CN115747584B - Crack-free reinforced Al-Mg 2 Si-Si alloy material, preparation method and application thereof - Google Patents
Crack-free reinforced Al-Mg 2 Si-Si alloy material, preparation method and application thereof Download PDFInfo
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- 229910018467 Al—Mg Inorganic materials 0.000 title claims abstract description 72
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- 229910006411 Si—Si Inorganic materials 0.000 title claims abstract description 38
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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
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- Y02P10/00—Technologies related to metal processing
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Abstract
The invention discloses a crack-free reinforced Al-Mg 2 Si-Si alloy material, and its preparation method and application are provided. The alloy material adopts Al-Mg with different grain diameters 2 Si powder and Si powder are mixed and prepared through an additive manufacturing process, so that the rapid forming of the high-strength and high-toughness alloy is realized. The alloy material is based on the synergistic effect among the components of the raw materials and the main strengthening phase Al-Mg 2 The co-operation between Si and the matrix and the auxiliary strengthening phase Si precipitation do not need to additionally introduce strengthening elements, so that the fluidity of the alloy in a molten state is improved, the solidification interval of the alloy material is greatly reduced, and the effect of no crack and pore is realized while the mechanical property of the alloy material is ensured. The alloy material provided by the invention effectively solves the problems of low strength, large solidification zone, poor formability and the like of the aluminum alloy, and can meet the mechanical requirements of turbine blades.
Description
Technical Field
The invention relates to a crack-free aluminum alloy material, in particular to a crack-free reinforced Al-Mg 2 Si-Si alloy material, and a preparation method and application thereof, belonging to the technical field of new material preparation.
Background
The aluminum alloy is the most widely used metal structural material at present, and has low density, high specific strength, easy processing and good corrosion resistance after steel. Has wide application and development potential in the fields of aviation, automobiles, power electronics and the like. At present, aluminum alloy structural parts are mainly manufactured by adopting traditional methods such as casting, forging, extrusion, powder metallurgy and the like. Although the aluminum alloy products produced by the traditional process are widely applied, the defects of low mechanical property, low production efficiency, low design freedom and the like exist. In addition, with the development of modern industry, the production of aluminum alloy parts with various structures, high dimensional accuracy and near net shape is a main research and development goal in the future.
Selective Laser Melting (SLM) is considered one of the most promising Additive Manufacturing (AM) techniques. SLM utilizes a high energy laser beam to completely melt a metal powder in a protective atmosphere along the laser path, where the molten metal solidifies rapidly. By repeating this step, the layers overlap one another, eventually forming a three-dimensional component. This layering approach has unique advantages in the integrated formation of complex structures and thin-walled components. SLM is an unbalanced solidification process that increases the solid solubility limit of alloying elements in the matrix and may produce metastable phases and fine precipitated phases. However, due to high rapid cooling in the manufacturing process of the SLM, extremely large thermal stress is easy to generate, so that the defects of periodic cracks, shrinkage cavities and the like of the sample are caused, and the types of commercial aluminum alloys are limited; the most common Al alloy melted by selective laser at present is mainly Al-Si alloy, such as Al-12Si, alSi10Mg, which has good formability but low mechanical property and can not be meltedMeets the high strength and toughness requirements of the current industrial Al alloy; and the high strength and toughness 2-series, 6-series and 7-series aluminum alloys have cracks due to an excessively large solidification zone, and have poor formability. Noble metals such as Sc and Zr or TiB are required to be added 2 Ceramic particles such as SiC, tiN, etc. increase formability, which increases the manufacturing cost, and are not suitable for industrial mass production. Therefore, by utilizing the characteristic of extreme metallurgical unbalanced solidification of SLM forming, it is of great importance to develop a novel complex part of high-strength and high-toughness aluminum alloy with low cost, narrow solidification interval and no cracks.
Disclosure of Invention
A first object of the present invention is to provide a crack-free reinforced Al-Mg, which solves the problems of the prior art 2 Si-Si alloy material using Si powder to Al-Mg 2 Modification of Si based on second phase particles Mg 2 Si and Si cooperate with strengthening effect, have improved the mobility under the alloy molten state, reduce the solidification interval of the alloy material by a wide margin, thus while guaranteeing the mechanical property of the alloy material, have realized the effect of the crack-free pore.
A second object of the present invention is to provide a crack-free reinforced Al-Mg 2 Preparation method of Si-Si alloy material, which adopts Al-Mg with different grain diameters 2 The Si powder and the Si powder are based on the synergistic effect of the components among the raw materials, and the additive manufacturing process is adopted, and the formability and the mechanical properties of the materials are controlled by adjusting the process parameters, so that the rapid forming of the high-strength and high-toughness alloy is realized.
A third object of the present invention is to provide a crack-free reinforced Al-Mg 2 The application of the Si-Si alloy material is used for preparing turbine blades. The alloy material provided by the invention can realize the compactness and the toughness of the alloy based on the semi-coherent action of the main strengthening phase and the precipitation of the auxiliary strengthening phase without adding noble metal elements such as Sc, zr and the like, ceramic particles and strengthening elements Cu and Zn, and the relative density of the alloy material provided by the invention is 99.8%, no crack exists, the maximum tensile strength is 484.3MPa, the yield strength is 386.1MPa and the extensibility is 7.85%, so that the performance requirement of the turbine blade is met.
To achieve the technical aim, the invention provides a crack-free reinforced Al-Mg 2 Preparation method of Si-Si alloy material comprises mixing Al-Mg 2 Uniformly mixing Si alloy powder and Si powder, paving on a substrate, and performing 3d printing and forming to obtain the composite material; the Si powder and Al-Mg 2 The mass ratio of the Si alloy powder is 1: 24-499.
The preparation method provided by the invention adopts Al-Mg with different particle sizes 2 The Si powder and the Si powder are based on the synergistic effect of the components among the raw materials, and the additive manufacturing process is adopted, and the formability and the mechanical properties of the materials are controlled by adjusting the process parameters, so that the rapid forming of the high-strength and high-toughness alloy is realized.
As a preferred embodiment, the Al-Mg 2 The grain size of the Si alloy powder is 30-60 mu m, and the grain size of the Si powder is 10-25 mu m.
The grain size of Si powder adopted in the preparation method provided by the invention is smaller than that of Al-Mg 2 The addition of the Si alloy powder and the fine powder Si can reduce the particle gap and improve the bulk density, thereby improving the density and mechanical property of the formed material.
The particle size of the raw materials adopted in the invention is strictly carried out according to the requirements, if Al-Mg 2 The excessively large particle size of the Si powder may cause the surface roughness of the printed metal sample to become high; if the Si powder particle size is too large, adhesion agglomeration is likely to occur, resulting in a decrease in powder flowability and a decrease in formability.
The proportion of the raw materials adopted by the invention is strictly executed according to the requirements, if the addition proportion of Si is too small, the alloy melt fluidity is poor, the solidification interval is too large, the heat sensitivity factor is too high, and poor formability is caused; when the addition proportion of Si is too large, on one hand, the generated eutectic phase is increased, so that the elongation of the alloy is low; on the other hand due to Al-Mg 2 Si content is too low to reduce mechanical properties.
As a preferred embodiment, the Al-Mg 2 The Si alloy powder comprises the following components in percentage by mass: 8-11% Mg 2 Si, the balance Al.
As a preferenceIn the scheme (1), the Al-Mg 2 The purity of the Si alloy powder and the Si powder is more than or equal to 99.9 percent.
As a preferable scheme, the main parameters of the 3d printing forming process are as follows: the main body laser power is 310-350W, and the main body laser scanning speed is 600-800 mm/s; the laser power of filling the upper surface and the lower surface is 250-280W, and the scanning speed is 1000-1200 mm/s; filling profile laser power is 220-270W, and scanning speed is 100-300 mm/s; the outer wall scanning power is 250-300W, and the scanning speed is 200-400 mm/s; the scanning interval is 0.1-0.15 mm, the powder spreading thickness is 0.02-0.04 mm, the scanning area width is 5-8 mm, and the substrate temperature is 80-100 ℃.
As a preferred embodiment, the Si powder is mixed with Al-Mg 2 The mass ratio of the Si alloy powder is 1:70 to 80 percent of Al-Mg 2 Mg in Si alloy powder 2 When Si is 8.5-9.5%, the main parameters of the 3d printing forming process are as follows: the main body laser power is 320-340W, and the scanning speed is 600-700 mm/s; the laser power of filling the upper surface and the lower surface is 250-270W, and the scanning speed is 1000-1100 mm/s; the filling contour laser power is 240-260W, the scanning speed is 150-250 mm/s, the outer wall scanning laser is 250-270W, and the scanning speed is 200-300 mm/s; the scanning interval is 0.1-0.14 mm, the powder spreading thickness is 0.02-0.03 mm, the scanning area width is 5-7 mm, and the substrate temperature is 80-100 ℃.
As a preferred embodiment, the Si powder is mixed with Al-Mg 2 The mass ratio of the Si alloy powder is 1:76, al-Mg 2 Mg in Si alloy powder 2 When Si is 9%, the main parameters of the 3d printing forming process are as follows: main body laser power 330W and scanning speed 650mm/s; the filling laser power of the upper surface and the lower surface is 260W, and the scanning speed is 1100mm/s; filling profile laser power 250W, scanning speed 200mm/s outer wall scanning laser 260W, and scanning speed 250mm/s; the scanning interval is 0.12mm, the powder spreading thickness is 0.02mm, the scanning area width is 6mm, and the substrate temperature is 90 ℃.
Si and Al-Mg provided by the invention 2 In the mass ratio range of Si, as the Si content increases, the melting temperature of the alloy decreases and the fluidity increases, so that the laser power is selected to be lower, the scanning speed is higher, the scanning interval is also larger, and the laser is excitedThe light energy density is low, and the formability is good; but with Al-Mg 2 Mg in Si 2 The Si content is increased, 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 the Si content and the Mg content are different 2 The choice of the process parameters for Si should be strictly in accordance with the requirements of the invention.
The invention also provides a crack-free reinforced Al-Mg 2 A Si-based alloy obtained by the production method according to any one of the above.
As a preferred embodiment, the Al-Mg 2 Si-Si alloy material comprising Mg having a main strengthening phase of 100 to 400nm 2 Si and Si of 100-200 nm as auxiliary strengthening phase.
As a preferred embodiment, the primary strengthening phase is semi-coherent with the Al matrix and the secondary strengthening phase precipitates around the cellular structure.
The main strengthening precipitation phase and the matrix boundary are in a coherent relation, which is beneficial to the dislocation to smoothly cut through the second phase particles so as to improve the strength and the plasticity, and the auxiliary strengthening precipitation phase is deposited around the cellular tissue so as to be beneficial to pinning the grain boundary so as to improve the strength.
As a preferred embodiment, the Al-Mg 2 The solidification zone of the Si-Si alloy material is 25-39 ℃, and the heat sensitivity factor is 0.19-2.6X10 4 ℃。
Thermal cracking generally occurs at solids fractions above 0.9 at the end of solidification, with smaller solidification ranges indicating lower crack sensitivity and better formability according to the unbalanced Scheil model. Relative to the 2-series Al-Cu solidification interval 141.7 ℃, the 6-series Al-Mg-Si solidification interval 114 ℃, and the 7-series Al-Zn-Mg-Cu solidification interval 168.4 ℃. Al-Mg of the invention 2 The solidification interval of Si-Si is only 25-39 ℃, and the heat sensitivity factor is 0.19-2.6X10 4 Based on the synergistic effect between the two, the excellent forming performance of the alloy material is ensured, so that the alloy material prepared by additive manufacturing has no crack and pore and has high relative density.
The solidification zone and the heat-sensitive factor of the alloy material provided by the invention are strictly executed according to the requirements, and when the solidification zone and the heat-sensitive factor are too high, the heat cracking tendency is serious, cracks are easy to generate, and the forming performance is poor.
The invention also provides a crack-free reinforced Al-Mg 2 The application of the Si-Si alloy material is used for preparing turbine blades.
The alloy material provided by the invention controls the formation through a solidification zone and a heat-sensitive factor, and simultaneously, the second phase particles Mg 2 Si and Si are synergistically strengthened, and technological parameters are adjusted to realize good combination of formability and mechanical properties, so that the aim of the formability synergy is fulfilled; the alloy material can realize the production of complex parts and can meet the mechanical requirements of light materials such as aerospace, high-speed rail and the like.
Compared with the prior art, the invention has the beneficial technical effects that:
1. the alloy material provided by the invention adopts Si powder to Al-Mg 2 Modification of Si based on second phase particles Mg 2 Si and Si cooperate with strengthening effect, have improved the mobility under the alloy molten state, reduce the solidification interval of the alloy material by a wide margin, thus while guaranteeing the mechanical property of the alloy material, have realized the effect of the crack-free pore.
2. In the technical scheme provided by the invention, the Al-Mg with different particle sizes is adopted 2 The Si powder and the Si powder are based on the synergistic effect of the components among the raw materials, and the additive manufacturing process is adopted, and the formability and the mechanical properties of the materials are controlled by adjusting the process parameters, so that the rapid forming of the high-strength and high-toughness alloy is realized.
3. According to the technical scheme provided by the invention, the provided alloy material can realize the compactness and the toughness of the alloy based on the semi-coherent action between the main strengthening phase and the matrix and the auxiliary strengthening phase precipitation without adding noble metal elements such as Sc, zr and the like, ceramic particles and strengthening elements Cu and Zn, and the relative density of the alloy material is 99.8%, the maximum tensile strength is 484.3MPa, the yield strength is 386.1MPa and the extensibility is 7.85%, and the performance requirements of turbine blades are met through tests.
Drawings
FIG. 1 is a drawing of Al-Mg as described in example 3 2 Microstructural map of Si-Si alloy powder;
FIG. 2 shows the Al-Mg of example 3 and comparative examples 1,3 2 A gold phase diagram of Si-Si;
wherein FIG. 2 (a) is the alloy phase diagram obtained in comparative example 3, FIG. 2 (b) is the alloy phase diagram obtained in comparative example 1, and FIG. 2 (c) is the alloy phase diagram obtained in example 3;
FIG. 3 is an Al-Mg alloy as described in example 3 2 TEM image of Si-Si;
FIG. 4 is a drawing showing the tensile properties of the alloys obtained in examples 1 to 4 and comparative examples 1 to 3;
FIG. 5 is a turbine blade made from the alloy material of example 3;
as can be seen from FIG. 1, the Si particle-added Al-Mg 2 Powder morphology of Si-Si;
as can be seen from fig. 2, (a) a gold phase diagram printed on an aluminum alloy without Si particles, which has a large number of defects such as crack and void; (b) For Al-Mg without using optimum process parameters 2 A Si-Si printed gold phase diagram, with a certain amount of voids; (c) The gold phase diagram printed for adding the optimal Si particles and the optimal process parameters shows that the gold phase diagram has no cracks and pores and high relative density;
as can be seen from FIG. 3, 100 to 400nmMg are distributed in a network 2 Si and Si of 100-200 nm;
the tensile properties of the respective examples and comparative examples can be seen from fig. 4;
from fig. 5, it can be seen that the best added fine Si particles and the best printing process parameters can be used to prepare complex parts with good formability, no cracks, and excellent mechanical properties.
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
Al-Mg made by SLM forming 2 The Al alloy component of the Si-Si alloy part consists of 8% of Mg 2 Si,0.5% Si, and the balance Al. The powder is prepared from coarse powder Al-Mg with average particle size of 30-60 μm 2 Si and 10-25 μm fine Si. The alloy solidification interval is 36 ℃, and the heat sensitivity factor is 0.24 multiplied by 10 4 DEG C. Al-Mg 2 Spreading Si-Si alloy powder on a substrate, and performing printing forming according to a three-dimensional model to obtain a complex part; wherein the laser parameters include: main body laser power 310W, main body laser scanning speed 600mm/s; the filling laser power of the upper surface and the lower surface is 250W, and the scanning speed is 1000mm/s; filling profile laser power 220W, and scanning speed 100mm/s; filling profile laser power 240W, scanning speed 200mm/s; the outer wall scanning power is 250W, and the scanning speed is 200mm/s; scanning interval is 0.1mm, powder spreading thickness is 0.02mm, scanning area width is 5mm, and substrate temperature is 90deg.C
The relative density of the Al alloy shown is 99.2%, the maximum tensile strength is 439.2MPa, the yield strength is 352.6MPa, and the elongation is 5.64%.
Example 2
Al-Mg made by SLM forming 2 The Al alloy component of the Si-Si alloy part consists of 9% of Mg 2 Si,0.5% Si, and the balance Al. The powder is prepared from coarse powder Al-Mg with average particle size of 30-60 μm 2 Si and 15-25 μm fine Si. The alloy solidification interval is 31 ℃, and the heat sensitivity factor is 0.22 multiplied by 10 4 DEG C. Al-Mg 2 Spreading Si-Si alloy powder on a substrate, and performing printing forming according to a three-dimensional model to obtain a complex part; wherein the laser parameters include: main body laser power 330W, main body laser scanning speed 600mm/s; the filling laser power of the upper surface and the lower surface is 260W, and the scanning speed is 1100mm/s; filling profile laser power 270W, and scanning speed 300mm/s; filling profile laser power 240W, scanning speed 100mm/s; the outer wall scanning power is 250W, and the scanning speed is 200mm/s; scanning interval is 0.1mm, powder spreading thickness is 0.02mm, scanning area width is 5mm, and substrate temperature is 90deg.C
The relative density of the Al alloy shown is 99.5%, the maximum tensile strength is 458.2MPa, the yield strength is 345.2MPa, and the elongation is 8.1%.
Example 3
Al-Mg made by SLM forming 2 The Al alloy component of the Si-Si alloy part consists of 9% of Mg 2 Si,1.3% Si, and the balance Al. The powder is prepared from coarse powder Al-Mg with average particle size of 30-60 μm 2 Si and 10-25 μm fine Si. The alloy solidification interval is 25 ℃, and the heat sensitivity factor is 0.19 multiplied by 10 4 DEG C. Al-Mg 2 Spreading Si-Si alloy powder on a substrate, and performing printing forming according to a three-dimensional model to obtain a complex part; wherein the laser parameters include: main body laser power 330W and scanning speed 650mm/s; the filling laser power of the upper surface and the lower surface is 260W, and the scanning speed is 1100mm/s; filling profile laser power 250W and scanning speed 200mm/s; the outer wall scans laser 260W at a scanning speed of 250mm/s; scanning interval is 0.12mm, powder spreading thickness is 0.02mm, scanning area width is 6mm, and substrate temperature is 90 ℃;
the printed complex part is a turbine blade, the relative density of the Al alloy is 99.8%, the Al alloy has no crack, the maximum tensile strength is 484.3MPa, the yield strength is 386.1MPa, and the elongation is 7.85%.
Example 4
Al-Mg made by SLM forming 2 The Al alloy component of the Si-Si alloy part consists of 11% of Mg 2 Si,4% Si, and the balance Al. The powder is prepared from coarse powder Al-Mg with average particle size of 30-60 μm 2 Si and 10-25 μm fine Si. The alloy solidification interval is 39 ℃, and the heat sensitivity factor is 0.26 multiplied by 10 4 DEG C. Al-Mg 2 Spreading Si-Si alloy powder on a substrate, and performing printing forming according to a three-dimensional model to obtain a complex part; wherein the laser parameters include: main body laser power is 350W, and scanning speed is 800mm/s; the filling laser power of the upper surface and the lower surface is 270W, and the scanning speed is 1200mm/s; filling profile laser power 270W, and scanning speed 300mm/s; the outer wall scans laser 280W at a scanning speed of 400mm/s; scanning interval is 0.15mm, powder spreading thickness is 0.04mm, scanning area width is 8mm, and substrate temperature is 90 ℃;
the relative density of the Al alloy shown is 99.1%, the maximum tensile strength is 461.8MPa, the yield strength is 357.8MPa, and the elongation is 5.2%.
Comparative example 1
Al-Mg made by SLM forming 2 The Al alloy component of the Si-Si alloy part consists of 9% of Mg 2 Si,1.3% Si, and the balance Al. The powder is prepared from coarse powder Al-Mg with average particle size of 30-60 μm 2 Si and 10-25 μm fine Si. The alloy solidification interval is 25 ℃, and the heat sensitivity factor is 0.19 multiplied by 10 4 DEG C. Al-Mg 2 Spreading Si-Si alloy powder on a substrate, and performing printing forming according to a three-dimensional model to obtain a complex part; wherein the laser parameters include: main body laser power 390W, scanning speed 1000mm/s; the filling laser power of the upper surface and the lower surface is 270W, and the scanning speed is 1200mm/s; filling profile laser power 330W, scanning speed 500mm/s; the outer wall scans the laser 300W, the scanning speed is 400mm/s; scanning interval is 0.2mm, powder spreading thickness is 0.05mm, scanning area width is 6mm, and substrate temperature is 70 ℃;
the relative density of the Al alloy shown is 99.6%, the maximum tensile strength is 414.0MPa, the yield strength is 328.2MPa, and the elongation is 3.3%.
Comparative example 2
Al-Mg made by SLM forming 2 The Al alloy component of the Si-Si alloy part consists of 9% of Mg 2 Si,6% Si, and the balance Al. The alloy solidification interval is 45 ℃, and the heat sensitivity factor is 0.29 multiplied by 10 4 DEG C. Al-Mg 2 Spreading Si-Si alloy powder on a substrate, and performing printing forming according to a three-dimensional model to obtain a complex part; wherein the laser parameters include: main body laser power 330W and scanning speed 650mm/s; the filling laser power of the upper surface and the lower surface is 260W, and the scanning speed is 1100mm/s; filling profile laser power 250W and scanning speed 200mm/s; the outer wall scans laser 260W at a scanning speed of 250mm/s; scanning interval is 0.12mm, powder spreading thickness is 0.02mm, scanning area width is 6mm, and substrate temperature is 90 ℃;
the relative density of the Al alloy shown is 98.8%, the maximum tensile strength is 392.9MPa, the yield strength is 306.7MPa, and the elongation is 2.8%.
Comparative example 3
Al-Mg made by SLM forming 2 The Al alloy component of the Si-Si alloy part consists of 9% of Mg 2 Si,0% Si, and the balance Al. The alloy solidification interval is 45 ℃, and the heat sensitivity factor is 0.29 multiplied by 10 4 DEG C. Paving alloy powder on a substrate, and performing printing forming according to a three-dimensional model to obtain a complex part; wherein the laser parameters include: main body laser power 330W and scanning speed 650mm/s; the filling laser power of the upper surface and the lower surface is 260W, and the scanning speed is 1100mm/s; filling profile laser power 250W and scanning speed 200mm/s; the outer wall scans laser 260W at a scanning speed of 250mm/s; scanning interval is 0.12mm, powder spreading thickness is 0.02mm, scanning area width is 6mm, and substrate temperature is 90 ℃;
the relative density of the Al alloy shown is 98.2%, the maximum tensile strength is 344.0MPa, the yield strength is 300.2MPa, and the elongation is 1.0%.
Table 1 shows the properties of samples of examples of the present invention
The detection results shown in table 1 show that the invention can reduce the solidification interval and crack sensitivity factor of the aluminum alloy by adding fine powder Si particles, improve the formability of the aluminum alloy, achieve high relative density, and have no cracks and pores, but the addition amount of Si needs 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 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 (8)
1. Crack-free reinforced Al-Mg 2 The preparation method of the Si-Si alloy material is characterized in that: al-Mg 2 Si alloy powderUniformly mixing the powder with Si powder, paving on a substrate, and performing 3d printing and forming to obtain the composite material; the Si powder and Al-Mg 2 The mass ratio of the Si alloy powder is 1: 24-499;
the Al-Mg 2 The grain size of the Si alloy powder is 30-60 mu m, and the grain size of the Si powder is 10-25 mu m; the Al-Mg 2 The Si alloy powder comprises the following components in percentage by mass: 8-11% Mg 2 Si, the balance of Al;
the Al-Mg 2 The Si-Si alloy material comprises Mg with a main strengthening phase of 100-400 nm 2 Si and Si with the auxiliary strengthening phase of 100-200 nm; the main strengthening phase is semi-coherent with the Al matrix, and the auxiliary strengthening phase is precipitated around the cellular tissue.
2. A crack-free strengthened Al-Mg according to claim 1 2 The preparation method of the Si-Si alloy material is characterized in that: the Al-Mg 2 The purity of the Si alloy powder and the Si powder is more than or equal to 99.9 percent.
3. A crack-free strengthened Al-Mg according to claim 1 2 The preparation method of the Si-Si alloy material is characterized in that: the main parameters of the 3d printing forming process are as follows: the main body laser power is 310-350W, and the main body laser scanning speed is 600-800 mm/s; filling laser power of the upper surface and the lower surface is 250-280W, and scanning speed is 1000-1200 mm/s; filling profile laser power is 220-270W, and scanning speed is 100-300 mm/s; the outer wall scanning power is 250-300W, and the scanning speed is 200-400 mm/s; the scanning interval is 0.1-0.15 mm, the powder spreading thickness is 0.02-0.04 mm, the scanning area width is 5-8 mm, and the substrate temperature is 80-100 ℃.
4. A crack-free strengthened Al-Mg according to claim 2 2 The preparation method of the Si-Si alloy material is characterized in that: the Si powder and Al-Mg 2 The mass ratio of the Si alloy powder is 1: 70-80% of Al-Mg 2 Mg in Si alloy powder 2 When Si is 8.5-9.5%, the main parameters of the 3d printing forming process are as follows: the main body laser power is 320-340W, and the scanning speed is 600-700 mm/s; the laser power of the upper surface and the lower surface is 250-270W,the scanning speed is 1000-1100 mm/s; filling profile laser power 240-260W, scanning speed 150-250 mm/s, outer wall scanning laser 250-270W, and scanning speed 200-300 mm/s; the scanning interval is 0.1-0.14 mm, the powder spreading thickness is 0.02-0.03 mm, the scanning area width is 5-7 mm, and the substrate temperature is 80-100 ℃.
5. A crack-free strengthened Al-Mg according to claim 4 2 The preparation method of the Si-Si alloy material is characterized in that: the Si powder and Al-Mg 2 The mass ratio of the Si alloy powder is 1:76, al-Mg 2 Mg in Si alloy powder 2 When Si is 9%, the main parameters of the 3d printing forming process are as follows: main body laser power 330W and scanning speed 650mm/s; the filling laser power of the upper surface and the lower surface is 260W, and the scanning speed is 1100mm/s; filling profile laser power 250W, scanning speed 200mm/s, outer wall scanning laser 260W, and scanning speed 250mm/s; the scanning interval is 0.12mm, the powder spreading thickness is 0.02mm, the scanning area width is 6mm, and the substrate temperature is 90 ℃.
6. Crack-free reinforced Al-Mg 2 An Si-Si-based alloy characterized in that: the process according to any one of claims 1 to 5.
7. A crack-free strengthened Al-Mg according to claim 6 2 The Si-Si alloy material is characterized in that: setting interval is 25-39 deg.c, and heat sensitivity factor is 0.19-2.6X10 4 ℃。
8. A crack-free strengthened Al-Mg as claimed in claim 6 or 7 2 The application of the Si-Si alloy material is characterized in that: for the preparation of turbine blades.
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| CN110760724A (en) * | 2019-11-19 | 2020-02-07 | 中南大学 | Al-Mg with high Fe content prepared by selective laser melting2Si alloy and preparation method thereof |
| CN111957960A (en) * | 2020-08-12 | 2020-11-20 | 南方科技大学 | Selective laser melting forming method for heat crack-free precipitation strengthening high-temperature alloy |
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| WO2019090398A1 (en) * | 2017-11-13 | 2019-05-16 | Monash University | Procedure for post-heat treatment of aluminium-silicon-magnesium components made by selective laser melting (3d metal printing) |
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