly used in metal cutting, but are explained in the table below nonetheless. Vc (m / min): Cutting speed in meters per minute fz (mm / tooth): Feed rate in millimeters per tooth (in milling) fn (mm / rev): Feed rate per revolution (in turning) z: (number) Number of teeth of the cutter a e (mm): Radial cutting depth in millimeters a p (mm): Axial cutting depth in millimeters

[0061] Crack Resistance Operation: Face Milling Tool Holder: R245-080027-12M, Dc = 80 mm Workpiece Material: Toolox33 (Tool Steel), L = 600 mm, I = 200 mm, h = 100 mm, Insert Type: R390-11 Cutting Speed V c = 320 m / min Feed Rate f z = 0.3 mm / rev z = 1 Cutting Depth a p = 2 mm Radial Engagement a e = 15 mm With Cutting Fluid

[0062] The criterion for the end of tool life is that the maximum chipping height VB > 0.3 mm.

[0063] Relief Face Wear Test Turning Operation Workpiece Material: Sverker21 (Tool Steel), hardness approximately 210 HB, D = 180, L = 700 mm, V c = 125 m / min f n = 0.072 mm / rev a p = 2 mm Without cutting fluid

[0064] The cut-off criterion for tool life is a flank wear VB of 0.15 mm.

[0065] Flaking resistance: Evaluation was carried out by a turning test on austenitic steel. To cause adhesive wear and flaking of the coating, the cutting depth a p was changed between 4 - 0 mm and 0 - 4 mm (once while facing in the radial direction). The insert was evaluated by SEM analysis.

[0066] Operation: Facing (turning) Workpiece material: Bar of austenitic stainless steel Sanmac 316L, L = 200 mm, D = 100 mm, approximately 215 HB Insert type: CNMG 120408 - MM Cooling: Yes Cutting depth a p = 4 - 0, 0 - 4 mm Cutting speed V c = 140 m / min Feed rate f z = 0.36 mm / rev

[0067] Edge toughness: Workpiece material: Unhardened Dievar, P3.0.Z.AN, z = 1 V c = 200 m / min f z = 0.20 mm a e = 12 mm a p = 3.0 Cutting length = 12 mm Without cutting fluid

[0068] The cutoff criteria are chipping of at least 0.5 mm on the cutting edge or a measurement depth of 0.2 mm in either the flank or rake face. To reach these criteria, the tool life is presented as the number of cutting entries.

[0069] The results of the cutting tests can be seen in Tables 3 - 5. TIFF2025518128000004.tif56170

[0070] Regarding crack resistance, the performance of Samples 1 - 4 is very good, with Sample 1 having the best performance, and the performance decreasing in the order of Sample 1 > Sample 2 > Sample 3 > Sample 4. Regarding flank wear resistance, Samples 1 and 2 have excellent performance, while Samples 3 and 4 have much inferior performance. TIFF2025518128000005.tif60170

[0071] Regarding flaking resistance, Samples 1 and 2 have excellent performance. However, for Sample 2, a difference can be seen between the peel tests performed at 100 m / min and 140 m / min. This peel test for stainless - steel machining at 100 m / min induces more smearing than when using 140 m / min, so it is the most stringent test. Samples 3 and 4, which contain (Ti,Al)N and (Ti,Al,Si)N nanomultilayers with a higher Al content in the (Ti,Al,Si)N nanolayer, have much inferior performance in the peel tests at both 100 m / min and 140 m / min. TIFF2025518128000006.tif33170

[0072] Regarding the toughness of the cutting edge, the samples according to the present invention have very good performance.

Claims

1. A coated cutting tool comprising a base material (5) and a coating (6), wherein the coating (6) is Ti １－ｘ Al ｘ N, a first nanolayer (9) where 0.55 < x ≤ 0.70, and Ti １－ｙ－ｚ Al ｙ Si ｚ A coated cutting tool (1) comprising a nanomultilayer (8) of alternating layers of second nanolayers (10) having N, 0.20 ≤ y ≤ 0.50, 0.13 ≤ z ≤ 0.25, and 0.46 ≤ y + z ≤ 0.65, wherein a series of one first nanolayer (9) and one second nanolayer (10) form a layer period, and the average layer period thickness of the nanomultilayer (8) is 20 nm or less.

2. Ti of the first nanolayer (9) １－ｘ Al ｘ The coated cutting tool (1) according to claim 1, wherein for N, 0.56 ≤ x ≤ 0.

63.

3. Ti of the second nano layer (10) １－ｙ－ｚ Al ｙ Si ｚ The coated cutting tool (1) according to claim 1, wherein for N, 0.25 ≦ y ≦ 0.45 and 0.13 ≦ z ≦ 0.

20.

4. Ti of the second nanolayer (10) １－ｙ－ｚ Al ｙ Si ｚ The coated cutting tool (1) according to claim 1, wherein for N, 0.46 ≤ y + z ≤ 0.

60.

5. Ti of the second nanolayer (10) １－ｙ－ｚ Al ｙ Si ｚ The coated cutting tool (1) according to claim 1, wherein for N, 0.33 ≤ y ≤ 0.40 and 0.14 ≤ z ≤ 0.

17.

6. Ti of the second nanolayer (10) １－ｙ－ｚ Al ｙ Si ｚ The coated cutting tool (1) according to claim 1, wherein for N, 0.47 ≤ y + z ≤ 0.

55.

7. The coated cutting tool (1) according to claim 1, wherein the average layer periodic thickness of the nanomultilayer (8) is 2 to 15 nm.

8. The coated cutting tool (1) according to claim 1, wherein the nanolayer (8) has a columnar microstructure.

9. A coated cutting tool (1) according to claim 1, wherein the FWHM value of the cubic (200) peak in X-ray diffraction is 0.4 to 1 degree (2 theta).

10. The coated cutting tool (1) according to claim 1, wherein the thickness of the nanolayer (8) is approximately 0.5 to approximately 15 μm.

11. The coated cutting tool (1) according to claim 1, wherein the coating (6) includes an innermost layer (7) of TiN, (Ti,Al)N, or (Cr,Al)N having a thickness of about 0.1 to about 3 μm, beneath a nanomultilayer (8) closest to the substrate.

12. The innermost layer (7) is Ti １－ｖ Al ｖ The coated cutting tool (1) according to claim 11, wherein N is and 0.35 ≤ v ≤ 0.

70.

13. The coated cutting tool (1) according to claim 1, wherein the nanomultilayer (8) is a cathode arc deposition layer.

14. The coated cutting tool (1) according to claim 1, wherein the base material (5) of the coated cutting tool (1) is selected from the group consisting of cemented carbide, cermet, ceramic, cubic boron nitride, and high-speed steel.

15. The coated cutting tool (1) according to claim 1, wherein the coated cutting tool (1) is a cutting tool insert, drill, or solid end mill for metal machining.

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