Al2O3-TiB2 double-phase composite titanium-based coating and preparation method thereof

Abstract

The invention belongs to the technical field of double-phase composite titanium-based coatings, and relates to an Al2O3-TiB2 double-phase composite titanium-based coating and a preparation method thereof. The Al2O3-TiB2 double-phase composite titanium-based coating is prepared from the following raw materials: titanium-based powder, Al2O3 powder and TiB2 powder; based on the total weight of the raw materials of the Al2O3-TiB2 double-phase composite titanium-based coating, the content of the TiB2 powder is 25-50 wt%, the content of the Al2O3 powder is 15-25 wt%, and the balance is the titanium-based powder. According to the formula of the high-proportion Al2O3-TiB2 double-phase composite titanium-based coating, the hardness of the double-phase composite titanium-based coating prepared through laser cladding according to the formula can be 3 times that of a TC4 substrate, the abrasion loss of the double-phase composite titanium-based coating can be 0.12 times that of the TC4 substrate, and the double-phase composite titanium-based coating has good abrasion resistance and high hardness. The preparation method provided by the invention is simple and operable, and can realize large-scale production.

Description

Technical Field

[0001] This invention belongs to the field of dual-phase composite titanium-based coating technology, specifically, it relates to an Al2O3-TiB2 dual-phase composite titanium-based coating and its preparation method. Background Technology

[0002] Titanium and titanium alloys are widely used in aerospace, defense, marine engineering, and biomedicine due to their lightweight, high strength, corrosion resistance, high temperature resistance, and good biocompatibility. However, their high coefficient of friction, poor wear resistance, and flammability during high-temperature, high-speed friction severely limit their further widespread application. Appropriate surface treatment can alter the state of titanium and titanium alloy products, thereby giving them a better appearance, improving the properties of the base material, and even acquiring new properties not present in the base material. This is of great significance for improving the lifespan of titanium and titanium alloy products and overcoming their inherent shortcomings.

[0003] Laser cladding technology is widely used due to its wide applicability, short repair cycle, and excellent remanufactured coating performance. It is often used to prepare various wear-resistant coatings for titanium alloys. TiB2 has advantages such as high melting point, high hardness (2800-3500 HV), low thermal conductivity, a coefficient of thermal expansion that matches the titanium matrix, good wettability with the titanium matrix, and high bonding strength, and is often used as a reinforcing phase for titanium matrix coatings. For single TiB2-reinforced titanium matrix coatings, when the mass fraction of the reinforcing phase TiB2 exceeds 15%, the composite coating is prone to cracking, thus limiting the reinforcing effect of the composite coating. Al2O3 is another optional reinforcing phase for titanium matrix composite coatings, which can improve the hardness and strength of the composite coating while also improving its oxidation resistance. However, as an oxide reinforcing phase, as the proportion of Al2O3 increases to 5%, the oxygen content in the composite coating increases, thereby increasing the tendency of the composite coating to crack. Summary of the Invention

[0004] The purpose of this invention is to prepare a titanium-based composite coating using two reinforcing phases, Al2O3 and TiB2. The addition of high Al2O3 content can effectively improve the shape and distribution of the TiB2 reinforcing phase, thereby improving the toughness of the composite coating and reducing cracks and pores in the two-phase composite coating.

[0005] To achieve the above objectives, a first aspect of the present invention provides an Al2O3-TiB2 dual-phase composite titanium-based coating, wherein the raw materials of the Al2O3-TiB2 dual-phase composite titanium-based coating include titanium-based powder, Al2O3 powder and TiB2 powder. Based on the total weight of the raw materials for the Al2O3-TiB2 dual-phase composite titanium-based coating, the content of TiB2 powder is 25-50 wt%, the content of Al2O3 powder is 15-25 wt%, and the remainder is titanium-based powder.

[0006] A second aspect of the present invention provides a method for preparing an Al2O3-TiB2 dual-phase composite titanium-based coating, comprising the following steps: (1) Obtaining cladding mixed powder: After uniformly mixing titanium-based powder, Al2O3 powder and TiB2 powder, vacuum drying is performed to obtain cladding mixed powder; wherein, based on the total weight of the cladding mixed powder, the content of TiB2 powder is 25-50wt%, the content of Al2O3 powder is 15-25wt%, and the remainder is titanium-based powder. (2) Pretreatment of titanium matrix material: The titanium matrix material is polished, cleaned and dried in sequence; (3) Preparation of dual-phase composite titanium-based coating: The laser cladding process is adopted. Under the protection atmosphere of argon, the cladding mixture powder is laser clad on the surface of the pretreated titanium substrate material by means of binder powder spreading method or synchronous powder feeding method to form Al2O3-TiB2 dual-phase composite titanium-based coating.

[0007] The technical solution of the present invention has the following beneficial effects: (1) This invention provides a formulation for a high-proportion Al2O3-TiB2 dual-phase composite titanium-based coating. The dual-phase composite titanium-based coating prepared by laser cladding using this formulation can achieve a hardness three times that of the TC4 substrate and reduce wear to 0.12 times that of the TC4 substrate, exhibiting excellent wear resistance and high hardness.

[0008] (2) The preparation method of the present invention is simple and operable and can be mass-produced.

[0009] Other features and advantages of the present invention will be described in detail in the following detailed description section. Attached Figure Description

[0010] The above and other objects, features and advantages of the present invention will become more apparent from the more detailed description of exemplary embodiments of the invention in conjunction with the accompanying drawings, wherein the same reference numerals generally represent the same components in the exemplary embodiments of the invention.

[0011] Figure 1 The cross-sectional macroscopic morphology of the Al2O3-TiB2 dual-phase composite titanium-based coating according to the present invention is shown in the figure. Figure 1 The figures above show the cross-sectional macroscopic morphology of Al2O3-TiB2 dual-phase composite titanium-based coatings for Comparative Examples 1, 2, 3 and 4, respectively.

[0012] Figure 2 A cross-sectional macroscopic morphology image of an Al2O3-TiB2 dual-phase composite titanium-based coating according to an embodiment of the present invention is shown, wherein, Figure 2 The figures ae show the cross-sectional macroscopic morphology of the Al2O3-TiB2 dual-phase composite titanium-based coatings in Examples 1, 2, 3, 4 and 5, respectively.

[0013] Figure 3 The cross-sectional microstructure of the Al2O3-TiB2 dual-phase composite titanium-based coating according to the present invention is shown in the figure. Figure 3 The figures above show the cross-sectional microstructures of the Al2O3-TiB2 dual-phase composite titanium-based coatings in Comparative Examples 1, 2, 3, and 4, respectively.

[0014] Figure 4 The cross-sectional microstructure of the Al2O3-TiB2 dual-phase composite titanium-based coating according to an embodiment of the present invention is shown, wherein... Figure 4 The images show the cross-sectional microstructures of the Al2O3-TiB2 dual-phase composite titanium-based coatings in Examples 1, 2, 3, 4, and 5, respectively.

[0015] Figure 5 A comparative microhardness distribution curve according to the present invention is shown, wherein, Figure 5 The figures ac show the microhardness distribution curves of the substrate and coating in the cross section, longitudinal section and melt channel intersection area of ​​the comparative examples 1-4 according to the present invention.

[0016] Figure 6 A microhardness distribution curve according to an embodiment of the present invention is shown, wherein, Figure 6 Figures a and b respectively show the microhardness distribution curves of the coating cross section and the melt channel intersection area of ​​the coating according to Embodiments 1-5 of the present invention.

[0017] Figure 7 The friction coefficient curves of the substrate and coating according to Comparative Examples 1-4 of the present invention are shown.

[0018] Figure 8 The wear amount histograms of the substrate and coating according to Comparative Examples 1-4 of the present invention are shown.

[0019] Figure 9 The friction coefficient curves of the substrate and coating according to Embodiments 1-5 of the present invention are shown.

[0020] Figure 10 The wear of the substrate and coating according to embodiments 1-5 of the present invention is shown in histograms.

[0021] Figure 11 Impedance spectra of the substrates and coatings according to Comparative Examples 1-4 of the present invention in an aqueous solution of NaCl with a mass concentration of 3.5 wt% are shown.

[0022] Figure 12 Polarization curves of the substrates and coatings according to Comparative Examples 1-4 of the present invention in a 3.5 wt% NaCl aqueous solution are shown.

[0023] Figure 13 A schematic diagram of the cladding path according to an embodiment and a comparative example of the present invention is shown.

[0024] Figure 14 A schematic diagram of hardness sampling points according to an embodiment and a comparative example of the present invention is shown, wherein, Figure 14 The ac values ​​respectively illustrate transverse sampling, longitudinal sampling, and longitudinal sampling at the weld seam overlap. Detailed Implementation

[0025] Preferred embodiments of the invention will now be described in more detail. While preferred embodiments of the invention are described below, it should be understood that the invention can be implemented in various forms and should not be limited to the embodiments set forth herein.

[0026] The first aspect of the present invention provides an Al2O3-TiB2 dual-phase composite titanium-based coating, wherein the raw materials of the Al2O3-TiB2 dual-phase composite titanium-based coating include titanium-based powder, Al2O3 powder and TiB2 powder; Based on the total weight of the raw materials for the Al2O3-TiB2 dual-phase composite titanium-based coating, the content of TiB2 powder is 25-50 wt%, the content of Al2O3 powder is 15-25 wt%, and the remainder is titanium-based powder.

[0027] In order to solve the problem of insufficient strengthening effect in existing single Al2O3 or TiB2 titanium-based composite coatings, this invention adopts simultaneous composite strengthening of Al2O3 and TiB2 as two strengthening agents to obtain an Al2O3 and TiB2 dual-phase composite titanium-based coating with better wear resistance and corrosion resistance.

[0028] According to the present invention, preferably, the titanium-based powder is titanium alloy powder and / or pure titanium powder, and the titanium alloy powder is preferably TC4 powder.

[0029] A second aspect of the present invention provides a method for preparing an Al2O3-TiB2 dual-phase composite titanium-based coating, comprising the following steps: (1) Obtaining cladding mixed powder: After uniformly mixing titanium-based powder, Al2O3 powder and TiB2 powder, vacuum drying is performed to obtain cladding mixed powder; wherein, based on the total weight of the cladding mixed powder, the content of TiB2 powder is 25-50wt%, the content of Al2O3 powder is 15-25wt%, and the remainder is titanium-based powder. (2) Pretreatment of titanium matrix material: The titanium matrix material is polished, cleaned and dried in sequence; (3) Preparation of dual-phase composite titanium-based coating: The laser cladding process is adopted. Under the protection atmosphere of argon, the cladding mixture powder is laser clad on the surface of the pretreated titanium substrate material by means of binder powder spreading method or synchronous powder feeding method to form Al2O3-TiB2 dual-phase composite titanium-based coating.

[0030] According to the present invention, preferably, in step (1), the mixing is carried out using a ball mill, a can mill, or a mixer, preferably using a ball mill; Preferably, the ball mill rotates at a speed of 80-120 r / min, the ball-to-material ratio is (1-5):1, and the mixing time is 20-24 hours.

[0031] In this invention, the ball mill is preferably a planetary ball mill.

[0032] According to the present invention, preferably, in step (1), the conditions for vacuum drying include: vacuum degree of 0.1-5 Pa, temperature of 80-120℃, and time of 3-4 h.

[0033] According to the present invention, preferably, in step (1), the particle size of the titanium-based powder is 53-106 micrometers; The particle size of the Al2O3 powder is 1-380 micrometers, preferably 180-380 micrometers; The average particle size of the TiB2 powder is 1-80 micrometers, preferably 65-75 micrometers.

[0034] According to the present invention, preferably, in step (2), the titanium matrix material is pure titanium or titanium alloy, and the titanium alloy is preferably TC4 (Ti-6Al-4V).

[0035] According to the present invention, preferably, in step (2), the polishing is done with 2000 grit sandpaper; the cleaning is done with anhydrous ethanol.

[0036] According to the present invention, preferably, in step (3), the conditions of the laser cladding process include: laser power of 1500-3000W, scanning speed of 13-18mm / s, powder feeding rate of 18-25g / min, powder feeding gas flow rate of 8-10L / min, and overlap rate of 45-55%.

[0037] According to the present invention, preferably, in step (3), the binder in the binder powdering method is water glass, which includes the following steps: After mixing the cladding powder with water glass, the mixture is uniformly applied to the pretreated titanium substrate material. After vacuum drying, laser cladding is performed.

[0038] In this invention, the modulus of the water glass Na2O·nSiO2 is 2.2~3.7, and there is no limit to its amount; it is sufficient to mix the cladding powder into a paste.

[0039] According to the present invention, preferably, the conditions for the vacuum drying process include: a vacuum degree of 0.1-5 Pa, a temperature of 80-120°C, and a time of 3-4 h.

[0040] The present invention is further illustrated by the following examples: Examples 1-5 (1) According to the formula in Table 1, TC4 powder, Al2O3 powder and TiB2 powder are mixed evenly in a planetary ball mill to obtain cladding mixed powder; wherein, the ball-to-material ratio is 2:1, the mixing time is 24 hours, and the speed of the planetary ball mill is 100 r / min.

[0041] (2) Using Ti-6Al-4V alloy as the matrix material, the matrix is ​​pretreated by first polishing the surface of the matrix material with 2000 fine sandpaper, then cleaning the surface of the matrix with anhydrous ethanol, and finally air drying.

[0042] (3) Then, the powder is mixed with water glass and evenly spread on the substrate to a thickness of about 1 mm. It is then placed in a vacuum drying oven and dried at 80°C for about 0.5 hours. After removal and cooling, once the temperature has stabilized, the vacuum-dried cladding material is clad onto the substrate surface using a laser cladding process to form an Al2O3-TiB2 dual-phase composite titanium-based coating. The cladding path of the laser cladding process is as follows: Figure 13 As shown, the conditions for laser cladding process include: laser power of 1800W, scanning speed of 14mm / s, powder feeding rate of 20g / min, powder feeding gas flow rate of 9L / min, and overlap rate of 50%.

[0043] Table 1

[0044] Note: The amounts of each component in Table 1 are based on the total weight of the cladding mixed powder. In Examples 1-5, the particle size of TC4 powder is 53-106 micrometers. In Example 5, the average particle size of Al2O3 powder and TiB2 powder is 1 micrometer. In Examples 1-4, the particle size of Al2O3 powder is 180-380 micrometers, and the average particle size of TiB2 powder is 70 micrometers.

[0045] Comparative Examples 1-4

[0046] (1) According to the formula in Table 2, TC4 powder with a particle size of 53-106 micrometers, Al2O3 powder with a particle size of 1 micrometer and TiB2 powder with a particle size of 1 micrometer were mixed evenly in a planetary ball mill to obtain the cladding material; wherein, the ball-to-material ratio was 2:1, the mixing time was 24 hours, and the rotation speed of the planetary ball mill was 100 r / min. Then the cladding material was vacuum dried in a vacuum drying oven at 0.3 Pa and 100 °C for 2 hours.

[0047] (2) Use Ti-6Al-4V alloy as the matrix material and pre-treat the matrix. First, use 2000 fine sandpaper to polish the surface of the matrix material, then clean the surface of the matrix with anhydrous ethanol, and finally let it air dry.

[0048] (3) Then, the vacuum-dried cladding mixture powder was clad using a laser cladding synchronous powder feeding method to obtain different Al2O3-TiB2 composite dual-phase composite titanium-based coating comparison examples. The cladding path of the laser cladding process is as follows: Figure 13 As shown, the conditions for laser cladding process include: laser power of 1800W, scanning speed of 14mm / s, powder feeding rate of 20g / min, powder feeding gas flow rate of 9L / min, and overlap rate of 50%.

[0049] Table 2

[0050] Note: The amounts of each component in Table 2 are based on the total weight of the cladding mixed powder. In Comparative Examples 1-4, the particle size of TC4 powder is 53-106 micrometers, and the average particle size of Al2O3 powder and TiB2 powder is 1 micrometer.

[0051] Test Example 1

[0052] The Al2O3-TiB2 dual-phase composite titanium-based coating and substrate prepared above were each cut into 6mm × 9mm samples using a wire EDM machine (sampling method as follows). Figure 14 As shown in the figure, the cross-section of the sample was then ground and polished, and after etching with metallographic etching solution (HF:HNO3:H2O=1:3:7), the macroscopic morphology of the cross-section was observed by metallographic microscope to obtain the macroscopic morphology of the cross-section of the prepared Al2O3-TiB2 dual-phase composite titanium-based coating.

[0053] Figure 2 a, Figure 2 b、 Figure 2 c. Figure 2 d、 Figure 2e shows the cross-sectional macroscopic morphology of the Al2O3-TiB2 dual-phase composite titanium-based coatings in Examples 1-5, respectively. Figure 4 a, Figure 4 b、 Figure 4 c. Figure 4 d、 Figure 4 e are microscopic morphology images of the Al2O3-TiB2 coatings in Examples 1-5, respectively. Figure 2 a~ Figure 2 As can be seen from the macroscopic morphology of the coating cross-section, compared with Comparative Examples 1-4, the porosity of Examples 1-4 is significantly reduced, while Example 5 has obvious pores with larger sizes. Examples 4 and 5 have the same powder composition ratio, and Example 5 uses the same reinforcing phase powder as Comparative Examples 2-4. Figure 4 a~ Figure 4 As can be seen, the addition of high content of Al2O3 and TiB2 reinforced phase composite titanium-based coating has a significant grain refining effect, and the microstructure is significantly different from that of the comparative example. Bamboo leaf-shaped TiB2 phase and fine-grained Al2O3 phase can be observed.

[0054] Figure 1 a, Figure 1 b、 Figure 1 c. Figure 1 Figure d shows the cross-sectional macroscopic morphology of the Al2O3-TiB2 dual-phase composite titanium-based coatings in Comparative Examples 1-4. Figure 3 a, Figure 3 b、 Figure 3 c. Figure 3 Images d show the microstructures of the Al₂O₃-TiB₂ dual-phase composite titanium-based coatings in Comparative Examples 1-4. Figure 1 a, Figure 1 b、 Figure 1 c. Figure 1 As can be seen from the macroscopic morphology of the coating cross-section, when the TiB2 content increases from 2 wt% to 6 wt%, the number and size of pores in the coating cross-section of Comparative Examples 1-4 increase significantly with the TiB2 content, and the coating cross-sections of Comparative Examples 3 and 4 have fine cracks.

[0055] Test Example 2

[0056] The Al2O3-TiB2 dual-phase composite titanium-based coatings and substrates prepared in the above embodiments and comparative examples were cut into samples of 10mm×10mm, 17mm×17mm, and 18mm×18mm sizes using a wire EDM machine. Hardness, wear resistance, and corrosion resistance were then tested. Specific test results are as follows: Figures 5 to 12 The specific testing method is as follows: Hardness: The microhardness of the cladding layer cross-section was measured using a 200HVS-5 Vickers microhardness tester. A standard Vickers diamond pyramid indenter was used, with a load of 0.5 kg and a loading time of 10 s. Measurements were taken from three directions: the cross-section, the longitudinal section, and the intersection of the weld channels. The specific selection of drilling points is as follows... Figure 9 As shown, the hardness points are spaced approximately 1 mm apart. During the test, the indentation position was adjusted to prevent the diamond indenter from contacting the hard phase particles.

[0057] Wear resistance: For comparative tests, an HK-MS100 high-temperature friction and wear testing machine was used. GCr15 balls with a diameter of 6 mm were selected as the grinding balls. The rotation speed was 300 r / min, the load was 15 N, and the time was 15–50 min. For Examples 1–5, an MS-M9000 dynamic damage and protection testing instrument was used. Reciprocating friction grinding balls were still CGr15 balls, the friction frequency was 5 Hz, the friction length was 5 mm, the load was 15 N, and the time was 15 min. Before and after wear, the mass of the sample was weighed using an electronic balance with an accuracy of 1 mg. Before weighing, the sample was cleaned with anhydrous ethanol, ultrasonically cleaned, and dried.

[0058] Corrosion resistance: Testing and data analysis were performed using a CS310X multichannel electrochemical workstation and CS Studio6 software. A saturated calomel electrode was used as the reference electrode, the coating surface as the working electrode, and a 3.5wt% NaCl aqueous solution was used as the etching solution. The scanning potential range was -0.5V to 0.6V, and the scan rate was 1mV / s.

[0059] like Figure 5 , Figure 7 , Figure 8 As shown, in Comparative Examples 1-4, the hardness and wear resistance of the composite coating fluctuated accordingly with the increase of TiB2 content. The hardness of the composite coating prepared using the technology provided by this invention (Comparative Example 3) is twice that of the substrate, the coefficient of friction is 1.5 times that of the substrate, and the wear amount is 0.07 that of the substrate. Figure 11 and Figure 12 Table 3 shows the impedance and polarization curves of the substrate and the comparative composite coating in a 3.5 wt% NaCl aqueous solution. Table 4 shows the self-corrosion current density and self-corrosion voltage of the substrate and the comparative composite coating in the same solution. A larger impedance radius indicates better corrosion resistance; a more positive self-corrosion voltage indicates a lower thermodynamic tendency for corrosion; and a smaller self-corrosion current density indicates a lower corrosion rate, thus indicating better corrosion resistance. Figure 11 and Figure 12 It can be seen that the corrosion resistance of the composite coating is significantly better than that of the substrate. Among them, Comparative Example 4 has the largest impedance radius, larger self-corrosion voltage, and smaller self-corrosion current density, indicating that the addition of Al2O3 and TiB2 can significantly improve the corrosion resistance of the composite coating.

[0060] Table 3

[0061] Note: Table 3 shows the values ​​of the self-corrosion current density Icorr and self-corrosion voltage Ecorr of the Al2O3-TiB2 dual-phase composite titanium coating and substrate of Comparative Examples 1-4 according to the present invention in 3.5 wt% NaCl aqueous solution.

[0062] like Figure 6 , Figure 9 , Figure 10 As shown, compared to the comparative example, the Al2O3-TiB2 dual-phase composite titanium-based coating prepared in the examples also exhibits a trend of increasing hardness with increasing TiB2 content, but the hardness variation in each group is relatively large. The friction coefficient of the examples is lower than that of the comparative example, but the difference is small compared to the substrate. Among them, Example 3 has the smallest friction wear, with wear amount being 0.12 times that of the substrate.

[0063] The various embodiments of the present invention have been described above. These descriptions are exemplary and not exhaustive, nor are they limited to the disclosed embodiments. Many modifications and variations will be apparent to those skilled in the art without departing from the scope and spirit of the described embodiments.

Claims

1. An Al2O3-TiB2 dual-phase composite titanium-based coating, characterized in that, The raw materials for the Al2O3-TiB2 dual-phase composite titanium-based coating include titanium-based powder, Al2O3 powder, and TiB2 powder. Based on the total weight of the raw materials for the Al2O3-TiB2 dual-phase composite titanium-based coating, the content of TiB2 powder is 25-50 wt%, the content of Al2O3 powder is 15-25 wt%, and the remainder is titanium-based powder.

2. The Al2O3-TiB2 dual-phase composite titanium-based coating according to claim 1, wherein, The titanium-based powder is titanium alloy powder and / or pure titanium powder, and the titanium alloy powder is preferably TC4 powder.

3. A method for preparing an Al2O3-TiB2 dual-phase composite titanium-based coating, characterized in that, Includes the following steps: (1) Obtaining cladding mixed powder: After uniformly mixing titanium-based powder, Al2O3 powder and TiB2 powder, vacuum drying is performed to obtain cladding mixed powder; wherein, based on the total weight of the cladding mixed powder, the content of TiB2 powder is 25-50wt%, the content of Al2O3 powder is 15-25wt%, and the remainder is titanium-based powder. (2) Pretreatment of titanium matrix material: The titanium matrix material is polished, cleaned and dried in sequence; (3) Preparation of dual-phase composite titanium-based coating: The laser cladding process is adopted. Under the protection atmosphere of argon, the cladding mixture powder is laser clad on the surface of the pretreated titanium substrate material by means of binder powder spreading method or synchronous powder feeding method to form Al2O3-TiB2 dual-phase composite titanium-based coating.

4. The method for preparing the Al2O3-TiB2 dual-phase composite titanium-based coating according to claim 3, wherein, In step (1), the mixing is carried out using a ball mill, a pot mill, or a mixer, preferably using a ball mill; Preferably, the ball mill rotates at a speed of 80-120 r / min, the ball-to-material ratio is (1-5):1, and the mixing time is 20-24 hours.

5. The method for preparing the Al2O3-TiB2 dual-phase composite titanium-based coating according to claim 3, wherein, In step (1), the conditions for vacuum drying include: vacuum degree of 0.1-5 Pa, temperature of 80-120℃, and time of 3-4 h.

6. The method for preparing the Al2O3-TiB2 dual-phase composite titanium-based coating according to claim 3, wherein, In step (1), the particle size of the titanium-based powder is 53-106 micrometers; The particle size of the Al2O3 powder is 1-380 micrometers, preferably 180-380 micrometers; The average particle size of the TiB2 powder is 1-80 micrometers, preferably 65-75 micrometers.

7. The method for preparing the Al2O3-TiB2 dual-phase composite titanium-based coating according to claim 3, wherein, In step (2), the titanium matrix material is pure titanium or a titanium alloy, and the titanium alloy is preferably TC4; The polishing was done using 2000-grit sandpaper; the cleaning was done using anhydrous ethanol.

8. The method for preparing the Al2O3-TiB2 dual-phase composite titanium-based coating according to claim 3, wherein, In step (3), the conditions of the laser cladding process include: laser power of 1500-3000W, scanning speed of 13-18mm / s, powder feeding rate of 18-25g / min, powder feeding gas flow rate of 8-10L / min, and overlap rate of 45-55%.

9. The method for preparing the Al2O3-TiB2 dual-phase composite titanium-based coating according to claim 3, wherein, In step (3), the binder used in the binder powdering method is water glass, and the method includes the following steps: After mixing the cladding powder with water glass, the mixture is uniformly applied to the pretreated titanium substrate material. After vacuum drying, laser cladding is performed.

10. The method for preparing the Al2O3-TiB2 dual-phase composite titanium-based coating according to claim 9, wherein, The conditions for the vacuum drying process include: a vacuum degree of 0.1-5 Pa, a temperature of 80-120℃, and a time of 3-4 hours.

Images