CN117778830A - Quasicrystal reinforced toughness high-strength aluminum alloy material and preparation method thereof - Google Patents
Quasicrystal reinforced toughness high-strength aluminum alloy material and preparation method thereof Download PDFInfo
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- 239000000956 alloy Substances 0.000 title claims abstract description 63
- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 38
- 239000013079 quasicrystal Substances 0.000 title claims abstract description 36
- 238000002360 preparation method Methods 0.000 title abstract description 9
- 239000000843 powder Substances 0.000 claims abstract description 68
- 229910021365 Al-Mg-Si alloy Inorganic materials 0.000 claims abstract description 32
- 238000000034 method Methods 0.000 claims abstract description 23
- 239000002245 particle Substances 0.000 claims abstract description 23
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 15
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims abstract description 15
- 238000005728 strengthening Methods 0.000 claims abstract description 15
- 238000004519 manufacturing process Methods 0.000 claims abstract description 11
- 239000000654 additive Substances 0.000 claims abstract description 9
- 230000000996 additive effect Effects 0.000 claims abstract description 9
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- 230000007480 spreading Effects 0.000 claims description 12
- 239000011856 silicon-based particle Substances 0.000 claims description 8
- 239000011159 matrix material Substances 0.000 claims description 6
- 229910003407 AlSi10Mg Inorganic materials 0.000 claims description 2
- 229910019018 Mg 2 Si Inorganic materials 0.000 claims description 2
- 230000001427 coherent effect Effects 0.000 claims description 2
- 238000002156 mixing Methods 0.000 claims description 2
- 229910045601 alloy Inorganic materials 0.000 abstract description 22
- 229910018464 Al—Mg—Si Inorganic materials 0.000 abstract description 19
- 239000000463 material Substances 0.000 abstract description 10
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- 230000002195 synergetic effect Effects 0.000 description 2
- LDXJRKWFNNFDSA-UHFFFAOYSA-N 2-(2,4,6,7-tetrahydrotriazolo[4,5-c]pyridin-5-yl)-1-[4-[2-[[3-(trifluoromethoxy)phenyl]methylamino]pyrimidin-5-yl]piperazin-1-yl]ethanone Chemical compound C1CN(CC2=NNN=C21)CC(=O)N3CCN(CC3)C4=CN=C(N=C4)NCC5=CC(=CC=C5)OC(F)(F)F LDXJRKWFNNFDSA-UHFFFAOYSA-N 0.000 description 1
- 229910018134 Al-Mg Inorganic materials 0.000 description 1
- 229910018125 Al-Si Inorganic materials 0.000 description 1
- 229910018137 Al-Zn Inorganic materials 0.000 description 1
- 229910018467 Al—Mg Inorganic materials 0.000 description 1
- 229910018520 Al—Si Inorganic materials 0.000 description 1
- 229910018573 Al—Zn Inorganic materials 0.000 description 1
- 229910019064 Mg-Si Inorganic materials 0.000 description 1
- 229910019406 Mg—Si Inorganic materials 0.000 description 1
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- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 1
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
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Abstract
The invention discloses a quasicrystal reinforced toughness high-strength aluminum alloy material and a preparation method thereof. The alloy is prepared from raw materials including Al-Mg-Si alloy and H13 through additive manufacturing; the Al-Mg-Si alloy comprises the following components in percentage by mass: 2 to 6 percent of Mg, 1 to 2.5 percent of Si, 0.2 to 0.6 percent of Mn and the balance of aluminum; the mass ratio of the Al-Mg-Si alloy to H13 is 80-120:3. The alloy material adopts Al-Mg-Si powder H13 powder with different particle sizes, realizes the integrated forming of the alloy material by an additive manufacturing LPBF technology, correspondingly adjusts the technological parameters of LPBF according to the mass ratio of Al-Mg-Si to H13, thereby improving the formability of the material, further playing the effect of strengthening the comprehensive performance of the alloy material, and the maximum relative density of the aluminum alloy material obtained by the method is 99.8%, the maximum tensile strength is 523.5MPa, the yield strength is 450.3MPa and the elongation is 9.4%.
Description
Technical Field
The invention relates to a quasicrystal reinforced aluminum alloy material, in particular to a quasicrystal reinforced high-strength aluminum alloy material with toughness and a preparation method thereof, belonging to the technical field of new material preparation.
Background
The aluminum alloy has been widely used in the industries of aerospace, automobiles, electronics, precision parts and the like because of low cost, high specific strength, low density, good plasticity and good corrosion resistance. In recent years, as the need to produce components of complex morphology has increased, there have been significant challenges to conventionally manufactured aluminum components. Laser Powder Bed Fusion (LPBF) is one of the most popular Additive Manufacturing (AM) techniques. This method is particularly attractive for producing near net assemblies with customizable geometry, size and performance without resorting to molds, tools or dies. By selective melting of the powder by LPBF using laser, a higher cooling rate can be achieved due to a smaller melt pool, a shorter interaction of the powder with the laser beam (10 3 -10 6 K/s), complex and ultrafine microstructures are formed, and even metastable phases are formed. Therefore, the processing of high strength and toughness aluminum-based alloys by LPBF technology is becoming more and more of a concern in scientific and enterprise industries.
To date, aluminum alloy series manufactured by LPBF, such as Al-Si, al-Cu, al-Mg-Si and Al-Zn, also referred to as 2XXX, 6XXX and 7XXX series, have been usedExtensive research has been conducted. However, most commercial high strength aluminum alloys are rarely successfully processed by LPBF due to their high crack sensitivity, high thermal conductivity, high laser reflectivity, high linear expansion coefficient, and the like. One of the most effective methods for expanding the application of conventional alloys is to add heterogeneous nucleation particles, such as the addition of noble metals such as Sc, zr, etc. to convert coarse columnar crystals into equiaxed crystals to improve crack resistance and formability, but this will increase the manufacturing cost and is not suitable for industrial mass production. TiB (TiB) 2 Ceramic particles such as SiC, tiN, etc. can also provide heterogeneous nucleation sites, fine grains improve formability, but these reinforcing phases have significantly different physical and mechanical properties from aluminum substrates due to the external addition. Thus, under rapid solidification or cyclic loading conditions, insufficient metallurgical bonding occurs.
In contrast, quasicrystals (QC) are attracting more and more attention due to their perfect properties of coordination with the metal matrix. The quasicrystal has the special property combination generated by quasiperiodic enhancement, and has the properties of low friction coefficient, heat conductivity coefficient, high hardness, elastic modulus, good corrosion resistance and the like, so that the quasicrystal has good enhancement phase performance in the aluminum matrix composite material. But cannot be used in a monolithic form for structural applications due to its relatively high hard and brittle nature and insufficient toughness. Therefore, how to realize the effective strengthening of the quasicrystal in the aluminum alloy has important significance for improving the strength and toughness of the aluminum alloy.
Disclosure of Invention
A first object of the present invention is to provide a quasicrystal reinforced tough high-strength aluminum alloy material that uses H13 powder to modify Al-Mg-Si alloy. On one hand, H13 steel powder has good laser absorptivity to improve the formability of the alloy integral material, and on the other hand, mg is formed in the center of a molten pool based on the formation of quasicrystal at the boundary of the molten pool 2 Si particles and Fe-rich phase particles are synergistically reinforced, so that the mechanical properties of the alloy are greatly improved.
The second aim of the invention is to provide a preparation method of the quasicrystal reinforced toughness high-strength aluminum alloy material, which adopts Al-Mg-Si powder H13 powder with different particle sizes, adopts the additive manufacturing LPBF technology, further adjusts the process parameters to control the formability and mechanical properties of the material, and thus realizes the rapid integrated forming of the high-toughness alloy.
In order to achieve the technical aim, the invention provides a quasicrystal reinforced toughness high-strength aluminum alloy material which is prepared by additive manufacturing of raw materials including Al-Mg-Si alloy and H13; the Al-Mg-Si alloy comprises the following components in percentage by mass: 2 to 6 percent of Mg, 1 to 2.5 percent of Si, 0.2 to 0.6 percent of Mn and the balance of aluminum;
the mass ratio of the Al-Mg-Si alloy to H13 is 80-120:3.
The proportion of the raw materials adopted by the invention is strictly executed according to the requirements, if the adding proportion of the H13 powder is too small, on one hand, too little H13 can not obviously improve the laser absorptivity of the whole alloy and influence the forming performance of the alloy, and on the other hand, too little quasicrystal produced by the alloy can be caused to reduce the mechanical property; if the addition ratio of the H13 steel powder is too large, the content of the generated quasicrystal increases, and the hard brittleness of the alloy is increased, so that the elongation of the alloy is reduced.
As a preferred embodiment, the molten pool boundary of the aluminum alloy material is quasi-crystalline.
As a preferred embodiment, the quasi-crystal has a particle size of 500 to 600nm.
As a preferable scheme, the center of a molten pool of the aluminum alloy material is Mg 2 Si particles and Fe-rich phase particles, the particle size is 30-50 nm.
As a preferred embodiment, the Mg in the center of the molten pool 2 The interfaces between the Si particles and the Fe-rich phase particles and the Al matrix are coherent interfaces. The quasicrystal has quasiperiodic property, can well strengthen an Al matrix, and simultaneously has the advantages of Mg 2 The Si and Fe phase particles are precipitated and semi-coherent with the matrix boundary, which facilitates the smooth cutting of dislocations through the second phase particles to improve strength and plasticity.
The invention also provides a preparation method of the quasicrystal reinforced toughness high-strength aluminum alloy material, which comprises the steps of uniformly mixing raw materials including Al-Mg-Si alloy powder and H13 powder, paving the mixture on a printed AlSi10Mg substrate, and performing LPBF printing and forming.
The preparation method provided by the invention adopts Al-Mg with different particle sizes 2 The method adopts Al-Mg-Si powder H13 powder with different particle sizes, adopts an additive manufacturing LPBF technology, and further adjusts technological parameters to control the formability and mechanical properties of the material, thereby realizing the rapid integrated forming of the high-strength and high-toughness alloy.
As a preferable embodiment, the Al-Mg-Si alloy powder has a particle size of 10 to 70 μm and the H13 powder has a particle size of 15 to 53. Mu.m.
As a preferable scheme, the purity of the Al-Mg-Si alloy powder and the purity of the H13 powder are both more than or equal to 99.9 percent.
As a preferable scheme, the main parameters of the LPBF printing forming are as follows: the laser power is 270-320W, and the laser scanning speed is 800-1000 mm/s; the scanning interval is 0.1-0.12 mm, the powder spreading thickness is 0.02-0.06 mm, the temperature of the substrate is 80-100 ℃, and the scanning strategy is that each layer rotates 50-70 degrees.
As a preferable scheme, when the mass ratio of the Al-Mg-Si alloy powder to the H13 powder is 90-100:3, the Al-Mg-Si alloy powder comprises the following components in percentage by mass: 3 to 5 percent of Mg, 1 to 1.5 percent of Si and 0.3 to 0.5 percent of Mn.
As a preferable scheme, the main parameters of the LPBF printing forming process are as follows: the laser power is 280-300W, and the laser scanning speed is 900-1000 mm/s; the scanning interval is 0.1-0.11 mm, the powder spreading thickness is 0.03-0.05 mm, the substrate temperature is 90-100 ℃, and the scanning strategy is that each layer rotates 55-65 degrees.
As a preferred scheme, the mass ratio of the Al-Mg-Si alloy powder to the H13 powder is 97:3, and wherein the Al-Mg-Si alloy consists of: mg 4%, si 1.2%, mn 0.4%, and the balance aluminum, the main parameters of the LPBF printing forming process are: laser power 290W and laser scanning speed 950mm/s; the scanning interval is 0.1mm, the powder spreading thickness is 0.04mm, the substrate temperature is 90 ℃, and the scanning strategy is that each layer rotates by 60 degrees.
In the mass ratio range of the Al-Mg-Si to the H13 steel, as the content of H13 is increased, the laser absorptivity of the alloy is increased, and the formability is improved, so that the selected laser power is lower, the scanning speed is higher, the scanning interval is also larger, and the laser energy density is low and the formability is better; however, as the content of Al-Mg-Si increases, the required laser energy density is high, so that the laser power is larger, the scanning speed is smaller, the scanning interval is smaller, the formability is better, and in addition, the scanning strategy is to cancel the anisotropy to a certain extent for better forming, so that the process parameter selection of the Al-Mg-Si and H13 steels with different contents should be strictly in accordance with the requirements of the invention.
Compared with the prior art, the technical scheme of the invention has the beneficial technical effects that:
1) The aluminum alloy material provided by the invention adopts H13 to modify Al-Mg-Si based on the synergistic effect of the components, on one hand, the H13 steel powder has good laser absorptivity to improve the formability of the alloy integral material, and on the other hand, the microstructure is promoted to form a fine layered structure, namely, quasi-crystals are formed at the boundary of a molten pool, and Mg is formed at the center of the molten pool 2 Si particles and Fe-rich phase particles are synergistically strengthened, so that the mechanical properties of the alloy are greatly improved.
2) According to the preparation method provided by the invention, the integrated forming of the alloy material is realized by adopting the Al-Mg-Si powder H13 powder with different particle sizes through the additive manufacturing LPBF technology, and the process parameters of the LPBF are correspondingly adjusted according to the mass ratio of the Al-Mg-Si to the H13, so that the formability of the material is improved, and the effect of strengthening the comprehensive performance of the alloy material is further achieved.
3) In the technical proposal provided by the invention, quasicrystal strengthening and Mg are formed by additive manufacturing 2 The Si particles and the Fe-rich phase are subjected to precipitation strengthening, and the compactness and the toughness of the alloy can be realized without adding noble metal elements, ceramic particles and the like. Through tests, the alloy material provided by the invention has the maximum relative density of 99.8%, the maximum tensile strength of 523.5MPa, the yield strength of 450.3MPa and the elongation of 9.4%.
Drawings
FIG. 1 is a microstructure of the Al-Mg-Si and H13 mixed powder used in example 3;
FIG. 2 is an SEM image of alloy materials prepared in example 3 and comparative example 3;
wherein, fig. 2a and 2b are SEM images of the alloy material obtained in comparative example 3, and fig. 2c and 2d are SEM images of the alloy material obtained in example 3;
fig. 3 is a TEM image of the alloy material obtained in example 3.
Detailed Description
The present invention will be described in detail below with reference to the drawings and the detailed description, and it should not be construed that the invention is limited to the embodiments. It will be apparent to those skilled in the art that several simple deductions or substitutions may be made without departing from the spirit of the invention, and these should be considered to be within the scope of the invention.
Example 1
The mass ratio of the Al alloy powder to the H13 powder of the Al-Mg-Si-H13 alloy part prepared by LPBF molding is 120:3, wherein the Al-Mg-Si alloy consists of the following components: mg 4%, si 1.2%, mn 0.4%, the balance being aluminum and non-removable impurity elements. The grain diameter Al-Mg-Si is 10-70 mu m, and the grain diameter of H13 powder is 15-53 mu m; the main parameters of the LPBF printing forming process are as follows: the laser power is 310W, and the laser scanning speed is 850mm/s; the scanning interval is 0.1mm, the powder spreading thickness is 0.04mm, the substrate temperature is 90 ℃, and the scanning strategy is that each layer rotates by 60 degrees.
The alloy material provided by the invention has the relative density of 99.4%, the horizontal plane maximum tensile strength of 463.15MPa, the yield strength of 377.7MPa and the elongation of 7.3%.
Example 2
The mass ratio of the Al alloy powder to the H13 powder of the Al-Mg-Si-H13 alloy part prepared by LPBF molding is 100:3, wherein the Al-Mg-Si alloy consists of the following components: mg 4%, si 1.2%, mn 0.4%, the balance being aluminum and non-removable impurity elements. The grain diameter Al-Mg-Si is 10-70 mu m, and the grain diameter of H13 powder is 15-53 mu m; the main parameters of the LPBF printing forming process are as follows: laser power 290W and laser scanning speed 950mm/s; the scanning interval is 0.1mm, the powder spreading thickness is 0.04mm, the substrate temperature is 90 ℃, and the scanning strategy is that each layer rotates by 60 degrees.
The alloy material provided by the invention has the relative density of 99.5%, the horizontal plane maximum tensile strength of 474.1MPa, the yield strength of 410.2MPa and the elongation of 8.1%.
Example 3
The mass ratio of the Al alloy powder to the H13 powder of the Al-Mg-Si-H13 alloy part prepared by LPBF molding is 97:3, wherein the Al-Mg-Si alloy consists of the following components: mg 4%, si 1.2%, mn 0.4%, the balance being aluminum and non-removable impurity elements. The grain diameter Al-Mg-Si is 10-70 mu m, and the grain diameter of H13 powder is 15-53 mu m; the main parameters of the LPBF printing forming process are as follows: laser power 290W and laser scanning speed 950mm/s; the scanning interval is 0.1mm, the powder spreading thickness is 0.04mm, the substrate temperature is 90 ℃, and the scanning strategy is that each layer rotates by 60 degrees.
The relative density of the alloy material provided by the invention is 99.8%, the maximum tensile strength of a horizontal plane is 523.5MPa, the yield strength is 420.3MPa, and the elongation is 9.4%.
Example 4
The mass ratio of the Al alloy powder to the H13 powder of the Al-Mg-Si-H13 alloy part prepared by LPBF molding is 97:3, wherein the Al-Mg-Si alloy consists of the following components: mg 3%, si 1%, mn 0.3%, the balance being aluminum and non-removable impurity elements. The grain diameter Al-Mg-Si is 10-70 mu m, and the grain diameter of H13 powder is 15-53 mu m; the main parameters of the LPBF printing forming process are as follows: laser power 290W and laser scanning speed 950mm/s; the scanning interval is 0.1mm, the powder spreading thickness is 0.04mm, the substrate temperature is 90 ℃, and the scanning strategy is that each layer rotates by 60 degrees.
The relative density of the Al alloy shown is 99.5%, the maximum tensile strength is 493.4MPa, the yield strength is 421.8MPa, and the elongation is 6.4%.
Comparative example 1
The mass ratio of the Al alloy powder to the H13 powder of the Al-Mg-Si-H13 alloy part prepared by LPBF molding is 97:3, wherein the Al-Mg-Si alloy consists of the following components: mg 4%, si 1.2%, mn 0.4%, the balance being aluminum and non-removable impurity elements. The grain diameter Al-Mg-Si is 10-70 mu m, and the grain diameter of H13 powder is 15-53 mu m; the main parameters of the LPBF printing forming process are as follows: laser power 260W, laser scanning speed 1300mm/s; the scanning interval is 0.14mm, the powder spreading thickness is 0.02mm, the substrate temperature is 70 ℃, and the scanning strategy is that each layer rotates 55 degrees.
The relative density of the alloy material provided by the invention is 99.1%, the maximum tensile strength of a horizontal plane is 430.1MPa, the yield strength is 335.4MPa, and the elongation is 5.6%.
Comparative example 2
The mass ratio of the Al alloy powder to the H13 powder of the Al-Mg-Si-H13 alloy part prepared by LPBF molding is 80:3, wherein the Al-Mg-Si alloy consists of the following components: mg 3%, si 1%, mn 0.4%, the balance being aluminum and non-removable impurity elements. The grain diameter Al-Mg-Si is 10-70 mu m, and the grain diameter of H13 powder is 15-53 mu m; the main parameters of the LPBF printing forming process are as follows: the laser power is 320W, and the laser scanning speed is 6000mm/s; the scanning interval is 0.1mm, the powder spreading thickness is 0.04mm, the substrate temperature is 90 ℃, and the scanning strategy is that each layer rotates by 60 degrees.
The alloy material provided by the invention has the relative density of 98.9%, the horizontal plane maximum tensile strength of 413.2MPa, the yield strength of 294.9MPa and the elongation of 2.6%.
Comparative example 3
An Al-Mg-Si alloy without added H13 powder prepared by LPBF forming, wherein the Al-Mg-Si alloy consists of the following components: mg 4%, si 1.2%, mn 0.4%, the balance being aluminum and non-removable impurity elements. The grain diameter Al-Mg-Si is 10-70 mu m; the main parameters of the LPBF printing forming process are as follows: laser power 290W and laser scanning speed 950mm/s; the scanning interval is 0.1mm, the powder spreading thickness is 0.04mm, the substrate temperature is 90 ℃, and the scanning strategy is that each layer rotates by 60 degrees.
The alloy material provided by the invention has the relative density of 98.7%, the horizontal plane maximum tensile strength of 410.7MPa, the yield strength of 320.1MPa and the elongation of 4.8%.
Table 1 shows the properties of samples of the invention and comparative examples
The detection results shown in Table 1 show that the formability and the mechanical properties of the Al-Mg-Si alloy can be synchronously improved by adding the H13 steel powder, but the addition amount of the H13 powder and the element content in the Al-Mg-Si alloy are required to be strictly controlled; meanwhile, selecting area laser melting printing parameters; the combination of these two components can achieve high strength and elongation of the aluminum alloy.
The raw materials adopted in the invention are shown in figure 1, the powder morphology of Al-Mg-Si and H13 can be seen in figure 1, the yellow frame is H13 powder, the two are uniformly mixed together, the alloy material without H13 powder in comparative example 3 has a typical printing state molten pool structure, no quasicrystal appears, a large number of quasicrystals appear in example 3 with H13 powder added, quasicrystal strengthening is realized, and further as can be seen from figure 3, the Mg exists in the molten pool center of the material obtained in example 3 2 Si and Fe phase particles with the size of 30-50 nm, which shows that the material provided by the invention fully utilizes the formation of quasicrystal at the boundary of a molten pool, and Mg is formed at the center of the molten pool 2 The synergistic strengthening effect of Si particles and Fe-rich phase particles realizes the great improvement of the comprehensive performance of the material.
The foregoing is merely illustrative of the preferred embodiments of this invention, and it will be appreciated by those skilled in the art that changes and modifications may be made without departing from the principles of this invention, which is also intended to be included within the scope of this invention.
Claims (9)
1. A quasicrystal reinforced toughness high-strength aluminum alloy material is characterized in that: is prepared from raw materials including Al-Mg-Si alloy and H13 through additive manufacturing; the Al-Mg-Si alloy comprises the following components in percentage by mass: 2 to 6 percent of Mg, 1 to 2.5 percent of Si, 0.2 to 0.6 percent of Mn and the balance of aluminum;
the mass ratio of the Al-Mg-Si alloy to H13 is 80-120:3.
2. The quasicrystal strengthening toughness high-strength aluminum alloy material according to claim 1, wherein: the boundary of the molten pool of the aluminum alloy material is a quasi-crystal; the grain diameter of the quasi-crystal is 500-600 nm.
3. The quasicrystal strengthening toughness high-strength aluminum alloy material according to claim 1, wherein: the center of a molten pool of the aluminum alloy material is Mg 2 Si particles and Fe-rich phase particles, the particle size is 30-50 nm.
4. A quasicrystal strengthening ductile high strength aluminum alloy material according to claim 3, characterized in that: mg in the center of the molten pool 2 The interfaces between the Si particles and the Fe-rich phase particles and the Al matrix are coherent interfaces.
5. The method for preparing the quasicrystal strengthening toughness high-strength aluminum alloy material according to any one of claims 1 to 4, which is characterized in that: uniformly mixing raw materials including Al-Mg-Si alloy powder and H13 powder, paving on a printed AlSi10Mg substrate, and performing LPBF printing and forming to obtain the aluminum alloy.
6. The method for preparing the quasicrystal strengthening toughness high-strength aluminum alloy material according to claim 5, which is characterized in that: the grain diameter of the Al-Mg-Si alloy powder is 10-70 mu m, and the grain diameter of the H13 powder is 15-53 mu m; the purity of the Al-Mg-Si alloy powder and the purity of the H13 powder are both more than or equal to 99.9 percent.
7. The method for preparing the quasicrystal strengthening toughness high-strength aluminum alloy material according to claim 5, which is characterized in that: the main parameters of the LPBF printing and forming are as follows: the laser power is 270-320W, and the laser scanning speed is 800-1000 mm/s; the scanning interval is 0.1-0.12 mm, the powder spreading thickness is 0.02-0.06 mm, the temperature of the substrate is 80-100 ℃, and the scanning strategy is that each layer rotates 50-70 degrees.
8. The method for preparing the quasicrystal strengthening toughness high-strength aluminum alloy material according to claim 5, which is characterized in that: when the mass ratio of the Al-Mg-Si alloy powder to the H13 powder is 90-100:3, the Al-Mg-Si alloy powder comprises the following components in percentage by mass: 3 to 5 percent of Mg, 1 to 1.5 percent of Si and 0.3 to 0.5 percent of Mn.
9. The method for preparing the quasicrystal strengthening toughness high-strength aluminum alloy material according to claim 8, which is characterized in that: the main parameters of the LPBF printing forming process are as follows: the laser power is 280-300W, and the laser scanning speed is 900-1000 mm/s; the scanning interval is 0.1-0.11 mm, the powder spreading thickness is 0.03-0.05 mm, the substrate temperature is 90-100 ℃, and the scanning strategy is that each layer rotates 55-65 degrees.
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