CN110760724A - Al-Mg with high Fe content prepared by selective laser melting2Si alloy and preparation method thereof - Google Patents
Al-Mg with high Fe content prepared by selective laser melting2Si alloy and preparation method thereof Download PDFInfo
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Abstract
The invention discloses Al-Mg with high Fe content prepared by selective laser melting2Si alloy and preparation method thereof, and Al-Mg2The Si alloy consists of Al-Mg2Si alloy raw material powder is formed by a selective laser melting technology; the Al-Mg2The Si alloy comprises the following components in percentage by mass: 5-5.5% of Mg, 2-2.2% of Si, 0.4-0.6% of Mn, 1-3% of Fe and the balance of aluminum, wherein the total mass percent is 100%. The invention skillfully utilizes the selective laser melting technology to prepare Al-Mg with high Fe content2The cooling rate of Si alloy in selective laser melting technology can reach 105～108k/s such that the alloyAfter the raw material powder is melted, under the condition of extremely high cooling speed, the alloy is solidified in a non-equilibrium way, the alloy elements are uniformly distributed, all the elements are not segregated, and (Al + Mg) is uniformly formed2Si) ultrafine eutectic structure, simultaneously inhibits the formation of coarse Fe-rich intermetallic compounds, forms fine Fe-rich intermetallic compounds which are uniformly dispersed, and thus obtains Al-Mg with high Fe content and excellent mechanical properties2An Si alloy.
Description
Technical Field
The invention belongs to the technical field of new material preparation, and particularly relates to Al-Mg with high Fe content prepared by selective laser melting2Si alloy and a preparation method thereof.
Background
Mg2Si has good physical and mechanical properties and is widely used as a reinforcing phase for preparing Mg2Si-reinforced aluminum matrix composite (Al-Mg)2Si) or Mg2Si-reinforced magnesium-based composite material (Mg-Mg)2Si) which are attractive candidates for the fields of automotive, aerospace, biomedical, etc. Due to Mg2The compatibility of Si phase and aluminum matrix is good, the interface is clean and firm, the structure is dispersed and distributed on the matrix, and the machinability and the formability of the composite material are enhanced by ceramic particles, so that Mg2Si intermetallic compound is very suitable as reinforcing phase of aluminum-based alloy material, and Al-Mg2The preparation method of the Si alloy material is simple and has low cost. Al-Mg2The Si composite material has high specific strength, high specific modulus, strong abrasion resistance and low production cost, and has wide development space as a light alloy material.
Fe is the most common impurity element in aluminum alloy, and can be accumulated and difficult to eliminate in the recovery and casting processes, along with the inevitable requirement of social sustainable development that the recovery and the reutilization of waste aluminum alloy become, the aluminum alloy with high iron content has an inevitable trend, however, the solubility of Fe in solid aluminum is extremely low (about 0.05 percent at the eutectic temperature), and Fe-rich intermetallic compounds are formed in the solidification process. Fe atoms are precipitated to the front edge of an interface due to strong segregation in the solidification process of the alloy, and even a small amount of Fe can form hard and brittle Fe in the alloyFe-rich phase, especially acicular β -Al5FeSi presents the greatest harm to aluminum alloys. In aluminum alloys, when the Fe content exceeds 0.3%, coarse flaky precipitates are produced, which adversely affect the casting properties, physical properties and mechanical properties of the alloy, and the higher the Fe content, the more harmful the alloy is.
The most basic methods for controlling the content of the iron element in industrial production are a dilution method and a gravity settling method, and methods for reducing the harm of the Fe-rich phase in the aluminum alloy mainly comprise a method for adding a neutralizing element, a method for quickly solidifying and a method for overheating a melt, but the methods all need high cost and support of a new technology and are difficult to popularize in practical application.
Disclosure of Invention
Aiming at the defects of the prior art, the invention aims to provide Al-Mg with high Fe content prepared based on selective laser melting and having excellent mechanical properties2Si alloy and its preparation method, cooling rate up to 10 in selective laser melting technology5～108k/s characteristics, so that the high Fe content Al-Mg2The thick and thick Fe-rich phase in the Si alloy is effectively refined under the condition of large supercooling to obtain the Fe-rich intermetallic compound with fine grains, which not only can eliminate the harmful effect of the needle-shaped phase, but also can form fine grains to play a good role in strengthening relative matrix to play a role in Al-Mg2The positive effect of the Si alloy performance, and in addition, the mechanical property can be further improved through further aging heat treatment.
In order to achieve the purpose, the invention adopts the following technical scheme,
the invention relates to Al-Mg with high Fe content prepared by selective laser melting2Si alloy, said Al-Mg2The Si alloy consists of Al-Mg2Si alloy raw material powder is formed by a selective laser melting technology; the Al-Mg2The Si alloy comprises the following components in percentage by mass: 5-5.5% of Mg, 2-2.2% of Si, 0.4-0.6% of Mn, 1-3% of Fe and the balance of aluminum, wherein the total mass percent is 100%.
In a preferred embodiment, the Al-Mg2The Si alloy consists of Al-Mg2Si alloy raw material powder is formed by a selective laser melting technology and then subjected to aging heat treatmentAnd (5) obtaining the product.
The invention relates to Al-Mg with high Fe content prepared by selective laser melting2The preparation method of the Si alloy comprises the following steps: mixing Al-Mg2Laying Si alloy raw material powder on a substrate of a selective laser melting forming device layer by layer, carrying out layer by layer laser scanning according to a three-dimensional model, and carrying out melting solidification forming to obtain Al-Mg2And in the laser scanning process, controlling the diameter of a light spot to be 0.09-0.12 mm, controlling the laser power to be 270-500W, and controlling the laser scanning speed to be 500-1200 mm/s.
In the preferable scheme, the laser power is 300-350W, and the laser scanning speed is 700-900 mm/s.
In a preferred embodiment, the Al-Mg2The particle size of the Si alloy raw material powder is 10-70 μm. Within the particle size range, the powder has good fluidity and good molding effect, and the powder can be fully melted to obtain a molded part with a smoother surface.
In a preferred embodiment, the Al-Mg2The Si alloy raw material powder is spherical powder which is obtained by using pure aluminum, pure magnesium, aluminum-silicon intermediate alloy, aluminum-manganese intermediate alloy and aluminum-iron intermediate alloy as raw materials and carrying out gas atomization and sieving. The gas atomization process employs the processes described in the prior art.
In the present invention, the material of the substrate is an aluminum alloy.
In a preferred scheme, the substrate is preheated at 100-150 ℃.
In a preferred embodiment, the Al-Mg2The thickness of the single-layer laying of the Si alloy raw material powder is 0.04-0.06 mm.
Preferably, the layer-by-layer laser scanning process is that when the nth layer of laser scanning is performed, the scanning direction rotates clockwise 67 degrees relative to the scanning direction of the (n-1) th layer of laser scanning.
In the preferred scheme, Al-Mg is obtained by melting, solidifying and forming and then carrying out heat treatment2An Si alloy.
Further preferably, the temperature of the heat treatment is 160-180 ℃ and the time is 1-20 h, preferably 3.5 h.
The principle of the invention is as follows:
the selective laser melting technology is a rapid laser forming technology which can lay powder layer by layer and melt and solidify layer by layer, can prepare parts with complex shapes and higher precision, and is additive manufacturing, so that raw materials can be saved to the maximum extent, and the manufacturing cost and time are reduced.
The aluminum alloy formed part of the invention contains high content of Fe and belongs to hypoeutectic Al-Mg2The invention relates to the field of Si alloy, which skillfully utilizes the selective laser melting technology to prepare Al-Mg with high Fe content2The cooling rate of Si alloy in selective laser melting technology can reach 105～108The characteristic of k/s ensures that the alloy raw material powder is non-equilibrium solidified at a very fast cooling speed after being melted, the alloy elements are uniformly distributed, and all the elements are not segregated and uniformly form (Al + Mg)2Si) ultrafine eutectic structure, simultaneously inhibits the formation of coarse Fe-rich intermetallic compounds, forms fine Fe-rich intermetallic compounds which are uniformly dispersed, and thus obtains Al-Mg with high Fe content and excellent mechanical properties2An Si alloy.
The invention has the beneficial effects that:
1) the invention is based on the selective laser melting technology, the alloy is non-equilibrium solidified under the rapid quenching condition, and (Al + Mg) is completely formed2Si) ultrafine eutectic structure, as shown in figure 1, the eutectic reinforced aluminum alloy with high density, high strength and good ductility is obtained. 2) Based on the selective laser melting manufacturing method, the Fe content in the alloy is improved, and Fe-rich intermetallic compounds with fine grains are obtained and are dispersed in the matrix, so that the harmful effect of needle-shaped phases is eliminated, the cracks of the formed part are avoided, and the matrix can be well strengthened. 3) The density of the Al-Mg2Si alloy formed part obtained by the invention is higher than 99%, and the comprehensive mechanical property of the obtained formed part is obviously superior to that of the traditional high-Fe-content cast Al-Mg2Si alloy, Al-Mg with optimized high Fe content obtained by applying selective laser melting technology2The hardness of the Si alloy reaches 195HV, the maximum tensile strength sigma b can reach 570MPa, the yield strength sigma 0.2 can reach 420MPa, and the alloy still keeps about 15 percent of elongation. 4) The inventionThe method has the advantages of simple process, low cost and easy realization of large-scale industrial production, provides a new research idea and solution for recycling the aluminum alloy with high Fe content, and can ensure that the production and recycling of aluminum alloy parts are not limited any more.
Drawings
FIG. 1 shows high Fe optimized Al-Mg prepared in example 22High-magnification SEM image of Si alloy.
FIG. 2 is the high Fe optimized Al-Mg prepared in example 22And (3) a distribution diagram of Si alloy elements.
FIG. 3 is the high Fe optimized Al-Mg prepared in example 22And the tensile fracture morphology of the Si alloy sample.
Detailed Description
The technical solutions in the embodiments of the present invention will be clearly and completely described below, and it is obvious that the described embodiments are only a part of the embodiments of the present invention, rather than all embodiments, and all other embodiments obtained by those skilled in the art without any creative work based on the embodiments of the present invention belong to the protection scope of the present invention.
The invention will be further illustrated with reference to the following specific examples and the accompanying drawings:
in the following examples, Al-Mg was used2The Si alloy raw material powder is gas atomized spherical powder obtained by using pure aluminum, pure magnesium, aluminum-silicon intermediate alloy, aluminum-manganese intermediate alloy and aluminum-iron intermediate alloy as raw materials and performing gas atomization and sieving, and Al-Mg is obtained by sieving2The grain size range of the Si gas atomized spherical powder is 10-70 mu m.
Comparative example 1
Composition and percentage content of aluminum alloy composition
A1-91.6％ Mg-5.5％ Si-2.2％ Mn-0.6％Fe-0.1％
Step two, preparation of aluminum alloy formed part
1) Providing the screened component Al-Mg2Si gas atomization of spherical powder;
2) slicing the CAD model of the part by using slicing software to obtain two-dimensional data of each layer, and transmitting the data to SLM equipment;
3) laying Al-Mg provided in step 1) 0.05mm on a removable aluminum alloy substrate preheated to 100 DEG C2Si alloy powder;
4) laser scanning the cross section of the metal powder layer in the step 3), wherein a laser spot is 0.1mm, the laser power is 310W, and the laser scanning speed is 800mm/s in the scanning process, so that the metal powder layer is melted, solidified and formed, and the laser scanning and forming are carried out under the condition of a sealed Ar atmosphere;
5) lowering the piston of the forming cylinder by the thickness of a powder layer, uniformly laying a second layer of powder by a scraper, scanning the geometric shape of the cross section of the newly laid metal powder layer by laser, rotating the scanning direction and the scanning direction of the previous layer clockwise by 67 degrees in the same step 4), and melting and solidifying to form a second layer;
6) and repeating the step 5) for multiple times until the whole program operation is finished to obtain the aluminum alloy formed part, wherein the repetition times are determined by the size of the formed part.
Third, performance test
The aluminum alloy formed part prepared in the embodiment is tested, and the density of the aluminum alloy formed part is 99.2%, the mechanical property indexes of the aluminum alloy formed part are that the hardness reaches 170HV, the maximum tensile strength sigma b is 520MPa, the yield strength sigma 0.2 is 350MPa, and the elongation is 18%.
Comparative example 2
First, the composition of the aluminum alloy and the percentage content
A1-89.7％ Mg-5.5％ Si-2.2％ Mn-0.6％ Fe-2％
Step two, preparation of aluminum alloy formed part
1) Providing the sieved Al-Mg2Si aerosolized spherical powder of the composition;
2) slicing the CAD model of the part by using slicing software to obtain two-dimensional data of each layer, and transmitting the data to SLM equipment;
3) laying Al-Mg2Si alloy powder provided in step 1) with the thickness of 0.05mm on a detachable aluminum alloy substrate preheated to 100 ℃;
4) laser scanning step 3), wherein the cross section of the metal powder layer is in a geometric shape, a laser spot is 0.1mm in the scanning process, the laser power is 530W, the laser scanning speed is 1800mm/s, so that the metal powder layer is melted, solidified and formed, and the laser scanning and forming are carried out under the condition of a sealed Ar atmosphere;
5) lowering the piston of the forming cylinder by the thickness of a powder layer, uniformly laying a second layer of powder by a scraper, scanning the geometric shape of the cross section of the newly laid metal powder layer by laser, rotating the scanning direction and the scanning direction of the previous layer clockwise by 67 degrees in the same step 4), and melting and solidifying to form a second layer;
6) and repeating the step 5) for multiple times until the whole program operation is finished to obtain the aluminum alloy formed part, wherein the repetition times are determined by the size of the formed part.
Third, performance test
The aluminum alloy formed part prepared in the embodiment is tested, and the density of the aluminum alloy formed part is 93.5%, the mechanical property indexes of the aluminum alloy formed part are that the hardness reaches 107HV, the maximum tensile strength sigma b is 380MPa, the yield strength sigma 0.2 is 293MPa, and the elongation is 3.5%.
Comparative example 3
Composition and content of aluminum alloy composition
A1-89.7％ Mg-5.5％ Si-2.2％ Mn-0.6％ Fe-2％
Step two, preparation of aluminum alloy formed part
1) Providing the sieved Al-Mg2Si aerosolized spherical powder of the composition;
2) slicing the CAD model of the part by using slicing software to obtain two-dimensional data of each layer, and transmitting the data to SLM equipment;
3) laying Al-Mg provided in step 1) 0.05mm on a removable aluminum alloy substrate preheated to 100 DEG C2Si alloy powder;
4) laser scanning the cross section of the metal powder layer in the step 3), wherein a laser spot is 0.1mm, the laser power is 270W, and the laser scanning speed is 500mm/s in the scanning process, so that the metal powder layer is melted, solidified and formed, and the laser scanning and forming are carried out under the condition of a sealed Ar atmosphere;
5) lowering the piston of the forming cylinder by the thickness of a powder layer, uniformly laying a second layer of powder by a scraper, scanning the geometric shape of the cross section of the newly laid metal powder layer by laser, rotating the scanning direction and the scanning direction of the previous layer clockwise by 67 degrees in the same step 4), and melting and solidifying to form a second layer;
6) and repeating the step 5) for multiple times until the whole program operation is finished to obtain the aluminum alloy formed part, wherein the repetition times are determined by the size of the formed part.
Third, performance test
The aluminum alloy formed part prepared in the embodiment is tested, and the density of the aluminum alloy formed part is 95.5%, the mechanical property indexes of the aluminum alloy formed part are that the hardness reaches 125HV, the maximum tensile strength sigma b is 416MPa, the yield strength sigma 0.2 is 330MPa, and the elongation is 6%. The hardness, the maximum tensile strength and the yield strength of the alloy are obviously reduced compared with those of the embodiment 2, the alloy powder is difficult to be completely melted by low laser power, the liquid phase viscosity is increased, the defects of holes and the like are easy to form, and the density of a formed part is not high.
Example 1
Composition and content of aluminum alloy composition
A1-89.7％ Mg-5.5％ Si-2.2％ Mn-0.6％ Fe-2％
Step two, preparation of aluminum alloy formed part
1) Providing the sieved Al-Mg2Si aerosolized spherical powder of the composition;
2) slicing the CAD model of the part by using slicing software to obtain two-dimensional data of each layer, and transmitting the data to SLM equipment;
3) laying Al-Mg provided in step 1) 0.05mm on a removable aluminum alloy substrate preheated to 100 DEG C2Si alloy powder;
4) laser scanning the cross section of the metal powder layer in the step 3), wherein a laser spot is 0.1mm, the laser power is 310W, and the laser scanning speed is 800mm/s in the scanning process, so that the metal powder layer is melted, solidified and formed, and the laser scanning and forming are carried out under the condition of a sealed Ar atmosphere;
5) lowering the piston of the forming cylinder by the thickness of a powder layer, uniformly laying a second layer of powder by a scraper, scanning the geometric shape of the cross section of the newly laid metal powder layer by laser, rotating the scanning direction and the scanning direction of the previous layer clockwise by 67 degrees in the same step 4), and melting and solidifying to form a second layer;
6) and repeating the step 5) for multiple times until the whole program operation is finished to obtain the aluminum alloy formed part, wherein the repetition times are determined by the size of the formed part.
Third, performance test
The aluminum alloy formed part prepared in the embodiment is tested, and the density of the aluminum alloy formed part is 99.1%, the mechanical property indexes of the aluminum alloy formed part are that the hardness reaches 185HV, the maximum tensile strength sigma b is 550MPa, the yield strength sigma 0.2 is 380MPa, and the elongation is 16%. Compared with the comparative example 1, the hardness, the maximum tensile strength and the yield strength of the alloy are all improved, the elongation rate is not obviously reduced, and the performance of the alloy formed part is optimized after the high-content Fe is added.
Example 2
Composition and content of aluminum alloy composition
A1-89.7％ Mg-5.5％ Si-2.2％ Mn-0.6％ Fe-2％
Step two, preparation of aluminum alloy formed part
1) Providing the sieved Al-Mg2Si aerosolized spherical powder of the composition;
2) slicing the CAD model of the part by using slicing software to obtain two-dimensional data of each layer, and transmitting the data to SLM equipment;
3) laying Al-Mg2Si alloy powder provided in step 1) with the thickness of 0.05mm on a detachable aluminum alloy substrate preheated to 100 ℃;
4) laser scanning the cross section of the metal powder layer in the step 3), wherein a laser spot is 0.1mm, the laser power is 310W, and the laser scanning speed is 800mm/s in the scanning process, so that the metal powder layer is melted, solidified and formed, and the laser scanning and forming are carried out under the condition of a sealed Ar atmosphere;
5) lowering the piston of the forming cylinder by the thickness of a powder layer, uniformly laying a second layer of powder by a scraper, scanning the geometric shape of the cross section of the newly laid metal powder layer by laser, rotating the scanning direction and the scanning direction of the previous layer clockwise by 67 degrees in the same step 4), and melting and solidifying to form a second layer;
6) and repeating the step 5) for multiple times until the whole program operation is finished to obtain the aluminum alloy formed part, wherein the repetition times are determined by the size of the formed part.
7) And (3) carrying out heat treatment on the aluminum alloy formed part obtained in the step 6) at 170 ℃ for 3.5h to obtain the aluminum alloy formed part by the selective laser melting technology.
Third, performance test
The microstructure and element distribution of the aluminum alloy molded part prepared in this example were examined and fracture characteristics thereof were observed. As can be seen in fig. 1: the texture structure of the alloy is an ultrafine lamellar eutectic structure, wherein the gray black phase is Mg2Si, grey-white phase Al matrix, grey-black Mg2The Si phase and the grey-white Al phase form a lamellar superfine eutectic structure, fine Fe-rich intermetallic compounds are uniformly dispersed and distributed in the matrix, and the fineness of the Fe-rich intermetallic compounds cannot be observed under a scanning electron microscope. In FIG. 2, the elements are uniformly distributed and have no segregation phenomenon. The tensile fracture of FIG. 3 shows a large number of dimples, and the alloy fractures as ductile fractures.
The aluminum alloy formed part prepared in the embodiment is tested, and the compactness of the aluminum alloy formed part is 99.1%, the mechanical property index of the aluminum alloy formed part is as follows, the maximum tensile strength sigma b can reach 580MPa, the yield strength sigma 0.2 can reach 420MPa, and the alloy still keeps a large percentage elongation of about 15.7. The hardness, the maximum tensile strength and the yield strength are better than those of the example 1, and the elongation rate is not changed greatly.
The Mg2Si reinforced phase of the aluminum alloy formed part with the optimized high Fe content is subjected to short-time low-temperature heat treatment, fine Fe-rich intermetallic compounds are uniformly dispersed, and the alloy performance is improved under the dual effects of precipitation strengthening and solid solution strengthening.
Claims (10)
1. Al-Mg with high Fe content prepared by selective laser melting2An Si alloy characterized by: the Al-Mg2The Si alloy consists of Al-Mg2Si alloy raw material powder is formed by a selective laser melting technology; the Al-Mg2The Si alloy comprises the following components in percentage by mass: 5-5.5% of Mg, 2-2.2% of Si, 0.4-0.6% of Mn, 1-3% of Fe and the balance of aluminumThe ratio was 100%.
2. The Al-Mg with high Fe content prepared by selective laser melting according to claim 12An Si alloy characterized by: the Al-Mg2The Si alloy consists of Al-Mg2The Si alloy raw material powder is formed by a selective laser melting technology and then subjected to aging heat treatment to obtain the Si alloy powder.
3. Preparation of Al-Mg according to claims 1-22A method of Si alloy, characterized by: the method comprises the following steps: mixing Al-Mg2Laying Si alloy raw material powder on a substrate of a selective laser melting forming device layer by layer, carrying out layer by layer laser scanning according to a three-dimensional model, and carrying out melting solidification forming to obtain Al-Mg2And in the laser scanning process, controlling the diameter of a light spot to be 0.09-0.12 mm, controlling the laser power to be 270-500W, and controlling the laser scanning speed to be 500-1200 mm/s.
4. The production method according to claim 3, characterized in that: the laser power is 300-350W, and the laser scanning speed is 700-900 mm/s.
5. The production method according to claim 3, characterized in that: the Al-Mg2The particle size of the Si alloy raw material powder is 10-70 μm.
6. The production method according to claim 3, characterized in that: the substrate is preheated at 100-150 ℃.
7. The production method according to claim 3, characterized in that: the Al-Mg2The thickness of the single-layer laying of the Si alloy raw material powder is 0.04-0.06 mm.
8. The production method according to claim 3, characterized in that: the layer-by-layer laser scanning process is that when the nth layer of laser scanning is carried out, the scanning direction rotates 67 degrees clockwise relative to the scanning direction of the (n-1) th layer of laser.
9. The production method according to claim 3, characterized in that: after melting, solidifying and forming, carrying out heat treatment to obtain Al-Mg2An Si alloy.
10. The method of claim 9, wherein: the temperature of the heat treatment is 160-180 ℃, and the time is 1-20 h.
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| CN111673085A (en) * | 2020-06-30 | 2020-09-18 | 同济大学 | 3D printing process method of high-strength aluminum-magnesium-silicon alloy |
| CN111842914A (en) * | 2020-06-30 | 2020-10-30 | 同济大学 | 3D printing process method of high-strength aluminum-copper alloy |
| CN112775440A (en) * | 2020-12-24 | 2021-05-11 | 上海交通大学 | Selective laser melting aluminum alloy and additive manufacturing method |
| CN114592148A (en) * | 2022-03-11 | 2022-06-07 | 中南大学 | High-strength and high-toughness Al-Mg for additive manufacturing2Si-Zn alloy and preparation method and application thereof |
| CN115747584A (en) * | 2022-11-11 | 2023-03-07 | 中南大学 | Crack-free reinforced Al-Mg 2 Si-Si alloy material and preparation method and application thereof |
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| CN108330344A (en) * | 2018-03-20 | 2018-07-27 | 中南大学 | A kind of 3D printing 7xxx aluminium alloys and preparation method thereof |
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Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
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| CN111673085A (en) * | 2020-06-30 | 2020-09-18 | 同济大学 | 3D printing process method of high-strength aluminum-magnesium-silicon alloy |
| CN111842914A (en) * | 2020-06-30 | 2020-10-30 | 同济大学 | 3D printing process method of high-strength aluminum-copper alloy |
| CN112775440A (en) * | 2020-12-24 | 2021-05-11 | 上海交通大学 | Selective laser melting aluminum alloy and additive manufacturing method |
| CN114592148A (en) * | 2022-03-11 | 2022-06-07 | 中南大学 | High-strength and high-toughness Al-Mg for additive manufacturing2Si-Zn alloy and preparation method and application thereof |
| CN115747584A (en) * | 2022-11-11 | 2023-03-07 | 中南大学 | Crack-free reinforced Al-Mg 2 Si-Si alloy material and preparation method and application thereof |
| CN115747584B (en) * | 2022-11-11 | 2023-11-17 | 中南大学 | Crack-free reinforced Al-Mg 2 Si-Si alloy material, preparation method and application thereof |
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