A high-temperature alloy cutting coating tool

Abstract

The present invention discloses a high-temperature alloy cutting coating tool and a preparation method thereof, comprising a tool substrate and a multi-layer coating deposited on the substrate, wherein the multi-layer coating sequentially comprises a transition layer, a periodic composite layer and a functional layer from the substrate side toward the surface side of the multi-layer coating, wherein the periodic composite layer has an alternating stacking structure consisting of a first composite layer and a second composite layer alternately repeated twice or more. The transition layer has the same chemical composition as the first composite layer and is composed of Ti a Al b Cr c The second composite layer has the same chemical composition as the functional layer and is composed of Ti d Al e Cr f M g L h The present invention provides a high-temperature alloy cutting coating tool with high wear resistance, crack resistance, high temperature resistance and oxidation resistance, high bonding strength between the coating and the substrate, simple production process and low production cost.

Description

Technical Field

[0001] The present invention relates to the technical field of a coating tool and a preparation method thereof, in particular to a high-temperature alloy cutting coating tool. Background Art

[0002] Since the 1960s, tool coatings have experienced rapid development. In terms of coating composition, a wide range of high-performance coatings, such as AlTiN, AlCrN, TiSiN, and TiCN, have been developed by adding elements such as Cr, Si, C, and O to traditional TiN and AlN coatings. In terms of coating structure, single-layer coatings have gradually evolved into complex structures such as double-layer coatings, multi-layer coatings, laminated composite coatings, and nanocomposite coatings. In line with recent advancements in coating processes, coating technology continues to innovate, coating systems are constantly being enriched, and coating performance is becoming increasingly powerful.

[0003] High-entropy alloys (HEAs) are a new type of high-performance alloy material, characterized by being composed of five or more principal elements. This multiplicity of principal elements results in a high mixing entropy, leading to a tendency for the material to form a simple solid solution or amorphous structure. Through strengthening mechanisms such as diffusion hysteresis, lattice distortion, and the cocktail effect, HEAs exhibit excellent properties such as fracture resistance, high-temperature resistance, and oxidation resistance.

[0004] High-entropy alloying of coatings is one of the latest methods to improve coating performance. By adding more refractory metal elements, rare earth elements, metalloid elements, and non-metallic elements, the high-temperature performance and mechanical properties of the coating can be further enhanced. Invention patent CN115341175A reports a rare-earth-doped high-entropy alloy coating. The patent describes a high-entropy alloy-like high-entropy coating characterized by a high-entropy alloy-based coating with a small amount of rare earth elements and non-metallic elements added. The coating has the advantages of being dense, strong, resistant to oxidation, and having strong film-base bonding. However, the high-entropy alloy coating described in the patent does not deviate from the scope of high-entropy alloys, and has low hardness and poor wear resistance, making it unsuitable for use as a tool coating. High-entropy nitride coatings are nitride coatings developed based on the strengthening principle of high-entropy alloys. Similar to high-entropy ceramics, although they have a high nitrogen content, they can still form multinary nitrides in the form of simple solid solutions and have strong high-temperature stability. Invention patent CN111902231A reports a surface-coated cutting tool, characterized in that the coating comprises an alternating stacked structural layer and a lower layer consisting of (Al, Ti, Cr, Si, Y) N layers and (Al, Ti) N layers. By adding a high-entropy alloy coating to the traditional laminated composite coating, the coating has excellent resistance to deposition, chipping, defect resistance and wear resistance. However, the overall hardness of the coating is relatively low, and it lacks wear-reducing properties. When used under conditions of processing high-hardness nickel-based alloys or low-speed cutting, problems such as severe adhesive wear and premature failure will occur. Patent invention CN108823526A reports a nano-multilayer composite superhard tool coating, characterized in that the coating comprises a CrN / TiAlSiYN composite layer with an alternating stacked structure. The coating refines the grains, delays diffusion, and further improves the strength, hardness, toughness and oxidation resistance of the coating by adding Si and Y elements to TiAlN. However, although the coating has a relatively complex chemical composition, it still does not meet the strengthening requirements of high-entropy alloys, and the coating performance needs to be further improved.

[0005] High-temperature alloys possess characteristics such as high strength and hardness at both high temperatures and room temperature, significant work hardening, low thermal conductivity, and a high coefficient of friction. This results in high cutting resistance, high cutting temperatures, and high wear rates when machining high-temperature alloys. Prolonged exposure to high temperatures not only causes oxidation of the coating but also accelerates its degradation, decomposition, and failure. Furthermore, the softening of chips caused by high temperatures can leave chip nodules on the coating surface, increasing cutting forces and exacerbating adhesive wear of the coating. Therefore, developing a coating suitable for high-temperature alloy cutting has become a difficult problem that those skilled in the art urgently need to solve. Summary of the Invention

[0006] The technical problem to be solved by the present invention is to overcome the shortcomings of the existing technology and provide a high-temperature alloy cutting coating tool, which can produce a high-temperature alloy cutting coating with high wear resistance, crack resistance, high temperature resistance and oxidation resistance through a simple process, conventional equipment and low production cost. To solve the above problems, the present invention provides the following technical solutions:

[0007] A high-temperature alloy cutting coating tool comprises a tool substrate and a multilayer coating deposited on the tool substrate. The multilayer coating is composed of a transition layer, a periodic composite layer and a functional layer deposited in sequence on the tool substrate. The periodic composite layer has an alternating stacking structure in which a first composite layer and a second composite layer are alternately repeated more than twice.

[0008] Preferably, the transition layer has the same chemical composition as the first composite layer and is composed of the compound Ti a Al b Cr c N composition, and satisfies 0.15≤a≤0.40, 0.15≤b≤0.40, 0.15≤c≤0.40, and a+b+c=1. Wherein, a represents the atomic ratio of the Ti element in the compound relative to all elements in the compound except the N element; b represents the atomic ratio of the Al element in the compound relative to all elements in the compound except the N element; and c represents the atomic ratio of the Cr element in the compound relative to all elements in the compound except the N element.

[0009] Preferably, the second composite layer has the same chemical composition as the functional layer and is composed of the compound Ti d Al e Cr f M g L hN, L represents an element set consisting of at least one element selected from C, B and Si, M represents an element set consisting of at least one element selected from Zr, V, Mo, Nb, Ta, W, Hf, Ce, Sc, Y and La, and satisfies 0.15≤d≤0.35, 0.15≤e≤0.35, 0.15≤f≤0.35, 0.10≤g≤0.15, 0.10≤h≤0.25, d+e+f+g+h=1. Wherein, d represents the atomic ratio of Ti element in the compound relative to all elements except N element in the compound; e represents the atomic ratio of Al element in the compound relative to all elements except N element in the compound; f represents the atomic ratio of Cr element in the compound relative to all elements except N element in the compound; g represents the atomic ratio of all elements in the M element set relative to all elements except N element in the compound; h represents the atomic ratio of all elements in the L element set relative to all elements except N element in the compound. Because, if d≤0.15 and / or e≤0.15 and / or f≤0.15 and / or g≤0.10 and / or h≤0.10, the high temperature resistance and oxidation resistance of the coating will be affected; if g≥0.15, the wear resistance of the coating will be affected; if h≥0.25, the coating preparation process and cost will be affected. According to the inventor's experiments, the compound Ti d Al e Cr f M g L h When the atomic proportion of each element in N relative to all elements except N is 5% to 35%, the second composite layer and the functional layer will produce a strengthening effect similar to that in high-entropy alloys, that is, the coating is composed of a simple solid solution with a face-centered cubic structure and has severe lattice distortion. At this time, the diffusion of elements in the second composite layer and the functional layer is blocked, and even after high-temperature annealing at 900°C, the coating still does not undergo obvious phase decomposition. According to the inventor's experiments, adding an appropriate amount of L element aggregate elements to the coating can not only produce solid solution strengthening to improve the strength and hardness of the coating, but also promote the formation of nano / amorphous impurity points at the grain boundaries, further blocking diffusion and hindering grain boundary movement.

[0010] Preferably, the compound Ti a Al b Cr c N and the compound Ti d Al e Cr f M g L hThe elemental composition of N satisfies 0.05≤|ad|≤0.20, 0.05≤|be|≤0.20, and 0.05≤|cf|≤0.20. According to the inventors' experiments, when the main elements of the alternating first and second composite layers in the periodic composite layer, namely the three elements Ti, Al, and Cr, have a composition difference of 5% to 20% between the two adjacent layers, the coating has higher hardness and strength. This is because, in a nano-multilayer composite coating, when adjacent layers have a certain composition difference, the coating easily forms two layer interfaces with similar crystal structures, crystal sizes, and thermal expansion coefficients, but different elastic moduli. In this case, the nano-composite coating has a periodic alternating stress field, which hinders interlayer diffusion and positional movement, and enhances the hardness and strength of the coating.

[0011] Preferably, the atomic ratio of nitrogen relative to all elements in the multilayer coating (hereinafter referred to as "N content") is 45% to 55%. This is because if the N content in the coating is less than 45%, the wear resistance of the coating will be affected; if the N content in the coating is greater than 55%, the crack resistance and high-temperature resistance of the coating will be affected. According to the inventor's experiments, when the N content in the multilayer coating is 45% to 55%, the hardness value of the coating is at a relatively high level; when the N content is too low, metallic amorphous structure is easily formed in the coating, seriously affecting the mechanical properties of the coating; when the N content is too high, high-N compounds with poor chemical stability are easily formed in the coating, seriously affecting the high-temperature stability of the coating.

[0012] Preferably, the thickness of the periodic composite layer accounts for 50% to 80% of the total coating thickness, more preferably 60% to 75%, and the thickness of the functional layer accounts for 10% to 30% of the total coating thickness, more preferably 15% to 25%. This is because if the periodic composite layer is too thin, the coating's resistance to chipping will be affected; and if the functional layer is too thin, the coating's wear resistance will be affected. According to the inventor's experiments, by adjusting the layer thickness ratio of each layer in the periodic composite coating, not only can the magnitude of the residual stress in the coating be regulated, but the wear resistance and chipping resistance of the coating can also be balanced, resulting in the coating having the best overall performance.

[0013] Preferably, the average thickness of the alternating first and second composite layers in the periodic composite layer is 2nm to 30nm, more preferably 5nm. This is because if the average thickness of the alternating first and second composite layers in the periodic composite layer is greater than 30nm, the wear resistance of the coating will be affected; when the average thickness of the alternating first and second composite layers is less than 2nm, the wear resistance and crack resistance of the coating will also be affected. According to the inventor's experiments, when the average thickness of the alternating first and second composite layers in the periodic composite layer is 2nm to 30nm, the interface between the adjacent layers in the periodic composite layer is complete and clear, and "superlattice" strengthening can be generated, which increases the hardness of the coating while also suppressing the interlayer propagation of cracks.

[0014] Preferably, the multi-layer coating has an average overall thickness of 1 μm to 8 μm, more preferably 3 μm. If the overall thickness of the multi-layer coating is too small, the coating's protective performance for the tool will be weak, affecting the coating's wear resistance; while if the overall thickness is too large, stress cracking of the coating will occur, affecting the coating's resistance to chipping.

[0015] Preferably, a bonding layer is provided between the tool substrate and the multilayer coating. The bonding layer is composed of a compound composed of at least one element selected from the group consisting of Al, Cr, Ti, V, Zr, Nb, Ta, Mo, W, B, C, Si, N, and O. The average thickness of the bonding layer is 10 nm to 50 nm, more preferably 20 nm to 30 nm. Experiments conducted by the inventors have shown that providing a bonding layer with low hardness and good plasticity between the tool substrate and the multilayer coating not only reduces the stress mismatch between the coating and the substrate, but also improves the bonding strength between the coating and the substrate.

[0016] Preferably, in the nanoindentation analysis of the multilayer coating, 28Gpa≤H≤40Gpa, 270Gpa≤E≤340Gpa, and 0.50≤H 3 / E 2 ≤0.70, where H is the hardness of the multilayer and E is the elastic modulus of the multilayer coating. 3 / E 2 When ≤0.50, the wear resistance of the coating will be affected; 3 / E 2 When the value is ≥0.70, the crack resistance of the coating will be affected. According to the inventor's experiments and relevant literature, the hardness and elastic modulus can be calculated by the formula H 3 / E 2A coefficient can be obtained, which is also called the "Plastic Deformation Resistance Factor". The Plastic Deformation Resistance Factor can roughly measure the wear resistance of the coating. A larger value means that the coating is more likely to undergo elastic deformation when subjected to load, and the coating is less likely to crack. A smaller value means that the elastic deformation of the coating is suppressed when subjected to load, and it is more likely to crack. However, the hardness is often higher at this time, so the wear resistance of the coating is better. Based on the above reasons, further optimization is made, 0.55≤H 3 / E 2 ≤0.65.

[0017] In each of the above technical solutions, the thickness of each layer of the multilayer coating and the bonding layer can be measured directly from a cross-section of the coated tool using an optical microscope (OM), scanning electron microscope (SEM), transmission electron microscope (TEM), or indirectly measured and calculated using the ball milling pit method (referring to international standard ISO 26423:2009). The chemical composition of each layer of the multilayer coating can be analyzed and detected from a cross-section of the coated tool using a detection device such as an energy dispersive X-ray spectrometer (EDS) or a wavelength dispersive X-ray spectrometer (WDS). The crystal structure of each layer of the multilayer coating can be determined from the surface of the coated tool using an X-ray diffractometer (XRD). The hardness, elastic modulus, and plastic deformation resistance of the multilayer coating can be measured and calculated from the coating surface using a nanoindenter. The specific testing methods and standards for the above coating properties refer to international standard ISO 21874:2019.

[0018] As a general technical concept, the present invention also provides a method for preparing a high-temperature alloy cutting coating tool, comprising the following preparation steps:

[0019] (1) Pretreatment of the tool base;

[0020] (2) selectively depositing a bonding layer on the surface of the tool substrate;

[0021] (3) A multi-target alternating deposition method using a physical vapor deposition process is used to deposit a transition layer using a TiAlCr target, a periodic composite layer having an alternating stacking structure using a TiAlCr target and a TiAlCrLM target, and a functional layer using a TiAlCrLM target, thereby obtaining the high-temperature alloy cutting coating tool.

[0022] The deposition process described in the above preparation steps is not particularly limited and may be any physical vapor deposition process known to those skilled in the art, such as ion plating, sputtering, and plasma plating. Preferably, the multi-layer coating is prepared using an ion plating process, as it offers advantages such as high deposition efficiency, good film-substrate bonding, and low deposition temperature. Furthermore, preferably, the multi-layer coating is prepared using a multi-arc ion plating process.

[0023] In the above technical solutions, the tool substrate can be various cutting tools known to those skilled in the art, and is suitable for cemented carbide tools, metal ceramic tools or high-speed steel tools, and is particularly suitable for cemented carbide tools.

[0024] Beneficial effects

[0025] Compared with the prior art, the present invention has the following beneficial effects:

[0026] The present invention is based on the high entropy alloy strengthening theory, further improves on the basis of the traditional TiAlCrN coating, adds at least two strengthening elements, and forms a multi-component high entropy nitride coating with a complex component system. d Al e Cr f M g L h N is a simple solid solution under the face-centered cubic structure, which has a strong diffusion hysteresis effect, making the functional layer and the periodic composite layer have good high temperature resistance and oxidation resistance. The periodic composite layer is composed of a compound containing Ti a Al b Cr c The first composite layer of N and the compound Ti d Al e Cr f M g L h The second composite layer of N is alternately stacked, and there is a certain difference in composition and modulus between the two adjacent layers. It can produce "superlattice" reinforcement through coherent epitaxial growth, thereby improving the crack resistance and impact resistance of the periodic composite layer. By providing a bonding layer with good toughness and low hardness between the tool substrate and the multi-layer coating, it is ensured that the coating has a high bonding strength. The present invention also provides a preparation method for high-temperature alloy cutting coated tools, which has a simple process, conventional equipment, and low production cost. The coated tool prepared by the method of the present invention has a wide range of applications, high processing efficiency, and long tool life. It can meet the high-temperature alloy cutting processing under various conditions, and is particularly suitable for high-temperature alloy cutting processing under various conditions. BRIEF DESCRIPTION OF THE DRAWINGS

[0027] In order to more clearly illustrate the technical solutions of the embodiments of the present invention, the following briefly introduces the drawings required for describing the embodiments. Obviously, the drawings described below are only some embodiments of the present invention. For ordinary technicians in this field, other drawings can be obtained based on these drawings without creative work.

[0028] Figure 1 Schematic diagram of the structure of the multilayer coating in Example 1 of the present invention;

[0029] Figure 2 This is a schematic diagram of the internal structure of the tool base of the present invention.

[0030] In the accompanying drawings, the components represented by the reference numerals are as follows:

[0031] 1. Tool substrate; 2. Adhesive layer; 3. Multilayer coating; 4. Transition layer; 5. Periodic composite layer; 5a. First composite layer; 5b. Second composite layer; 6. Functional layer. DETAILED DESCRIPTION

[0032] The present invention will be further described below with reference to the accompanying drawings and specific embodiments.

[0033] This specific example is merely an explanation of the present invention and is not intended to limit the present invention. After reading this specification, those skilled in the art may make modifications to this example as needed that do not contribute to creativity. However, as long as they fall within the scope of the claims of the present invention, they are protected by patent law. Unless otherwise specified, the drugs used in the following examples can be purchased from regular channels.

[0034] Example 1:

[0035] A high temperature alloy cutting coating tool and a preparation method thereof according to the present invention, Figure 1-2 As shown, it includes a tool substrate 1 and a multilayer coating 3 deposited on the tool substrate 1. The multilayer coating 3 includes a transition layer 4 deposited on the tool substrate 1, a periodic composite layer 5 deposited on the transition layer 4, and a functional layer 6 deposited on the periodic composite layer 5. In addition, a bonding layer 2 is selectively deposited between the tool substrate 1 and the multilayer coating 3. By adjusting the target material composition and deposition parameters, the bonding layer 2 is specifically a TiAlCr metal compound layer; the transition layer 4 is specifically Ti0.30Al0.60Cr0.10N with an average thickness of 0.5μm; the periodic composite layer 5 is specifically Ti 0.15 Al 0.40 Cr 0.20 Ta 0.15 Si 0.10 N / Ti0.30Al0.60Cr0.10N, this layer is Ti 0.15 Al 0.40 Cr0.20 Ta 0.15 Si 0.10 The periodic composite layer obtained by alternating deposition of N layer and Ti0.30Al0.60Cr0.10N layer is specifically 200 cycles with an average thickness of 2.0 μm. The average thickness of the Ti0.30Al0.60Cr0.10N first composite layer 5a is 4.0 nm. 0.15 Al 0.40 Cr 0.20 Ta 0.15 Si 0.10 The average thickness of the second composite layer 5b is 6.0 nm; the functional layer 6 is specifically Ti 0.15 Al 0.40 Cr 0.20 Ta 0.15 Si 0.10 N, with an average thickness of 0.5 μm. In this embodiment, the multilayer coating 3 has an overall average thickness of 3.0 μm, a hardness of 36.8 GPa, an elastic modulus of 301.5 GPa, and H 3 / E 2 is 0.55.

[0036] A method for preparing a high-temperature alloy cutting coating tool according to the present invention comprises the following steps:

[0037] (1) Matrix cleaning: Ultrasonic cleaning of the tool to remove surface oil and impurities, and drying for later use;

[0038] (2) Ion etching: Place the tool in a vacuum coating furnace and slowly evacuate to 1×10 -5 After mba, appropriate argon gas was introduced into the vacuum furnace chamber to maintain the pressure in the chamber at 2×10 -3 mba, when the vacuum coating furnace is heated to the furnace chamber temperature of 500℃, a negative bias voltage of -200V is applied to the tool, and the tool is accelerated by Ar + The tool surface is subjected to ion bombardment for 30 minutes to improve the bonding strength between the coating and the substrate, thereby forming a coated tool substrate 1;

[0039] (3) Deposition of bonding layer: Add appropriate amount of argon gas into the vacuum furnace chamber to maintain the pressure in the chamber at 0.8×10 - 2 mba, a current of 180A is passed through the TiAlCr target and a bias voltage of -80V is applied to the tool to deposit a TiAlCr bonding layer 2 on the surface of the tool substrate 1 for 2 minutes;

[0040] (4) Deposition of transition layer: 200 sccm to 300 sccm nitrogen is introduced into the vacuum furnace chamber to maintain the pressure in the chamber at 3.2×10 -2mba, a current of 180A is passed through the TiAlCr target and a bias voltage of -80V is applied to the tool to deposit a Ti0.30Al0.60Cr0.10N transition layer 4 on the surface of the TiAlCr bonding layer 2 for 10 minutes;

[0041] (5) Deposition of the composite layer: 500 sccm to 600 sccm of nitrogen was introduced into the vacuum furnace chamber to maintain the pressure in the chamber at 3.2×10 -2 mba, 180A current is passed to the TiAlCr target, 160A current is passed to the TiAlCrLM target, and a -80V bias voltage is applied to the tool. Ti with an alternating stacking structure is deposited on the surface of the Ti0.30Al0.60Cr0.10N transition layer 4. 0.15 Al 0.40 Cr 0.20 Ta 0.15 Si 0.10 N / Ti0.30Al0.60Cr0.10N periodic composite layer 5, the disk speed is set to 3.5rpm, so that the Ti0.30Al0.60Cr0.10N first composite layer 5a and Ti 0.15 Al 0.40 Cr 0.20 Ta 0.15 Si 0.10 N second composite layer 5b is alternately deposited in sequence, with a deposition time of 30 minutes;

[0042] In order to form the Ti0.30Al0.60Cr0.10N first composite layer 5a and Ti 0.15 Al 0.40 Cr 0.20 Ta 0.15 Si 0.10 The second composite layer 5b of N is repeated twice or more in an alternating stacking structure. A transmission method with three-order rotation around the axis is used to make the tool rotate and revolve simultaneously in the furnace chamber, and two or more targets are symmetrically placed in the furnace chamber, so that Ti with an alternating stacking structure is deposited on the surface of the Ti0.30Al0.60Cr0.10N transition layer 4. 0.15 Al 0.40 Cr 0.20 Ta 0.15 Si 0.10 N / Ti0.30Al0.60Cr0.10N periodic composite layer 5. By adjusting the rotation rate of the rotating structure, the alternating stacked Ti0.30Al0.60Cr0.10N first composite layer 5a and Ti 0.15 Al 0.40 Cr 0.20 Ta 0.15 Si 0.10The average thickness of each single layer of the second composite layer 5b is adjusted. More specifically, if the rotation speed of the rotating structure is faster, the average thickness of each single layer decreases, and vice versa.

[0043] (6) Deposition of coating functional layer: 400 sccm to 500 sccm nitrogen is introduced into the vacuum furnace chamber to maintain the pressure in the chamber at 3.2×10 -2 mba, a 160A current was fed into the TiAlCrLM target, and a -80V bias was applied to the tool to deposit Ti on the surface of the periodic composite layer 5. 0.15 Al 0.40 Cr 0.20 Ta 0.15 Si 0.10 N functional layer 6, deposition time 10 minutes.

[0044] In this embodiment, a multi-arc ion plating process employs alternating deposition of multiple targets, depositing a bonding layer using a TiAlCrLM target, a transition layer using a TiAlCr target, a periodic composite layer with an alternating stacking structure using a TiAlCr target and a TiAlCrLM target, and finally a functional layer using a TiAlCrLM target to produce the high-temperature alloy cutting coating tool. Unless otherwise specified, the following other embodiments share the same preparation steps as this embodiment.

[0045] In this embodiment, the tool base 1 adopts a four-edge ball-end carbide milling cutter, and the milling cutter structure and material parameters are as follows:

[0046] Ball head rake angle: 0°;

[0047] Ball head back angle: 16°;

[0048] Helix angle: 17°;

[0049] Blade diameter: 6mm;

[0050] Handle diameter: 8mm;

[0051] Tool material: Cobalt content 9%, hardness 93HRA, particle size 0.2~0.4.

[0052] The tool substrate of the control product is the same as that of Example 1. A multi-arc ion plating process is used to deposit a common AlTiN coating on the market. The coating has a single-layer structure and a thickness of 3.0 μm.

[0053] Unless otherwise specified, the tool base structure and material parameters, as well as the reference coated tools used in the following other embodiments are the same as those in this embodiment.

[0054] The coated tools prepared in Example 1 and the control product were used to perform milling experiments on a high-temperature alloy (GH4169). When the maximum wear width of the tool flank was ≥0.3 mm, the tool was considered to have failed, and the accumulated machining time was recorded as the tool life. The comparative experimental results are shown in Table 1 below:

[0055] Table 1: Comparative experimental results of Example 1 of the present invention and the reference product

[0056]

[0057] As shown in Table 1, under the same tool structure and cutting conditions, the multi-layer coated tool of the present invention has an 88% longer service life when milling high-temperature alloys than the AlTiN coated tool of the prior art. This shows that the coating technology of this embodiment has a significant performance improvement over the prior art.

[0058] Example 2:

[0059] A high temperature alloy cutting coating tool and a preparation method thereof according to the present invention, Figure 1 As shown, it includes a tool substrate 1 and a multilayer coating 3 deposited on the tool substrate 1. The multilayer coating 3 includes a transition layer 4 deposited on the tool substrate 1, a periodic composite layer 5 deposited on the transition layer 4, and a functional layer 6 deposited on the periodic composite layer 5. In addition, a bonding layer 2 is selectively deposited between the substrate 1 and the multilayer coating 3. By adjusting the target material composition and deposition parameters, the bonding layer 2 is specifically a TiAlCr metal compound layer; the transition layer 4 is specifically Ti0.30Al0.60Cr0.10N with an average thickness of 0.5μm; the periodic composite layer 5 is specifically Ti 0.15 Al 0.40 Cr 0.20 Ta 0.15 Si 0.10 N / Ti0.30Al0.60Cr0.10N, this layer is Ti 0.15 Al 0.40 Cr 0.20 Ta 0.15 Si 0.10 The periodic composite layer obtained by alternating deposition of N layer and Ti0.30Al0.60Cr0.10N layer is specifically 400 cycles with an average thickness of 2.0 μm. The average thickness of the Ti0.30Al0.60Cr0.10N first composite layer 5a is 2.0 nm. 0.15 Al 0.40 Cr 0.20 Ta 0.15 Si 0.10 The average thickness of the second composite layer 5b is 3.0 nm; the functional layer 6 is specifically Ti 0.15 Al 0.40 Cr0.20 Ta 0.15 Si 0.10 N, with an average thickness of 0.5 μm. In this embodiment, the multilayer coating 3 has an overall average thickness of 3.0 μm, a hardness of 37.2 GPa, an elastic modulus of 300.6 GPa, and H 3 / E 2 It is 0.57.

[0060] The coated tools prepared in Example 2 and the control were used to perform milling experiments on a high-temperature alloy (GH4169). When the maximum wear width of the tool flank was ≥0.3 mm, the tool was considered to have failed, and the accumulated machining time was recorded as the tool life. The comparative experimental results are shown in Table 2 below:

[0061] Table 2: Comparative experimental results of Example 2 of the present invention and the reference product

[0062]

[0063] As shown in Table 2, under identical tool structure and cutting conditions, the multilayer coated tool of the present invention has a 112% longer service life when milling high-temperature alloys than the conventional AlTiN-coated tool. Compared to Example 1, this example reduces the average thickness of the alternating first and second composite layers in the periodic composite layer by 33%, resulting in a significant improvement in performance compared to Example 1.

[0064] Example 3:

[0065] A high temperature alloy cutting coating tool and a preparation method thereof according to the present invention, Figure 1 As shown, it includes a tool substrate 1 and a multilayer coating 3 deposited on the tool substrate 1. The multilayer coating 3 includes a transition layer 4 deposited on the tool substrate 1, a periodic composite layer 5 deposited on the transition layer 4, and a functional layer 6 deposited on the periodic composite layer 5. In addition, a bonding layer 2 is selectively deposited between the substrate 1 and the multilayer coating 3. By adjusting the target material composition and deposition parameters, the bonding layer 2 is specifically a TiAlCr metal compound layer; the transition layer 4 is specifically Ti0.30Al0.60Cr0.10N with an average thickness of 0.2μm; the periodic composite layer 5 is specifically Ti 0.15 Al 0.40 Cr 0.20 Ta 0.15 Si 0.10 N / Ti0.30Al0.60Cr0.10N, this layer is Ti 0.15 Al 0.40 Cr 0.20 Ta 0.15 Si 0.10The periodic composite layer obtained by alternating deposition of N layer and Ti0.30Al0.60Cr0.10N layer is specifically 100 cycles with an average thickness of 1.0 μm. The average thickness of the Ti0.30Al0.60Cr0.10N first composite layer 5a is 4.0 nm. 0.15 Al 0.40 Cr 0.20 Ta 0.15 Si 0.10 The average thickness of the second composite layer 5b is 6.0 nm; the functional layer 6 is specifically Ti 0.15 Al 0.40 Cr 0.20 Ta 0.15 Si 0.10 N functional layer, with an average thickness of 0.3 μm. In this embodiment, the multilayer coating 3 has an average thickness of 1.5 μm, a hardness of 36.0 GPa, an elastic modulus of 295.7 GPa, and a 3 / E 2 It is 0.53.

[0066] The coated tools prepared in Example 3 and the control product were used to perform milling experiments on a high-temperature alloy (GH4169). When the maximum wear width of the tool flank was ≥0.3 mm, the tool was considered to have failed, and the accumulated machining time was recorded as the tool life. The comparative experimental results are shown in Table 3 below:

[0067] Table 3: Comparative experimental results of Example 3 of the present invention and the reference product

[0068]

[0069] As shown in Table 3, under identical tool structure and cutting conditions, the multilayer coated tool of the present invention exhibits a 41% longer service life when milling high-temperature alloys than the conventional AlTiN-coated tool. Compared to Example 1, this example reduces the overall thickness of the multilayer coating by 50%, but the technical performance is significantly lower than that of Example 1.

[0070] Example 4:

[0071] A high temperature alloy cutting coating tool and a preparation method thereof according to the present invention, Figure 1As shown, it includes a tool substrate 1 and a multilayer coating 3 deposited on the tool substrate 1. The multilayer coating 3 includes a transition layer 4 deposited on the tool substrate 1, a periodic composite layer 5 deposited on the transition layer 4, and a functional layer 6 deposited on the periodic composite layer 5. In addition, a bonding layer 2 is selectively deposited between the substrate 1 and the multilayer coating 3. By adjusting the target material composition and deposition parameters, the bonding layer 2 is specifically a TiAlCr metal compound layer; the transition layer 4 is specifically Ti0.30Al0.60Cr0.10N with an average thickness of 1.0μm; the periodic composite layer 5 is specifically Ti 0.15 Al 0.40 Cr 0.20 Ta 0.15 Si 0.10 N / Ti0.30Al0.60Cr0.10N, this layer is Ti 0.15 Al 0.40 Cr 0.20 Ta 0.15 Si 0.10 The periodic composite layer obtained by alternating deposition of N layer and Ti0.30Al0.60Cr0.10N layer is specifically 500 cycles with an average thickness of 5.0 μm. The average thickness of the Ti0.30Al0.60Cr0.10N first composite layer 5a is 4.0 nm. 0.15 Al 0.40 Cr 0.20 Ta 0.15 Si 0.10 The average thickness of the second composite layer 5b is 6.0 nm; the functional layer 6 is specifically Ti 0.15 Al 0.40 Cr 0.20 Ta 0.15 Si 0.10 N, with an average thickness of 1.5 μm. In this embodiment, the multilayer coating 3 has an average thickness of 7.5 μm, a hardness of 37.1 GPa, an elastic modulus of 305.2 GPa, and H 3 / E 2 is 0.55.

[0072] The coated tools prepared in Example 4 and the control were used to perform milling experiments on a high-temperature alloy (GH4169). When the maximum wear width of the tool flank was ≥0.3 mm, the tool was considered to have failed, and the accumulated machining time was recorded as the tool life. The comparative experimental results are shown in Table 4 below:

[0073] Table 4: Comparative experimental results of Example 4 of the present invention and the reference product

[0074]

[0075] As shown in Table 4, under identical tool structure and cutting conditions, the multilayer coated tool of the present invention exhibits a 38% longer service life when milling high-temperature alloys than the conventional AlTiN-coated tool. Compared to Example 1, this example increases the overall thickness of the multilayer coating by 150%, but the technical performance is significantly lower than that of Example 1.

[0076] Embodiment 5:

[0077] A high temperature alloy cutting coating tool and a preparation method thereof according to the present invention, Figure 1 As shown, it includes a tool substrate 1 and a multilayer coating 3 deposited on the tool substrate 1. The multilayer coating 3 includes a transition layer 4 deposited on the tool substrate 1, a periodic composite layer 5 deposited on the transition layer 4, and a functional layer 6 deposited on the periodic composite layer 5. In addition, a bonding layer 2 is selectively deposited between the substrate 1 and the multilayer coating 3. By adjusting the target material composition and deposition parameters, the bonding layer 2 is specifically a TiAlCr metal compound layer; the transition layer 4 is specifically Ti0.30Al0.60Cr0.10N with an average thickness of 0.5μm; the periodic composite layer 5 is specifically Ti 0.15 Al 0.40 Cr 0.20 Ta 0.15 Si 0.10 N / Ti0.30Al0.60Cr0.10N, this layer is Ti 0.15 Al 0.40 Cr 0.20 Ta 0.15 Si 0.10 The periodic composite layer obtained by alternating deposition of N layer and Ti0.30Al0.60Cr0.10N layer is specifically 200 cycles with an average thickness of 2.0 μm. The average thickness of the Ti0.30Al0.60Cr0.10N first composite layer 5a is 4.0 nm. 0.15 Al 0.40 Cr 0.20 Ta 0.15 Si 0.10 The average thickness of the second composite layer 5b is 6.0 nm; the functional layer 6 is specifically Ti 0.15 Al 0.40 Cr 0.20 Ta 0.15 Si 0.10 N, with an average thickness of 0.5 μm. In this embodiment, the multilayer coating 3 has an average thickness of 3.0 μm, a hardness of 34.2 GPa, an elastic modulus of 281.4 GPa, and H 3 / E 2 is 0.51.

[0078] The coated tools prepared in Example 5 and the control were used to perform milling experiments on a high-temperature alloy (GH4169). When the maximum wear width of the tool flank was ≥0.3 mm, the tool was considered to have failed, and the accumulated machining time was recorded as the tool life. The comparative experimental results are shown in Table 5 below:

[0079] Table 5: Comparative experimental results of Example 5 of the present invention and the reference product

[0080]

[0081] Table 5 shows that, under identical tool structure and cutting conditions, the multilayer coated tool of the present invention offers a 73% longer service life when milling high-temperature alloys than the conventional AlTiN-coated tool. Compared to Example 1, the M element set in this embodiment is modified from Ta (15%) in Example 1 to Zr (15%), resulting in a slight decrease in performance compared to Example 1.

[0082] Example 6:

[0083] A high temperature alloy cutting coating tool and a preparation method thereof according to the present invention, Figure 1 As shown, it includes a tool substrate 1 and a multilayer coating 3 deposited on the tool substrate 1. The multilayer coating 3 includes a transition layer 4 deposited on the tool substrate 1, a periodic composite layer 5 deposited on the transition layer 4, and a functional layer 6 deposited on the periodic composite layer 5. In addition, a bonding layer 2 is selectively deposited between the substrate 1 and the multilayer coating 3. By adjusting the target material composition and deposition parameters, the bonding layer 2 is specifically a TiAlCr metal compound layer; the transition layer 4 is specifically Ti0.30Al0.60Cr0.10N with an average thickness of 0.5μm; the periodic composite layer 5 is specifically Ti 0.15 Al 0.40 Cr 0.15 Ta 0.10 Si 0.10 B 0.10 N / Ti0.30Al0.60Cr0.10N, this layer is Ti 0.15 Al 0.40 Cr 0.15 Ta 0.10 Si 0.10 B 0.10 The periodic composite layer obtained by alternating deposition of N layer and Ti0.30Al0.60Cr0.10N layer is specifically 200 cycles with an average thickness of 2.0 μm. The average thickness of the Ti0.30Al0.60Cr0.10N first composite layer 5a is 4.0 nm. 0.15 Al 0.40 Cr 0.15 Ta 0.10 Si0.10 B 0.10 The average thickness of the second composite layer 5b is 6.0 nm; the functional layer 6 is specifically Ti 0.15 Al 0.40 Cr 0.15 Ta 0.10 Si 0.10 B 0.10 N, with an average thickness of 0.5 μm. In this embodiment, the multilayer coating 3 has an overall average thickness of 3.0 μm, a hardness of 39.5 GPa, an elastic modulus of 315.7 GPa, and H 3 / E 2 It is 0.62.

[0084] The coated tools prepared in Example 6 and the control were used to perform milling experiments on a high-temperature alloy (GH4169). When the maximum wear width of the tool flank was ≥0.3 mm, the tool was considered to have failed, and the accumulated machining time was recorded as the tool life. The comparative experimental results are shown in Table 6 below:

[0085] Table 6: Comparative experimental results of Example 6 of the present invention and the reference product

[0086]

[0087] As shown in Table 6, under the same tool structure and cutting conditions, the multilayer coated tool of the present invention has a 139% longer service life when milling high-temperature alloys than the AlTiN coated tool of the prior art. Compared with Example 1, the elements selected in the L element set of this embodiment are changed from Si (10%) in Example 1 to B (10%) + Si (10%), and the elements selected in the M element set are changed from Ta (15%) in Example 1 to Ta (10%). This technical effect significantly improves performance compared to Example 1.

[0088] Embodiment seven:

[0089] A high temperature alloy cutting coating tool and a preparation method thereof according to the present invention, Figure 1 As shown, it includes a tool substrate 1 and a multilayer coating 3 deposited on the tool substrate 1. The multilayer coating 3 includes a transition layer 4 deposited on the tool substrate 1, a periodic composite layer 5 deposited on the transition layer 4, and a functional layer 6 deposited on the periodic composite layer 5. In addition, a bonding layer 2 is selectively deposited between the substrate 1 and the multilayer coating 3. By adjusting the target material composition and deposition parameters, the bonding layer 2 is specifically a TiAlCr metal compound layer; the transition layer 4 is specifically Ti0.30Al0.60Cr0.10N with an average thickness of 0.5μm; the periodic composite layer 5 is specifically Ti 0.15 Al 0.40 Cr 0.15 V 0.10 Ta0.10 B 0.10 N / Ti0.30Al0.60Cr0.10N, this layer is Ti 0.15 Al 0.40 Cr 0.15 V 0.10 Ta 0.10 B 0.10 The periodic composite layer obtained by alternating deposition of N layer and Ti0.30Al0.60Cr0.10N layer is specifically 200 cycles with an average thickness of 2.0 μm. The average thickness of the Ti0.30Al0.60Cr0.10N first composite layer 5a is 4.0 nm. 0.15 Al 0.40 Cr 0.15 V 0.10 Ta 0.10 B 0.10 The average thickness of the second composite layer 5b is 6.0 nm; the functional layer 6 is specifically Ti 0.15 Al 0.4 0Cr 0.15 V 0.10 Ta 0.10 B 0.10 N, with an average thickness of 0.5 μm. In this embodiment, the multilayer coating 3 has an overall average thickness of 3.0 μm, a hardness of 37.6 GPa, an elastic modulus of 305.0 GPa, and H 3 / E 2 It is 0.57.

[0090] The coated tools prepared in Example 7 and the control were used to perform milling experiments on a high-temperature alloy (GH4169). When the maximum wear width of the tool flank was ≥0.3 mm, the tool was considered to have failed, and the accumulated machining time was recorded as the tool life. The comparative experimental results are shown in Table 7 below:

[0091] Table 7: Comparative experimental results of Example 7 of the present invention and the reference product

[0092]

[0093] As shown in Table 7, under the same tool structure and cutting conditions, the multilayer coated tool of the present invention has a 123% longer service life when milling high-temperature alloys than the AlTiN coated tool of the prior art. Compared with Example 1, the elements selected in the L element set of this embodiment are changed from Si (10%) in Example 1 to B (10%), and the elements selected in the M element set are changed from Ta (15%) in Example 1 to V (10%) + Ta (10%). The technical effect is significantly improved compared to Example 1.

[0094] Embodiment 8:

[0095] A high temperature alloy cutting coating tool and a preparation method thereof according to the present invention, Figure 1 As shown, it includes a tool substrate 1 and a multilayer coating 3 deposited on the tool substrate 1. The multilayer coating 3 includes a transition layer 4 deposited on the tool substrate 1, a periodic composite layer 5 deposited on the transition layer 4, and a functional layer 6 deposited on the periodic composite layer 5. In addition, a bonding layer 2 is selectively deposited between the substrate 1 and the multilayer coating 3. By adjusting the target material composition and deposition parameters, the bonding layer 2 is specifically a TiAlCr metal compound layer; the transition layer 4 is specifically Ti0.30Al0.60Cr0.10N with an average thickness of 0.5μm; the periodic composite layer 5 is specifically Ti 0.15 Al 0.40 Cr 0.15 Zr 0.10 Ta 0.10 Si 0.10 N / Ti0.30Al0.60Cr0.10N, this layer is Ti 0.15 Al 0.40 Cr 0.15 Zr 0.1 0Ta 0.10 Si 0.10 The periodic composite layer obtained by alternating deposition of N layer and Ti0.30Al0.60Cr0.10N layer is specifically 200 cycles with an average thickness of 2.0 μm. The average thickness of the Ti0.30Al0.60Cr0.10N first composite layer 5a is 4.0 nm. 0.15 Al 0.40 Cr 0.15 Zr 0.10 Ta 0.10 Si 0.10 The average thickness of the second composite layer 5b is 6.0 nm; the functional layer 6 is specifically Ti 0.15 Al 0.40 Cr 0.15 Zr 0.10 Ta 0.10 Si 0.10 N, with an average thickness of 0.5 μm. In this embodiment, the multilayer coating 3 has an overall average thickness of 3.0 μm, a hardness of 34.8 GPa, an elastic modulus of 284.3 GPa, and H 3 / E 2 It is 0.52.

[0096] The coated tools prepared in Example 8 and the control were used to perform milling experiments on a high-temperature alloy (GH4169). When the maximum wear width of the tool flank was ≥0.3 mm, the tool was considered to have failed, and the accumulated machining time was recorded as the tool life. The comparative experimental results are shown in Table 8 below:

[0097] Table 8: Comparative experimental results of Example 8 of the present invention and the reference product

[0098]

[0099] Table 8 shows that, under identical tool structure and cutting conditions, the multilayer coated tool of the present invention achieves an 85% longer service life when milling high-temperature alloys than the conventional AlTiN-coated tool. Compared to Example 1, the M element set is modified from Ta (15%) in Example 1 to Zr (10%) + Ta (10%), maintaining the same technical performance as in Example 1.

[0100] The above description is only a preferred specific embodiment of the present invention, but the scope of protection of the present invention is not limited thereto. Any technician familiar with the technical field, within the technical scope disclosed by the present invention, who makes equivalent replacements or changes based on the technical solution and inventive concept of the present invention, should be covered by the scope of protection of the present invention.

Claims

1. A high-temperature alloy cutting coating tool, comprising a tool substrate and a multi-layer coating deposited on the tool substrate, characterized in that: The multilayer coating includes a transition layer, a periodic composite layer, and a functional layer in sequence from the tool substrate side toward the surface side of the multilayer coating, wherein the periodic composite layer has an alternating stacking structure in which a first composite layer and a second composite layer are alternately repeated twice or more, and the transition layer has the same chemical composition as the first composite layer and is composed of a compound represented by the following formula (1): You a To b Cr c No. 1 In formula (1), 0.10≤a≤0.45, 0.10≤b≤0.45, 0.10≤c≤0.45, a+b+c=1, The second composite layer has the same chemical composition as the functional layer and is composed of a compound represented by the following formula (2): You d To e Cr f M g THE h No. 2 In formula (2), M represents an element set consisting of at least one element selected from Zr, V, Mo, Nb, Ta, W, Hf, Ce, Sc, Y, and La, and L represents an element set consisting of at least one element selected from C, B, and Si, and satisfies 0.10≤d≤0.40, 0.10≤e≤0.40, 0.10≤f≤0.40, 0.10≤g≤0.25, 0.10≤h≤0.20, and d+e+f+g+h=1. The compound Ti a Al b Cr c N and the compound Ti d Al e Cr f M g L h The element composition of N satisfies 0.05≤|ad|≤0.20, 0.05≤|be|≤0.20, 0.05≤|cf|≤0.20; In the nanoindentation analysis of the multilayer coating, 28 GPa ≤ H ≤ 40 GPa, 270 GPa ≤ E ≤ 340 GPa, and 0.30 ≤ H 3 / E 2 ≤0.65, wherein H is the hardness of the multilayer and E is the elastic modulus of the multilayer coating.

2. The high-temperature alloy cutting coating tool according to claim 1, characterized in that: The atomic ratio of nitrogen element relative to all elements in the multilayer coating is 45% to 55%.

3. The high-temperature alloy cutting coating tool according to claim 1, characterized in that: The thickness of the periodic composite layer accounts for 50% to 80% of the total thickness of the multilayer coating, and the thickness of the functional layer accounts for 10% to 30% of the total thickness of the multilayer coating.

4. The high-temperature alloy cutting coating tool according to claim 1, characterized in that: The average thickness of each single layer of the first composite layer and the second composite layer alternately stacked in the periodic composite layer is 2 nm to 30 nm.

5. The high-temperature alloy cutting coating tool according to claim 1, characterized in that: The overall average thickness of the multi-layer coating is 1 μm to 8 μm.

6. The high-temperature alloy cutting coating tool according to claim 1, characterized in that: There is also a bonding layer between the tool substrate and the multilayer coating. The bonding layer is composed of a compound composed of at least one element selected from the element set consisting of Al, Cr, Ti, V, Zr, Nb, Ta, Mo, W, B, C, Si, N, and O. The average thickness of the bonding layer is 10nm to 50nm.

7. The high-temperature alloy cutting coating tool according to claim 1, characterized in that: The tool base material is any one of cemented carbide, metal ceramic or high-speed steel tool.

8. The method for preparing a high-temperature alloy cutting coating tool according to any one of claims 1 to 7, comprising the following steps: (1) Pretreatment of the tool base; (2) selectively depositing a bonding layer on the surface of the tool substrate; (3) A physical vapor deposition process is used in an alternating deposition manner to deposit a transition layer through a TiAlCr target, a periodic composite layer with an alternating stacking structure through a TiAlCr target and a TiAlCrLM target, and a functional layer through a TiAlCrLM target, thereby obtaining the high-temperature alloy cutting coating tool.

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