Preparation method of CuAlC-Mo wear-resistant anticorrosive coating

Abstract

The invention discloses a preparation method of a CuAlC-Mo wear-resistant anticorrosive coating, which comprises the following steps: preparing pure Mo powder; cuAlC alloy powder is prepared; mo powder and CuAlC alloy powder are mixed in proportion, and the mass fraction of the Mo powder is 1-7%; preparing a coating on a 304 stainless steel substrate by using a high-power laser cladding technology; wherein the laser cladding parameters are as follows: the laser power is 2kw, the powder feeding rate is 6.25 g / min, and the scanning speed is 8.5 mm / s. According to the preparation method, the CuAlC-Mo coating is prepared on the 304 stainless steel substrate through the laser cladding technology, the developed CuAlC-Mo gradient composite coating achieves the synergistic effect of multiple strengthening mechanisms through innovative component design, and the brittleness problem of a traditional Cu-based coating is solved while the high hardness of the coating is kept.

Description

TECHNICAL FIELD

[0001] The application belongs to the technical field of metal surface modification, and particularly relates to a preparation method of a CuAlC-Mo wear-resistant and corrosion-resistant coating. BACKGROUND

[0002] Corrosion and wear are important forms of material and workpiece failure, and surface engineering treatment technology is an important way to solve the corrosion and wear of workpiece surfaces, and the corresponding protection effect is achieved by treating the surface of the material or workpiece. However, existing researches are mostly concentrated on steel matrix or nickel-based coatings (such as Ni-Mo, Fe-Mo), and the optimization research on CuAlC-Mo system is less. For many years, CuAlC has been widely used in ship parts, chemical valves, power equipment and other fields due to its excellent thermal conductivity, electrical conductivity and corrosion resistance. However, the traditional CuAlC alloy has low hardness (usually only 150-250 HV), and is easy to fail under friction and wear or corrosion-wear coupling conditions, which limits its service life in harsh environments.

[0003] Mo-based wear-resistant coatings have become a research hotspot in the fields of aerospace, electronic devices and advanced materials due to their excellent tribological properties and good mechanical toughness. Traditional Cu-Mo alloy coating systems (such as CN110129730A) usually adopt a preparation process of mechanically mixing molybdenum powder. However, this method has obvious technical limitations: due to the density difference between molybdenum powder (10.22 g / cm³) and copper matrix (8.96 g / cm³), composition segregation is easy to occur during processing; at the same time, the poor interface bonding caused by mechanical mixing will cause the initiation and expansion of microcracks in the coating, and finally cause the anisotropy of the mechanical properties of the coating.

[0004] The central temperature of laser cladding is the highest, so spraying of various ceramics, high-melting-point, wear-resistant and heat-resistant materials can be carried out, and the porosity of the laser cladding coating is low, and the bonding strength between the coating and the substrate is high. In the process of high-power laser cladding, the central temperature is obviously higher than the melting point of CuAlC-Mo mixed powder, and it is feasible to use it to prepare CuAlC-Mo composite coating.

[0005] When laser cladding technology is applied to CuAlC-Mo system, the following problems need to be solved: composition uniformity problem, Mo is easy to settle in the molten pool due to its high density (10.2 g / cm³); crack sensitivity problem: the difference in thermal physical properties between CuAlC and Mo leads to residual stress; narrow process window. SUMMARY

[0006] The purpose of this section is to summarize some aspects of the embodiments of the application and briefly introduce some preferred embodiments.

[0007] In view of the above and / or problems existing in the prior art, the present application is proposed.

[0008] Therefore, the purpose of the present application is to overcome the deficiencies in the prior art, and provide a preparation method of CuAlC-Mo wear-resistant anticorrosive coating.

[0009] To solve the above technical problems, the present application provides the following technical solutions: a preparation method of CuAlC-Mo wear-resistant anticorrosive coating, comprising, preparing pure Mo powder; preparing CuAlC alloy powder; Mixing Mo powder and CuAlC alloy powder in proportion, the mass fraction of Mo powder is 1-7%; Using high-power laser cladding technology to prepare the coating on the 304 stainless steel substrate; Wherein, the laser cladding parameters are: laser power is 2kw, powder feeding rate is 6.25g / min, and scanning speed is 8.5mm / s.

[0010] As a preferred scheme of the preparation method of the present application, wherein: the preparation of pure Mo powder comprises: preparing Mo powder by atomizing metal Mo wire, the shape is near spherical, Mo≥99.0%, the particle size range is 200-400 mesh, and the average particle size is 56μm.

[0011] As a preferred scheme of the preparation method of the present application, wherein: the CuAlC alloy powder, wherein, according to mass percentage, comprises: Cu: 80%, Al: 10%, C: 10%.

[0012] As a preferred scheme of the preparation method of the present application, wherein: the particle size range of the CuAlC alloy powder is 200-500 mesh, and the average particle size is 60μm.

[0013] As a preferred scheme of the preparation method of the present application, wherein: the mass fraction of Mo powder is 1%, 3%, 5% and 7%.

[0014] As a preferred scheme of the preparation method of the present application, wherein: the high-power laser cladding technology is used to prepare the coating on the 304 stainless steel substrate, and the parameters include: powder feeding carrier gas flow is 10L / min.

[0015] As a preferred scheme of the preparation method of the present application, wherein: 99.99% argon is used as the main gas and the powder feeding carrier gas.

[0016] Still another object of the present application is to overcome the deficiencies in the prior art, and provide a CuAlC-Mo wear-resistant anticorrosive coating, wherein: the thickness of CuAlC-Mo is 900-1100um.

[0017] Advantages of the present application: (1) The present application first uses laser cladding technology to prepare CuAlC-Mo coating on 304 stainless steel substrate, and by adjusting the addition amount of Mo (0 / 1 / 3 / 5 / 7 wt.%), the macroscopic morphology of the coating is observed, phase analysis is carried out, and wear resistance and corrosion resistance performance test is carried out; research found that the developed CuAlC-Mo gradient composite coating realizes the synergistic effect of multiple strengthening mechanisms through innovative component design: first, the solid solution strengthening effect of Mo element in Cu / Al matrix significantly improves the hardness of the coating (microhardness can reach 400 HV); second, as Li et al. (Materials & Design, 2020) confirmed, the in-situ generated nanoscale AlMo3 intermetallic compound can effectively inhibit the cracking of the coating through the grain boundary pinning effect and crack tip blunting mechanism; more importantly, the gradient addition technology (0 / 1 / 3 / 5 / 7 wt.%) of the present system promotes the co-generation of Mo2C hard phase and AlMo3 phase, which improves the brittleness problem of traditional Cu-based coating while maintaining high hardness of the coating. In terms of corrosion protection performance, the coating system shows unique advantages: the addition of molybdenum promotes the formation of a dense passivation film (mainly MoO3), and the charge transfer resistance (Rct) of the coating containing 5wt.% Mo can reach 8887 Ω·cm², which is nearly 5 times higher than that of the sample without adding molybdenum. This passivation film induced by molybdenum can effectively block the penetration of corrosive media, significantly improving the service life of the coating in harsh environments.

[0018] (2) The wear and corrosion resistance experiment results of CuAlC-Mo coating can be found that when the addition amount is 5 wt.%, the microhardness of the coating is increased by 30%~50% (0wt.% Mo coating hardness 150~250 HV, 5wt.% Mo coating hardness 300~400 HV), under the dry sliding linear friction wear test conditions of alumina ball as friction pair, friction rotation speed of 4 hz, and loading pressure of 10 Newton, the lubrication effect of Mo reduces the friction coefficient of the coating by 13% (0wt.% Mo coating friction coefficient is 0.31, 5wt.% Mo coating friction coefficient is 0.26), and high Mo content (5 / 7 wt.%) coating shows excellent anti-abrasive wear ability in SEM. The corrosion resistance of the coating is tested by Gamary electrochemical workstation, and in 3.5% NaCl solution, the self-corrosion potential (Ecorr) and impedance of 5wt.% Mo coating are significantly better than 0wt.% Mo, which promotes the formation of passivation film (such as MoO3), inhibits electrochemical corrosion, and improves the corrosion resistance. BRIEF DESCRIPTION OF DRAWINGS

[0019] In order to more clearly illustrate the technical solutions of the embodiments of the present application, the drawings needed to be used in the embodiments will be briefly introduced as follows. Obviously, the drawings in the following description are only some embodiments of the present application, and other drawings can be obtained by those skilled in the art without any creative effort on the basis of these drawings. Among them: Figure 1 CuAlC-Mo coating cross-section microstructure diagram, wherein (a) corresponds to CuAlC-0wt.%Mo, (b) corresponds to CuAlC-1wt.%Mo, (c) corresponds to CuAlC-3wt.%Mo, (d) corresponds to CuAlC-5wt.%Mo, (e) corresponds to CuAlC-7wt.%Mo cross-section microstructure diagram; Figure 2 CuAlC-0wt.%Mo, CuAlC-1wt.%Mo, CuAlC-3wt.%Mo, CuAlC-5wt.%Mo, CuAlC-7wt.%Mo coating surface microhardness diagram; Figure 3 CuAlC-0wt.%Mo, CuAlC-1wt.%Mo, CuAlC-3wt.%Mo, CuAlC-5wt.%Mo, CuAlC-7wt.%Mo coating thickness diagram; Figure 4 CuAlC-Mo coating Mo element content EDS diagram, wherein (a) corresponds to CuAlC-0wt.%Mo, (b) corresponds to CuAlC-1wt.%Mo, (c) corresponds to CuAlC-3wt.%Mo, (d) corresponds to CuAlC-5wt.%Mo, (e) corresponds to CuAlC-7wt.%Mo coating Mo element content EDS diagram; Figure 5 CuAlC-Mo friction coefficient diagram; Figure 6 CuAlC-Mo wear scar SEM diagram, wherein (a) corresponds to CuAlC-0wt.%Mo wear scar SEM diagram, (b) corresponds to CuAlC-1wt.%Mo wear scar SEM diagram, (c) corresponds to CuAlC-3wt.%Mo wear scar SEM diagram, (d) corresponds to CuAlC-5wt.%Mo wear scar SEM diagram, (e) corresponds to CuAlC-7wt.%Mo wear scar SEM diagram; Figure 7 CuAlC-Mo electrochemical polarization test result diagram and electrochemical impedance test result diagram, wherein, a is the CuAlC-Mo electrochemical polarization test result diagram, and b is the CuAlC-Mo electrochemical impedance test result diagram. DETAILED DESCRIPTION

[0020] In order to make the above-mentioned purposes, features and advantages of the present application more obvious and easy to understand, the specific embodiments of the present application will be described in detail below with reference to the description examples.

[0021] In this embodiment, 304 stainless steel is used as the substrate material for laser cladding, with a geometric size of 100x 100x10 mm, and the main chemical components are: C≤0.08%, Si≤1.0%, Mn≤2.0%, Cr: 18.0-20.0%, Ni: 8.0-10.5%, S≤0.03%, P≤0.035%, N≤0.1%, and the balance is Fe.

[0022] In this embodiment, CuAlC-0wt.%Mo, CuAlC-1wt.%Mo, CuAlC-3wt.%Mo, CuAlC-5wt.%Mo, CuAlC-7wt.%Mo are used as laser cladding powders for laser cladding; pure Mo powder with a mass fraction of Mo≥99.0% is used, and the mass percentage of CuAlC includes: Cu: 80%, Al: 10%, C: 10%, and the particle size distribution interval of the two powders is 56-60μm.

[0023] The laser cladding system used in the laser cladding experiment of the present application is composed of an RFL-C3000 type fiber laser, an HR-PFS-STBN06 type powder feeder, a CWFL*3000ANS type water cooler and an SBW-50KVA type voltage stabilizing power supply.

[0024] Example 1 (1) 304 stainless steel substrate treatment Before the experiment, the oxides, rust or other contaminants on the surface of the material are removed by wiping. This helps to ensure a clean, smooth and flat metal surface during laser cladding, and then ethanol is used to clean the surface of the material to remove residual dirt. The 304 stainless steel substrate is preheated before the experiment, placed on a constant temperature heating table at 300 degrees Celsius, effectively preventing deformation or cracking of the substrate during laser cladding due to excessive temperature gradient, and ensuring the smooth progress of the experiment.

[0025] (2) Drying treatment of cladding powder: The CuAlC-Mo powder is heated in an oven, with a temperature setting of 120℃ and a timing of 2.5h to remove water vapor in the powder.

[0026] (3) Laser cladding: The coaxial powder feeding laser cladding method is used, and during the laser cladding process, the cladding powder is fed synchronously into the laser beam below the laser beam, so that it is melted; On the surface of 304 stainless steel, the cladding powder melts rapidly and cools quickly to form cladding layers CuAlC-0wt.%Mo, CuAlC-1wt.%Mo, CuAlC-3wt.%Mo, CuAlC-5wt.%Mo, CuAlC-7wt.%Mo, with a thickness of 1000-1200 μm; The parameters include: powder feeding carrier gas flow: 10 L / min, powder feeding rate: 6.25 g / min, scanning speed: 8.5 mm / s, laser power: 2 kw, cladding distance: 35 mm; 99.99% argon is used as the main gas and powder feeding carrier gas.

[0027] In combination Figure 1 (a-e) Coating cross-section, cladding CuAlC-0wt.%Mo, CuAlC-1wt.%Mo, CuAlC-3wt.%Mo, CuAlC-5wt.%Mo, CuAlC-7wt.%Mo powder on 304 stainless steel substrate by coaxial powder feeding laser cladding process, powder feeding carrier gas flow: 10 L / min, powder feeding rate: 6.25 g / min, scanning speed: 8.5 mm / s, laser power: 2 kw, cladding distance: 35 mm; 99.99% argon is used as the main gas and powder feeding carrier gas.

[0028] The coating cross-section is cut using an electric spark cutting machine, and the coating cross-section is polished with 400 mesh, 600 mesh, 800 mesh, 1200 mesh, and 2000 mesh sandpaper, respectively, and polished with W2.5 and W0.5 diamond polishing paste. Under the optical microscope, it can be found that the formed coating is a dense structure without pores and cracks.

[0029] (4) Hardness test The Vickers hardness tester (model HV-1000A) produced by Laizhou Huayin Test Instrument Co., Ltd. is used to test the CuAlC-0wt.%Mo, CuAlC-1wt.%Mo, CuAlC-3wt.%Mo, CuAlC-5wt.%Mo, CuAlC-7wt.%Mo coating surface. The sample is polished into a mirror surface before testing, the loading direction is perpendicular to the sample surface, and the main parameters of the instrument are: load 1N, retention time 15s. Take the position of the top end of the coating as the starting point, every 0.15mm as a hardness test point, record the hardness value of 6 points, and take the average value; The hardness value is shown in Figure 2 The results show that the addition of Mo powder improves the hardness of CuAlC coating, and the hardness is highest (30%~50%) when the addition amount is 5 wt.%.

[0030] (5) Coating thickness test The thickness of CuAlC-0wt.%Mo, CuAlC-1wt.%Mo, CuAlC-3wt.%Mo, CuAlC-5wt.%Mo, CuAlC-7wt.%Mo coatings were measured by the scale function of optical microscope, as shown in Fig. 1. Figure 3 As shown, the coating thickness becomes thicker with the addition of Mo content, and the thickening of the coating can improve the wear resistance and provide a longer protection period in the corrosion environment.

[0031] (4) Preparation before friction corrosion experiment The experimental coating samples were cut by an electric spark cutting machine with a size of 10mm*10mm*2mm. The surface was polished with 180-grit sandpaper to remove the surface oxide layer and lap marks, in preparation for the friction and electrochemical experiments.

[0032] In combination with Figure 4 (a-e) EDS maps of Mo element content in CuAlC-Mo coatings. To ensure the uniform presence of Mo in the coating, EDS surface scanning method was used to observe the prepared coating. The EDS scanning analysis results show that with the increase of Mo content in the coating, the uniformity of Mo element distribution is significantly improved, indicating that the solid solubility of Mo in the coating matrix is enhanced, and there is no obvious segregation or precipitation phenomenon.

[0033] (5) Friction experiment In combination with Figure 5 the friction coefficient diagram of CuAlC-Mo in the, under the dry sliding linear friction and wear test conditions of a linear reciprocating friction machine, an alumina ball, a frequency of 4 hz, a load of 10N, and a friction time of 1h, the friction coefficient of each coating was obtained. From the experimental results, it can be found that the lubrication effect of Mo reduces the friction coefficient of the coating by 13% (the average friction coefficient of the 0wt.%Mo coating is 0.31, and the average friction coefficient of the 5% wt. Mo coating is 0.26). With the increase of Mo element content, the friction coefficient of the coating decreases, and the optimal content of Mo is 5 wt.%. The reason is that when the Mo content is≦5 wt.%, Mo2C hard phase is uniformly distributed in the coating to improve its wear resistance; However, when it exceeds 5 wt.%, the excess Mo leads to the aggregation of unmelted Mo particles, local stress concentration, and thus reduces the density of the coating, thereby reducing its wear resistance.

[0034] In combination with Figure 6 the SEM images of CuAlC-0wt.%Mo, CuAlC-1wt.%Mo, CuAlC-3wt.%Mo, CuAlC-5wt.%Mo, CuAlC-7wt.%Mo coating wear scars in Figure 6 (a-c) The wear scar surface presents continuous furrows and adhesive wear spalling pits, and the wear form is typical adhesive wear and abrasive wear.Figure 6 d is the optimal Mo content (5 wt.%) wear scar, which can be found that the furrow is obviously shallower, no large area peeling, and slight abrasive wear is mainly. Figure 6 e mark the wear scar exists crack and block peeling, the main wear mechanism is brittle peeling.

[0035] (6) Electrochemical experiment Combining Figure 7 The electrochemical experiment results figure, the test equipment is Gamry electrochemical workstation.

[0036] The sample is used as the working electrode, and the coating surface is parallel to the platinum electrode surface. The reference electrode is a saturated silver chloride electrode. The open circuit potential, impedance spectrum and dynamic polarization curve of the coating are tested in a 3.5% NaCl solution. The frequency range of the electrochemical impedance test is 10 kHz~0.01 Hz, the relative open circuit potential OCP is selected from-500mV to +500mV, and the dynamic polarization curve test is carried out at a scanning rate of 10 mV / s. All tests are carried out at room temperature.

[0037] From Figure 7 a, the polarization curves of all samples show obvious passivation characteristics: in the initial stage of anodic polarization, the current density decreases sharply with the increase of potential, indicating that the passivation film is rapidly generated; then it enters the stable passivation zone, and the current density remains at a low level; when the potential exceeds the critical value, the current density increases exponentially, indicating that the passivation film fails and causes active dissolution of the metal. With the increase of Mo content from 0 wt.% to 7 wt.%, the self-corrosion potential gradually shifts to the positive direction. Among them, the self-corrosion potential of CuAlC-0wt.%Mo is-0.27 V, and the self-corrosion potential of CuAlC-5wt.%Mo is-0.21 V, which is positively offset by 60 mV. This change shows that with the increase of Mo content, the corrosion tendency of the material is obviously reduced, the stability of the passivation film is enhanced, and the corrosion resistance is significantly improved.

[0038] Combining Figure 7 b impedance spectrum, ZSimpleWin software is used for fitting, and the equivalent circuit is R(Q(R(QR))), the model composition is: solution resistance R1, coating resistance R2, Q1(CPE) representing the capacitance characteristics of the coating, charge transfer resistance R3 and Q2(CPE) representing the double-layer capacitance.

[0039] The fitting results are shown in Table 1, and the R1 value of all samples is in the range of 5-8Ω•cm 2, which is in the typical range of 3.5 NaCl solution, indicating that the Mo content has no effect on the bulk resistance of the electrolyte. With the increase of Mo content, the R2 value increases, and the R2 of CuAlC-5wt.%Mo is the highest (3077 Ω•cm²), indicating that its coating has the best compactness. The R2 of CuAlC-7wt.%Mo decreases to 2022 Ω•cm², which may be related to the micro-cracks caused by high Mo content. The R3 of CuAlC-5wt.%Mo is as high as 8887 Ω•cm², which is much higher than that of other groups, indicating that its interface passivation film is the most stable and the corrosion reaction is the most difficult to produce. The R3 of CuAlC-7wt.%Mo decreases to 5731 Ω•cm², but it is still better than the 0-3wt.%Mo group, indicating that the passivation effect of Mo is still partially retained. The CuAlC-5wt.%Mo coating has the best wear and corrosion resistance, indicating that there is an optimal value for the Mo content of the CuAlC-Mo coating, and 5wt.%Mo is the inflection point of the coating performance.

[0040] Table 1 Comparative Example 1 On 304 stainless steel, the cladding material is CuAlC+5%Mo, and the preparation process is as in Example 1, except that: Laser process parameters: power 1500 W, scanning speed 12 mm / s, powder feeding rate: 8 g / min, other processes are the same as in Example 1.

[0041] It is found that, at a low laser power, the molten pool energy is insufficient, Mo is not completely dissolved, and the hard phase is not fully precipitated, resulting in low hardness; the cooling rate of the cladding layer is too high, and the coating has micro-cracks. The powder is not completely melted, resulting in too low coating density.

[0042] Comparative Example 2 Hardness improvement: the "critical threshold effect" of Mo breaks the linear growth expectation: Conventional prediction: as a solid solution strengthening element, the hardness should increase by ~30 HV per 1 wt.% Mo (based on the solid solution strengthening model). Actual findings: 3 wt.% Mo: the hardness only increases to 300 HV (as expected). 5 wt.% Mo: the hardness increases sharply to 400 HV (far exceeding the predicted value of 340 HV).

[0043] Theoretical prediction: Mo improves wear resistance, but the friction coefficient should slowly decrease with the increase of Mo content (based on the Archard wear model), and the actual measurement result: the friction coefficient of 5 wt.% Mo decreases sharply to 0.26.

[0044] The classic percolation theory predicts that the addition of low content (<10%) conductive fillers usually only makes the Rtr of the coating increase by 1-2 times, but the experimental data (5 times increase, Rtr=8887 Ω·cm²) breaks through the theoretical limit.

[0045] The present application realizes breakthroughs in mechanical properties, corrosion resistance, process stability, etc. through the synergistic regulation of gradient addition of Mo and high-power laser process, especially when the Mo content is high (5-7 wt.%), it exhibits performance combinations beyond existing literature reports, providing a new surface strengthening solution for extreme environment components.

[0046] The skilled person in the art may believe that the addition of Mo will linearly improve corrosion resistance and hardness (based on the properties of Mo itself), but the present application achieves unexpected results: at a certain proportion (such as 5-7 wt.% Mo), the corrosion resistance and hardness show nonlinearity, indicating the existence of a threshold; the hardness can reach 400HV at 5% Mo, while it is only 300HV at 3 wt.% Mo, indicating that Mo triggers grain boundary strengthening or the formation of nano precipitates at the critical concentration. This nonlinear mutation is not easily predictable by the skilled person in the art.

[0047] The present application solves the problem that traditional CuAlC coatings cannot balance corrosion resistance, high-temperature stability and bonding strength through the specific proportion regulation of Mo.

[0048] It should be noted that the above examples are only used to illustrate the technical solutions of the present application and are not limiting. Although the present application has been described in detail with reference to the preferred embodiments, those skilled in the art should understand that the technical solutions of the present application can be modified or replaced by equivalents without departing from the spirit and scope of the present application, and they should be included in the scope of the present application.

Claims

1. A method for preparing a CuAlC-Mo wear-resistant and corrosion-resistant coating, characterized in that: include, Preparation of pure Mo powder; Preparation of CuAlC alloy powder; Mo powder and CuAlC alloy powder are mixed in a certain proportion, with the mass fraction of Mo powder being 1-7%. A coating was prepared on a 304 stainless steel substrate using high-power laser cladding technology; The laser cladding parameters are as follows: laser power is 2 kW, powder feeding rate is 6.25 g / min, and scanning speed is 8.5 mm / s.

2. The preparation method according to claim 1, characterized in that: The preparation of pure Mo powder includes producing Mo powder by atomizing a metal Mo filament. The powder is nearly spherical in shape, with Mo ≥ 99.0%, a particle size range of 200~400 mesh, and an average particle size of 56 μm.

3. The preparation method according to claim 1 or 2, characterized in that: The CuAlC alloy powder comprises, by mass percentage: Cu: 80%, Al: 10%, C: 10%.

4. The preparation method according to claim 3, characterized in that: The CuAlC alloy powder has a particle size range of 200~500 mesh and an average particle size of 60μm.

5. The preparation method according to claim 1 or 4, characterized in that: The Mo powder has a mass fraction of 1%, 3%, 5%, and 7%.

6. The preparation method according to claim 1, characterized in that: The coating is prepared on a 304 stainless steel substrate using high-power laser cladding technology, wherein the parameters include: powder carrier gas flow rate: 10L / min.

7. The preparation method according to claim 6, characterized in that: Argon with a purity of 99.99% is used as the main gas and the powder carrier gas.

8. The CuAlC-Mo wear-resistant and corrosion-resistant coating prepared by any of the preparation methods described in claims 1 to 7.

9. The CuAlC-Mo wear-resistant and corrosion-resistant coating according to claim 8, characterized in that: The thickness of the CuAlC-Mo is 900~1100um.

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