Reb6 reinforced AlSi10Mg alloy composite material and preparation method thereof

Abstract

The application discloses a kind of ReB6 Enhanced AlSi10Mg Alloy Composite and preparation method thereof, micron grade ReB6 Alloy powder is obtained after once over sieve, add anhydrous ethanol, ultrasonic dispersion, dry, pass 1200-2000 mesh sieve, take undersize, obtain secondary sieving powder, mix secondary sieving powder with spherical AlSi10Mg Alloy powder in table double movement dry powder mixing machine to obtain mixed powder, the mixed powder is selected laser melting forming, and ReB6 Enhanced AlSi10Mg Alloy Composite is obtained.The preparation method of the application, by making ReB6 Alloy powder in mixed powder adsorbed or wrapped in AlSi10Mg particle surface, effectively avoids the reflectivity of laser, reduces the surface tension of molten pool metal, improves the fluidity of molten pool, so as to print and obtain high density, high quality ReB6 Enhanced AlSi10Mg Alloy Composite.

Description

Technical Field

[0001] This invention belongs to the field of aluminum-based composite material preparation technology, specifically relating to a ReB6-reinforced AlSi10Mg alloy composite material and its preparation method. Background Technology

[0002] AlSi10Mg alloys possess high specific strength, low density, and corrosion resistance, making them widely used in aerospace, automotive manufacturing, and other fields. However, traditional manufacturing methods are prone to metallurgical defects such as porosity and cracks during the forming process, and are difficult to adapt to the processing of complex-shaped components, affecting component performance and reliability. This contradicts current policies advocating for advanced intelligent manufacturing and green, low-carbon manufacturing to achieve industrial upgrading and transformation. With the rapid development of laser additive manufacturing technology, new solutions are emerging for traditional manufacturing industries. Laser additive manufacturing of aluminum alloys can significantly improve the efficiency of complex component fabrication and reduce post-processing costs, having a significant impact on the manufacturing of lightweight, high-performance, complex parts in aerospace, aviation, and automotive industries.

[0003] However, aluminum exhibits extremely high reflectivity (over 90%) to commonly used infrared wavelengths (such as 1064nm) in both its solid and liquid states. This means that most of the laser energy is reflected rather than absorbed, requiring higher laser power to initiate and maintain melting, resulting in low melting efficiency and unstable processes. Furthermore, AlSi10Mg alloys are prone to vaporization under high laser energy density processes, generating metal vapor back pressure that forms keyholes. In addition, accompanied by Marangoni convection, the molten pool surface experiences strong fluctuations, making it difficult for metal vapors to escape during solidification, thus forming keyholes, reducing the density of the printed parts, and consequently affecting mechanical properties. Summary of the Invention

[0004] To address the shortcomings of existing technologies, the first objective of this invention is to provide a method for preparing ReB6-reinforced AlSi10Mg alloy composite materials. This method is simple, controllable, and suitable for industrial production.

[0005] The second objective of this invention is to provide a ReB6-reinforced AlSi10Mg alloy composite material prepared by the above-described preparation method.

[0006] To achieve the above objectives, the present invention adopts the following technical solution:

[0007] This invention discloses a method for preparing ReB6-reinforced AlSi10Mg alloy composite material. The method involves sieving micron-sized ReB6 alloy powder once, adding the undersize to anhydrous ethanol, ultrasonically dispersing, drying, and then sieving through a 1200-2000 mesh sieve to obtain a second-sieved powder. This second-sieved powder is then mixed with spherical AlSi10Mg alloy powder in a benchtop dual-motion dry powder mixer to obtain a mixed powder. Finally, the mixed powder is subjected to selective laser melting to form the ReB6-reinforced AlSi10Mg alloy composite material.

[0008] During the mixing process, the rotation speed of the material cylinder is controlled at 20 rpm to 25 rpm, and the rotation speed of the blades is controlled at 40 rpm to 50 rpm; the mixing time is 1 to 2 hours.

[0009] The particle size of the AlSi10Mg alloy powder is ≥16μm;

[0010] In the ReB6-reinforced AlSi10Mg alloy composite material, the mass fraction of ReB6 is 1 wt.% to 3 wt.%.

[0011] The preparation method of this invention involves first sieving micron-sized ReB6 alloy powder once, then adding it to anhydrous ethanol and ultrasonically dispersing it. Anhydrous ethanol serves as a liquid medium to separate the agglomerated ReB6 powder. Secondly, as a volatile substance, anhydrous ethanol can remove some of the heat generated during the ultrasonic separation process, preventing localized overheating of the powder and thus obtaining fully dispersed ReB6 alloy powder. Then, the ReB6 alloy powder, after a second sieving, is mixed with AlSi10Mg alloy powder in a benchtop dual-motion dry powder mixer. This allows the second-sieved ReB6 alloy powder to firmly adsorb or coat the surface of the AlSi10Mg particles, improving interfacial wettability and increasing... The surface roughness and micro-unevenness of AlSi10Mg particles effectively avoid laser reflectivity and enable molding at lower laser energy densities. Furthermore, the addition of ReB6 alloy powder effectively reduces the surface tension of the molten pool, improves the fluidity of the molten pool, and reduces the number of keyholes, thereby printing high-density, high-quality ReB6-reinforced AlSi10Mg alloy composites. Due to the extremely high hardness of ReB6 particles, dislocations are difficult to cut through the particles and instead bypass the particles through the Orowan mechanism, forming dislocation loops. Therefore, through the synergy of the above-mentioned aspects, the mechanical properties of ReB6-reinforced AlSi10Mg alloy composites are significantly improved.

[0012] In this invention, to obtain a composite material with excellent comprehensive properties through selective laser melting, it is crucial to ensure that ReB6 alloy powder is firmly adsorbed or coated onto the surface of AlSi10Mg particles. This requires first passing the micron-sized powder through a relatively coarser sieve, then fully dispersing it in anhydrous ethanol, and finally passing it through a relatively finer sieve to obtain ReB6 alloy powder that is even finer and more dispersed than AlSi10Mg alloy powder. Experiments have shown that because ReB6 is micron-sized, there may be some satellite powder particles or slightly larger lumps adsorbed together due to electrostatics or van der Waals forces. The two-step sieving process not only ensures the fineness of the powder but also... The sieve serves a protective function, preventing clogging and allowing for a smaller particle size distribution, facilitating subsequent uniform powder mixing. Secondly, only by using a benchtop dual-motion dry powder mixer to mix ReB6 alloy powder and AlSi10Mg alloy powder and controlling the process parameters within the range of this invention can the ReB6 alloy powder be completely adsorbed or coated on the surface of AlSi10Mg, avoiding deformation and oxidation of the AlSi10Mg powder. If ball milling or other mixing methods are used, ball milling will not only fail to ensure that the ReB6 alloy powder is adsorbed or coated on the surface of AlSi10Mg, but will also result in deformation and oxidation.

[0013] In a preferred embodiment, the ReB6 in the ReB6 alloy powder is CeB6. Experiments have shown that when ReB6 is selected from CeB6, the additive composite material exhibits the highest stability due to its excellent thermodynamic stability at high temperatures, effectively improving the high-temperature stability of the AlSi10Mg alloy.

[0014] In a preferred embodiment, the ReB6 alloy powder is spherical.

[0015] The preferred method involves sieving the micron-sized ReB6 alloy powder through a 300-500 mesh sieve. Experiments revealed that micron-sized raw materials are essential for sieving. Using nano-sized ReB6, due to its high surface energy, leads to agglomeration, preventing the mixed ReB6 alloy powder from firmly adsorbing or coating the AlSi10Mg particles. Furthermore, it causes stress concentration and cracking during printing.

[0016] In a preferred embodiment, the undersize material obtained after sieving micron-sized ReB6 alloy powder once is added to anhydrous ethanol, ultrasonically dispersed for 5-10 minutes, and then dried under vacuum at 60℃-80℃ for 1-3 hours.

[0017] In a preferred embodiment, the AlSi10Mg alloy powder has the following composition by mass percentage: Si 9~11 wt.%, Mg 0.2~0.5 wt.%, Zn≤0.02 wt.%, Ti≤0.15 wt.%, Mg≤0.4 wt.%, Fe≤0.25 wt.%, with the balance being Al and other unavoidable impurities.

[0018] In this invention, the unavoidable impurity content in the AlSi10Mg alloy powder is ≤0.15 wt.%.

[0019] In a preferred embodiment, the particle size of the AlSi10Mg alloy powder is 16 μm to 60 μm. Controlling the particle size of the AlSi10Mg alloy powder within this range results in the final composite material with optimal performance.

[0020] In a preferred embodiment, the mixing is carried out under a protective atmosphere, and the oxygen content is controlled to be below 100 ppm during the mixing process.

[0021] In a preferred embodiment, during the selective laser melting forming, an Al-Si alloy substrate is used. The Al-Si alloy substrate is first preheated to 120°C to 150°C, and then, under a protective atmosphere, the mixed powder is laid on the Al-Si alloy substrate by the cooperation of a powder spreading cart and a scraper. The thickness of the first layer of powder is controlled to be 25 to 50 μm, preferably 28 μm to 32 μm.

[0022] In a further preferred embodiment, the protective atmosphere is argon.

[0023] In a preferred embodiment, the forming pressure during selective laser melting is 5-10 kPa, and the oxygen content in the forming chamber is less than 100 ppm.

[0024] In a preferred embodiment, the process parameters for selective laser melting forming are as follows: laser power 225W~300W, scanning speed 1500mm / s~2250mm / s, scanning spacing 0.8mm~1.2mm, powder layer thickness 28μm~32μm, and laser energy density controlled at 33~67J / mm². 3 .

[0025] In this invention, since CeB6 is adsorbed onto AlSi10Mg powder, the reflectivity is improved, so excellent forming effect can be obtained at a lower laser power. Of course, the laser power cannot be too low, otherwise more internal defects will be formed.

[0026] Further optimizations include a laser power of 250W–300W, a scanning speed of 1800mm / s–2200mm / s, a scanning spacing of 0.8mm–1.2mm, a powder layer thickness of 28μm–32μm, and a laser energy density controlled between 40 and 67J / mm². 3 By synergistically adjusting various process parameters, a suitable laser energy density is obtained, thereby producing a high-density, defect-free ReB6-reinforced AlSi10Mg alloy composite material.

[0027] In a preferred embodiment, during the selective laser melting and forming process, the laser scanning direction is rotated by 61 to 67°, preferably 67°, during the printing process between each adjacent layer.

[0028] The present invention also provides a ReB6-reinforced AlSi10Mg alloy composite material prepared by the above preparation method.

[0029] In a preferred embodiment, the ReB6-reinforced AlSi10Mg alloy composite material has a density of 98.88%–99.39% and a tensile strength of 470 MPa–545 MPa.

[0030] Principles and advantages

[0031] The preparation method of this invention involves first sieving micron-sized ReB6 alloy powder once, then adding it to anhydrous ethanol and ultrasonically dispersing it. Anhydrous ethanol serves as a liquid medium to separate the agglomerated ReB6 powder. Secondly, as a volatile substance, anhydrous ethanol can remove some of the heat generated during the ultrasonic separation process, preventing localized overheating of the powder and thus obtaining fully dispersed ReB6 alloy powder. Then, the ReB6 alloy powder, after a second sieving, is mixed with AlSi10Mg alloy powder in a benchtop dual-motion dry powder mixer. This allows the second-sieved ReB6 alloy powder to firmly adsorb or coat the surface of the AlSi10Mg particles, improving interfacial wettability and increasing... The surface roughness and micro-unevenness of AlSi10Mg particles effectively avoid laser reflectivity and enable molding at lower laser energy densities. Furthermore, the addition of ReB6 alloy powder effectively reduces the surface tension of the molten pool, improves the fluidity of the molten pool, and reduces the number of keyholes, thereby printing high-density, high-quality ReB6-reinforced AlSi10Mg alloy composites. Due to the extremely high hardness of ReB6 particles, dislocations are difficult to cut through the particles and instead bypass the particles through the Orowan mechanism, forming dislocation loops. Therefore, through the synergy of the above-mentioned aspects, the mechanical properties of ReB6-reinforced AlSi10Mg alloy composites are significantly improved. Attached Figure Description

[0032] Figure 1The images show the microstructure of the alloy powder in Example 1 of the present invention, where (a) is the microstructure of the AlSi10Mg alloy powder used in Example 1, and (b) is the microstructure of the AlSi10Mg / 1wt.%CeB6 composite alloy powder.

[0033] Figure 2 The density of the alloy materials prepared in the embodiments and comparative examples of the present invention is shown.

[0034] Figure 3 The tensile test properties of the alloy materials prepared in the embodiments and comparative examples of the present invention are shown.

[0035] Figure 4 The fracture morphology is shown for the alloy material prepared in Example 1.

[0036] Figure 5 The fracture morphology is shown for the alloy material prepared in Example 2.

[0037] Figure 6 The fracture morphology is shown for the alloy material prepared in Comparative Example 1.

[0038] Figure 7 The fracture morphology is shown for the alloy material prepared in Comparative Example 2.

[0039] Figure 8 The fracture morphology is shown for the alloy material prepared in Comparative Example 3. Detailed Implementation

[0040] The present invention will be further described in detail below through specific embodiments. Unless otherwise specified, the raw materials, reagents, or apparatus used in the embodiments and comparative examples are all available from conventional commercial sources or can be obtained by existing technical methods. Unless otherwise specified, the test or experimental methods are conventional methods in the art.

[0041] Example 1

[0042] Spherical, micron-sized ReB6 powder was sieved through a 500-mesh sieve. The undersize was collected and mixed with anhydrous ethanol in a beaker, then placed in an ultrasonic cleaner and shaken for 5 minutes. The shaken powder was then placed in a constant-temperature vacuum drying oven at 80℃ for 2 hours, maintaining a vacuum throughout the drying process. After drying, the powder was sieved through a 1250-mesh sieve. The undersize was collected to obtain a second-sieved powder. This second-sieved powder was then mixed with spherical AlSi10Mg alloy powder with a particle size of 35μm using a benchtop dual-motion dry powder mixer (model: JHT10) under a nitrogen atmosphere. The cylinder rotation speed was 22 rpm, the blade rotation speed was 50 rpm, and the mixing time was 2 hours, yielding an AlSi10Mg / 1wt.%CeB6 composite metal powder. In this AlSi10Mg / 1wt.%CeB6 composite metal powder, the mass fraction of CeB6 powder was 1 wt.%, and the mass fraction of AlSi10Mg alloy powder was 99 wt.%.

[0043] Subsequently, after the Al-Si substrate is heated to 150°C, AlSi10Mg / 1wt.%CeB6 composite metal powder is spread evenly on the substrate to form an alloy powder layer of uniform thickness.

[0044] The target part is geometrically modeled using the 3D solid modeling software Solidworks. The model data is then imported into Magics software in STL format. The 3D solid geometric model is then sliced. The sliced ​​CLI file is saved and imported into the selective laser melting equipment. The powder is then manually scraped from the powder cylinder onto the forming substrate in a uniform 30μm layer thickness using a scraper.

[0045] In the printing process of this embodiment, pre-printing preparations are also required. To ensure printing quality, the sandblasted substrate is cleaned and wiped with alcohol before printing. The powder cylinder, scraper, and other parts are cleaned, and the galvanometer is wiped with lint-free paper. After wiping, the chamber door is closed, and inert gas (Ar) is introduced into the forming chamber. The laser scanning strategy is set as 67° rotation printing, and the laser process parameters are as follows: laser power 250W, scanning speed 2000mm / s, scanning spacing 1mm, powder thickness 30μm, and energy density 41.66J / mm². 3 Once the pressure inside the forming chamber is maintained at 5 kPa and the oxygen content is below 100 ppm, the laser is enabled, and the laser beam scans and prints layer by layer according to the model slicing path, eventually accumulating to obtain the sample.

[0046] In this embodiment, the substrate of the molding chamber is an Al-Si alloy plate.

[0047] In this embodiment, the AlSi10Mg alloy is composed of the following components by mass percentage: Si: 10 wt.%, Mg: 0.5 wt.%, Zn: 0.02 wt.%, Ti: 0.15 wt.%, Fe: 0.25 wt.%, unavoidable impurities 0.15 wt%, balance Al.

[0048] In this embodiment, CeB6 is composed of the following components by mass percentage: B: 31.37 wt.%; Ce: 68.13 wt.%; and other unavoidable impurities: 0.5 wt.%.

[0049] Example 2

[0050] The specific process for preparing AlSi10Mg alloy additive manufacturing in this embodiment is as follows:

[0051] Spherical, micron-sized ReB6 powder was sieved through a 400-mesh sieve. The undersize was collected and mixed with anhydrous ethanol in a beaker, then placed in an ultrasonic cleaner and shaken for 5 minutes. The shaken powder was then placed in a constant temperature vacuum drying oven for drying at 80°C for 2 hours, maintaining a vacuum during the drying process. After drying, the powder was sieved through an 1800-mesh sieve. The undersize was collected to obtain a second-sieved powder. This second-sieved powder was then mixed with spherical AlSi10Mg alloy powder with a particle size of 35 μm using a benchtop dual-motion dry powder mixer (model: JHT10) under a nitrogen atmosphere. The barrel rotation speed was 25 rpm, the blade rotation speed was 40 rpm, and the mixing time was 2 hours to obtain AlSi10Mg / 1wt.%CeB6 composite metal powder.

[0052] Subsequently, after the Al-Si substrate is heated to 150°C, AlSi10Mg composite metal powder is spread evenly on the substrate to form an alloy powder layer of uniform thickness.

[0053] The target part is geometrically modeled using the 3D solid modeling software Solidworks. The model data is then imported into Magics software in STL format. The 3D solid geometric model is then sliced. The sliced ​​CLI file is saved and imported into the selective laser melting equipment. The powder is then manually scraped from the powder cylinder onto the forming substrate in a uniform 30μm layer thickness using a scraper.

[0054] In the printing process of this embodiment, pre-printing preparations are also required. To ensure printing quality, the sandblasted substrate is cleaned and wiped with alcohol before printing. The powder cylinder, scraper, and other parts are cleaned, and the galvanometer is wiped with lint-free paper. After wiping, the chamber door is closed, and inert gas (Ar) is introduced into the forming chamber. The laser scanning strategy is set as follows: 67° rotational printing. Laser process parameters are: laser power 225W, scanning speed 2250mm / s, scanning spacing 1mm, powder thickness 30μm, and energy density 33.33J / cm². 3 Once the pressure inside the forming chamber is maintained at 5 kPa and the oxygen content is below 100 ppm, the laser is enabled, and the laser beam scans and prints layer by layer according to the model slicing path, eventually accumulating to obtain the sample.

[0055] In this embodiment, the substrate of the molding chamber is an Al-Si alloy plate.

[0056] In this embodiment, the AlSi10Mg alloy is composed of the following components by mass percentage: Si: 10 wt.%, Mg: 0.5 wt.%, Zn: 0.02 wt.%, Ti: 0.15 wt.%, Fe: 0.25 wt.%, unavoidable impurities 0.15 wt%, balance Al.

[0057] Comparative Example 1

[0058] All other conditions were the same as in Example 1, except that the material mixing method was ball milling. The ball-to-material ratio was 6:1, the ball milling speed was 300 r / min, and the ball milling time was 2 h.

[0059] It was discovered that ReB6 alloy powder could not be effectively adsorbed or coated on the AlSi10Mg surface, and deformation and oxidation occurred, which was not conducive to subsequent additive manufacturing and affected the improvement of its mechanical properties.

[0060] Comparative Example 2

[0061] Other conditions were the same as in Example 1, except that the powder was sieved through a 500-mesh screen once. This resulted in uneven particle size in the additively prepared powder, which was detrimental to improving density and mechanical properties.

[0062] Comparative Example 3

[0063] Other conditions were the same as in Example 1, except that CeB6 was not added, and AlSi10Mg alloy powder was directly additively prepared. Due to the absence of CeB6 particles, it was difficult to increase the surface roughness and micro-unevenness of the AlSi10Mg particles, reduce the reflection of laser light by AlSi10Mg / 1wt.%CeB6, and improve energy utilization. This also easily led to the formation of a large number of keyholes under the same energy density conditions, which is a significant reason for the insufficient mechanical properties of the stretched parts.

[0064] Performance testing

[0065] 1. The morphology of the AlSi10Mg alloy powder and the AlSi10Mg / 1wt.%CeB6 composite alloy powder in Example 1 was examined using a scanning electron microscope (EVO MA10), as shown in the figure. Figure 1 (a) in the example refers to the AlSi10Mg alloy powder used in the example. Figure 1 The microstructure of (b) AlSi10Mg / 1wt.%CeB6 composite alloy powder.

[0066] from Figure 1 As can be seen in (a) above, the AlSi10Mg alloy powder is spherical. Figure 1 As can be seen from (b), after being sieved twice and mixed by the dual-motion dry powder mixer, the alloy powder still maintains a spherical shape and the CeB6 powder particles completely adsorb or encapsulate the AlSi10Mg spherical particles. This increases the surface roughness and micro-unevenness of the AlSi10Mg particles, reduces the reflection of laser light by AlSi10Mg / 1wt.%CeB6, improves energy utilization, increases the stability of the molten pool, reduces spatter and keyholes, thereby improving the mechanical properties.

[0067] 2. Measurement of printed sample density:

[0068] The Archimedes displacement method was used to determine the sample density: The sample was dried, and its dry weight in air was measured three times (recorded as m1). The sample was then placed in a beaker of deionized water on a heating plate and boiled for 2 hours. After cooling to room temperature, the sample was removed and placed in a weighing net to measure its wet weight after saturation with water, recorded three times (recorded as m2). A paper towel soaked in deionized water was used to dry the sample until no obvious water droplets remained. The sample was then placed back in the weighing net and its weight in air after saturation with water was measured (recorded as m3), recorded three times. The measured density is as follows: Figure 2 As shown.

[0069] Figure 2 The density of the examples and comparative examples is as follows: Example 1 has a density of 99.39%, Example 2 has a density of 98.88%, Comparative Example 1 has a density of 98.76%, Comparative Example 2 has a density of 97.55%, and Comparative Example 3 has a density of 97.66%. The addition of CeB6 improved the sample density, while insufficient energy density would reduce the density.

[0070] 3. Tensile property test:

[0071] The specimens from each embodiment and comparative example were fixed onto an electronic universal testing machine (WDW-100C) and subjected to tensile tests at room temperature. After tensile testing, the fracture surface was wrapped with plastic wrap. The tensile strength was as follows: Figure 3As shown.

[0072] Combination Figures 4-8 The fracture morphology diagrams show that the density differences are caused by several factors: AlSi10Mg alloys are prone to vaporization under high laser energy density processes, generating metal vapor back pressure that forms keyholes. Additionally, the presence of Marangoni convection causes strong fluctuations in the molten pool surface, making it difficult for metal vapor to escape during solidification, thus forming keyholes and reducing the density of the printed part, thereby affecting its mechanical properties. The addition of ReB6 reduces the surface tension of the molten pool metal, improves the fluidity of the molten pool, and reduces the number of keyholes, thereby improving the density and mechanical properties of the sample.

[0073] Figure 3 The tensile strengths of the examples and comparative examples are as follows: Example 1 has a tensile strength of 545 MPa, Example 2 has a tensile strength of 472 MPa, Comparative Example 1 has a tensile strength of 454 MPa, Comparative Example 2 has a tensile strength of 443 MPa, and Comparative Example 3 has a tensile strength of 430 MPa. This indicates that the AlSi10Mg-CeB6 alloy of the present invention can improve the strength of the AlSi10Mg alloy.

[0074] Combination Figures 4-8 The fracture morphology of Example 1 shows a typical river-like pattern, while Example 2 has a lower laser energy density than Example 1, thus failing to completely melt the high-melting-point CeB6 particles. Therefore, both the density and mechanical properties are lower than those of Example 1. In Comparative Example 1, the ball milling of the powder destroys the original spherical powder morphology, preventing CeB6 powder particles from completely adsorbing or encapsulating AlSi10Mg spherical particles, reducing reflection, affecting the flowability of the powder printing process, and forming a large number of keyholes, resulting in reduced density and tensile strength. In Comparative Example 2, after only one screening, the powder particles are of varying sizes, leading to an increase in the number of unmelted large particles during the additive manufacturing process. In Comparative Example 3, due to the absence of CeB6 particles, it is difficult to increase the surface roughness and micro-unevenness of AlSi10Mg particles, reduce the reflection of AlSi10Mg / 1wt.%CeB6 to the laser, and improve energy utilization. However, it is easy to generate a large number of keyholes under the same energy density conditions, which results in insufficient mechanical properties of the stretched part.

[0075] Impact on mechanical properties: Insufficient energy density leads to incomplete fusion becoming the dominant process; excessive energy input is prone to keyholes, both of which reduce the tensile strength of the sample.

[0076] The above embodiments are preferred embodiments of the present invention, but the embodiments of the present invention are not limited to the above embodiments. Any changes, modifications, substitutions, combinations, or simplifications made without departing from the spirit and principle of the present invention shall be considered equivalent substitutions and shall be included within the protection scope of the present invention.

Claims

1. A method for preparing a ReB6-reinforced AlSi10Mg alloy composite material, characterized in that: The undersize material obtained after the first sieving of micron-sized ReB6 alloy powder is added to anhydrous ethanol and ultrasonically dispersed for 5-10 minutes. Then, it is dried under vacuum at 60℃-80℃ for 1-3 hours. After drying, it is passed through a 1200-2000 mesh sieve, and the undersize material is collected to obtain a second-sieved powder. The second-sieved powder is mixed with spherical AlSi10Mg alloy powder in a benchtop dual-motion dry powder mixer to obtain a mixed powder. The mixed powder is then subjected to selective laser melting to form the ReB6-reinforced AlSi10Mg alloy composite material. When the micron-sized ReB6 alloy powder is sieved for the first time, a 300-500 mesh sieve is used. During the mixing process, the rotation speed of the material cylinder is controlled at 20 rpm to 25 rpm, and the rotation speed of the blades is controlled at 40 rpm to 50 rpm; the mixing time is 1 to 2 hours. The particle size of the AlSi10Mg alloy powder is ≥16μm; In the mixed powder, the ReB6 alloy powder is completely adsorbed or coated on the surface of AlSi10Mg; The process parameters for selective laser melting forming are as follows: laser power 225W~300W, scanning speed 1500mm / s~2250mm / s, scanning spacing 0.8mm~1.2mm, powder layer thickness 28μm~32μm, and laser energy density controlled at 33~67J / mm². 3 ; In the ReB6-reinforced AlSi10Mg alloy composite material, the mass fraction of ReB6 is 1 wt.% to 3 wt.%.

2. The method for preparing a ReB6-reinforced AlSi10Mg alloy composite material according to claim 1, characterized in that: The ReB6 in the ReB6 alloy powder is CeB6; The ReB6 alloy powder is spherical.

3. The method for preparing a ReB6-reinforced AlSi10Mg alloy composite material according to claim 1, characterized in that: The AlSi10Mg alloy powder has the following composition by mass percentage: Si 9~11 wt.%, Mg 0.2~0.5 wt.%, Zn≤0.02 wt.%, Ti≤0.15 wt.%, Mg≤0.4 wt.%, Fe≤0.25 wt.%, with the balance being Al and other unavoidable impurities; The particle size of the AlSi10Mg alloy powder is 16μm to 60μm.

4. The method for preparing a ReB6-reinforced AlSi10Mg alloy composite material according to claim 1, characterized in that: The mixing is carried out under a protective atmosphere, and the oxygen content is controlled to be below 100 ppm during the mixing process.

5. The method for preparing a ReB6-reinforced AlSi10Mg alloy composite material according to claim 1, characterized in that: During the selective laser melting forming process, an Al-Si alloy substrate is used. The Al-Si alloy substrate is first preheated to 120℃~150℃, and then, under a protective atmosphere, the mixed powder is laid on the Al-Si alloy substrate by the cooperation of a powder spreading cart and a scraper, and the thickness of the first layer of powder is controlled to be 25~50μm. During the selective laser melting and forming process, the pressure in the forming chamber is controlled at 5~10 kPa; the oxygen content in the forming chamber is less than 100 ppm.

6. The method for preparing a ReB6-reinforced AlSi10Mg alloy composite material according to claim 1, characterized in that: During the selected area laser melting and forming process, the laser scanning direction rotates by 61 to 67 degrees during the printing process between each adjacent layer.

7. The ReB6-reinforced AlSi10Mg alloy composite material prepared by the preparation method of any one of claims 1-6, characterized in that: The ReB6-reinforced AlSi10Mg alloy composite material has a density of 98.88%–99.39% and a tensile strength of 470 MPa–545 MPa.

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