CN115747584A - Crack-free reinforced Al-Mg 2 Si-Si alloy material and preparation method and application thereof - Google Patents
Crack-free reinforced Al-Mg 2 Si-Si alloy material and preparation method and application thereof Download PDFInfo
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- 229910018134 Al-Mg Inorganic materials 0.000 title claims abstract description 73
- 229910018467 Al—Mg Inorganic materials 0.000 title claims abstract description 73
- 229910008045 Si-Si Inorganic materials 0.000 title claims abstract description 37
- 229910006411 Si—Si Inorganic materials 0.000 title claims abstract description 37
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Abstract
The invention discloses a crack-free reinforced Al-Mg 2 Si-Si alloy material, preparation method and application thereof. The alloy material adopts Al-Mg with different grain diameters 2 The Si powder and the Si powder are mixed and prepared by an additive manufacturing process, so that the rapid forming of the high-toughness alloy is realized. The alloy material is based on the synergistic effect among the components of the raw materials and on the main strengthening phase Al-Mg 2 The coherent action between Si and a 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, and the solidification interval of the alloy material is greatly reduced, thereby ensuring the mechanical property of the alloy material and realizing the effect of no crack and no pore. The alloy material provided by the invention effectively solves the problems of low strength, large solidification interval, 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 crack-free reinforced Al-Mg 2 A Si-Si alloy material, a preparation method and application thereof, belonging to the technical field of new material preparation.
Background
Aluminum alloy is the most widely used metal structural material at present, and has the advantages of 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, the aluminum alloy structural part is mainly manufactured by the traditional methods of casting, forging, extruding, 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 generation efficiency, low design freedom degree 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 target in the future.
Selective Laser Melting (SLM) is considered to be one of the most promising Additive Manufacturing (AM) techniques. SLM utilizes a high energy laser beam to completely melt metal powder in a protective atmosphere along the laser path, and this molten metal solidifies rapidly. By repeating this step, the layers are overlapped one by one, and a three-dimensional component is finally formed. This layering approach has unique advantages in the integration of complex structural and thin-walled components. SLM is a non-equilibrium solidification process that increases the solid solution limit of the alloying elements in the matrix and may produce metastable phases and fine precipitates. However, in the SLM manufacturing process, due to high and rapid cooling, great thermal stress is easily generated, which causes defects such as periodic cracks and shrinkage cavities of a sample, so that the types of commercial aluminum alloys are relatively limited; at present, the Al alloy which is most commonly melted by laser in a selected area is mainly Al-Si alloy, such as Al-12Si and AlSi10Mg, the formability is good, but the mechanical property is not high, and the high strength and toughness requirements of the current industrial Al alloy cannot be met; on the other hand, the 2-, 6-and 7-series aluminum alloys having high toughness have cracks due to excessively large solidification regions, and are inferior in formability. Requires addition of a noble metal such as Sc or Zr or TiB 2 Ceramic particles of SiC, tiN, etc. increase the formability, which increases the production cost, and are not suitable for industrial mass production. Therefore, the development of a novel high-strength and high-toughness aluminum alloy complex part with low cost, narrow solidification range and no crack by utilizing the characteristic of extreme metallurgical non-equilibrium solidification of SLM forming is of great significance.
Disclosure of Invention
In view of the problems in the prior art, the first object of the present invention is to provide a crack-free strengthened Al-Mg 2 Si-Si alloy material, which adopts Si powder to Al-Mg 2 Si modified based on second phase particles Mg 2 The Si and the Si have synergistic strengthening effect, so that the fluidity of the alloy in a molten state is improved, and the solidification interval of the alloy material is greatly reduced, thereby ensuring the mechanical property of the alloy material and realizing the effect of no crack and no pore.
The second purpose of the invention is to provide a crack-free reinforced Al-Mg 2 SiPreparation method of-Si alloy material, which adopts Al-Mg with different grain diameters 2 The Si powder and the Si powder are prepared by an additive manufacturing process based on the synergistic effect of the components of the raw materials, and the formability and the mechanical property of the material are controlled by adjusting process parameters, so that the rapid forming of the high-strength and high-toughness alloy is realized.
The third purpose of the invention is to provide a crack-free reinforced Al-Mg 2 The application of the Si-Si series alloy material is used for preparing turbine blades. The alloy material provided by the invention can realize the compactness and the obdurability of the alloy based on the semi-coherent action of the main strengthening phase and the precipitation of the auxiliary strengthening phase without additionally adding noble metal elements such as Sc, zr and the like, ceramic particles and strengthening elements Cu and Zn, and tests show that the alloy material provided by the invention has the advantages of 99.8% of relative density, no crack, 484.3MPa of maximum tensile strength, 386.1MPa of yield strength and 7.85% of elongation and meets the performance requirements of turbine blades.
In order to achieve the technical purpose, the invention provides a crack-free reinforced Al-Mg 2 Preparation method of Si-Si series alloy material, al-Mg 2 Uniformly mixing Si alloy powder and Si powder, laying the mixture on a substrate, and printing and forming the mixture for 3d to obtain the Si-based composite material; the Si powder and Al-Mg 2 The mass ratio of the Si alloy powder is 1:24 to 499.
The preparation method provided by the invention adopts Al-Mg with different grain diameters 2 The Si powder and the Si powder are based on the synergistic effect of the components in the raw materials, the additive manufacturing process is adopted, and the formability and the mechanical property of the material are controlled by adjusting the process parameters, so that the rapid forming of the 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 diameter of Si powder adopted in the preparation method provided by the invention is smaller than that of Al-Mg 2 The addition of Si alloy powder and fine powder can reduce the particle gap and improve the apparent density, thereby improving the density and mechanical property of the formed material.
The grain diameter of the raw materials adopted by the invention is strictLattice is performed as above if Al-Mg 2 The excessively large grain size of the Si powder causes the surface roughness of the metal sample obtained by printing to become high; if the particle size of the Si powder is too large, the Si powder is likely to be adhered and agglomerated, which results in a decrease in powder flowability and a decrease in moldability.
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 has poor melting fluidity, the solidification interval is too large, and the heat sensitive factor is too high, so that the poor formability is caused; when the addition ratio of Si is too large, on the one hand, the generated eutectic phase increases, so that the elongation of the alloy is low; on the other hand, due to Al-Mg 2 The Si content is too low to degrade mechanical properties.
As a preferred embodiment, the Al-Mg 2 The Si alloy powder comprises the following components in percentage by mass: 8 to 11% of Mg 2 Si, and the balance being Al.
As a preferred embodiment, 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 and 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 the upper surface and the lower surface is 250-280W, and the scanning speed is 1000-1200 mm/s; the filling profile laser power is 220-270W, and the 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 distance 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 of Al-Mg 2 Mg in Si alloy powder 2 When the Si content is 8.5-9.5%, the main parameters of the 3d printing and 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, and the scanning speed is 1000-1100 mm/s; the filling profile 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; scanning interval of 0.1-0.14 mm, spreading powderThe thickness is 0.02-0.03 mm, the width of the scanning area is 5-7 mm, and the temperature of the substrate 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 and forming process are as follows: the laser power of the main body is 330W, and the scanning speed is 650mm/s; the filling laser power of the upper surface and the lower surface is 260W, and the scanning speed is 1100mm/s; the filling profile laser power is 250W, the scanning speed is 200mm/s, the outer wall scanning laser is 260W, and the scanning speed is 250mm/s; the scanning distance is 0.12mm, the powder spreading thickness is 0.02mm, the scanning area width is 6mm, and the substrate temperature is 90 ℃.
The Si and Al-Mg provided by the invention 2 In the mass ratio range of Si, along with the increase of Si content, the melting temperature of the alloy is reduced, and the fluidity is improved, so that the selected laser power is lower, the scanning speed is higher, the scanning distance is larger, the laser energy density is low, and the formability is better; and with Al-Mg 2 Mg in Si 2 The Si content is increased, the required laser energy density is high, the laser power is larger, the scanning speed is smaller, the scanning distance is smaller, the formability is good, and therefore, the Si content and the Mg are different 2 The selection of the process parameters for Si should be strictly in accordance with the requirements of the present invention.
The invention also provides crack-free reinforced Al-Mg 2 An Si-Si alloy obtained by any one of the above-described production methods.
As a preferred embodiment, the Al-Mg 2 The Si-Si alloy material contains Mg with a main strengthening phase of 100-400 nm 2 Si and Si with the auxiliary strengthening phase of 100-200 nm.
In a preferred embodiment, the primary strengthening phase is semi-coherent with the Al matrix, and the secondary strengthening phase is precipitated around the cellular structure.
The main strengthening precipitated phase and the matrix boundary are in a coherent relationship, which is beneficial to the dislocation smoothly cutting second phase particles so as to improve the strength and the plasticity, and the auxiliary strengthening precipitated phase is precipitated around the cellular structure 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 interval of the Si-Si alloy material is 25-39 ℃, and the thermal sensitivity factor is 0.19-2.6 multiplied by 10 4 ℃。
Thermal cracking generally occurs at solids fractions above 0.9 at the end of solidification, and a smaller solidification range indicates lower crack sensitivity and better formability according to the non-equilibrium Scheil model. The solidification intervals of Al-Cu of 2 series are 141.7 ℃, al-Mg-Si of 6 series is 114 ℃ and Al-Zn-Mg-Cu of 7 series is 168.4 ℃. Al-Mg of the invention 2 The solidification interval of Si-Si is only 25-39 deg.C, and the thermal sensitive factor is 0.19-2.6X 10 4 The excellent forming performance of the alloy material is ensured based on the synergistic effect of the two components, so that the alloy material prepared by additive manufacturing has no crack pores and high relative density.
The solidification region and the heat sensitive factor of the alloy material provided by the invention are strictly executed according to the requirements, and when the solidification region and the heat sensitive factor are too high, the hot cracking tendency is serious, cracks are easy to generate, and the forming performance is poor.
The invention also provides crack-free reinforced Al-Mg 2 The application of the Si-Si series alloy material is used for preparing turbine blades.
The alloy material provided by the invention controls the forming through a solidification interval and a heat sensitive factor, and meanwhile, the second phase particles Mg 2 The combination of good formability and mechanical property is realized by the cooperative reinforcement of Si and the adjustment of process parameters, and the goal of the cooperative formability is reached; the alloy material can realize the production of complex parts and components, and meets the mechanical requirements of light materials such as aerospace, high-speed rails 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 Si modified based on second phase particles Mg 2 The Si and the Si have synergistic strengthening effect, so that the fluidity of the alloy in a molten state is improved, and the solidification interval of the alloy material is greatly reduced, thereby ensuring the mechanical property of the alloy material and realizing the effect of no crack and no pore.
2、In the technical scheme provided by the invention, al-Mg with different grain diameters is adopted 2 The Si powder and the Si powder are prepared by an additive manufacturing process based on the synergistic effect of the components of the raw materials, and the formability and the mechanical property of the material are controlled by adjusting 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 alloy material is based on the semi-coherent action between the main strengthening phase and the matrix and the precipitation of the auxiliary strengthening phase, noble metal elements such as Sc and Zr, ceramic particles and strengthening elements Cu and Zn are not required to be additionally added, so that the compactness and the obdurability of the alloy can be realized, and through tests, the alloy material provided by the invention has the advantages that the relative density is 99.8%, no crack exists, the maximum tensile strength is 484.3MPa, the yield strength is 386.1MPa, the elongation is 7.85%, and the performance requirements of turbine blades are met.
Drawings
FIG. 1 shows Al-Mg as described in example 3 2 A microstructure view of the Si — Si alloy powder;
FIG. 2 shows Al-Mg in example 3 and comparative examples 1 and 3 2 A gold phase diagram of Si-Si;
wherein FIG. 2 (a) is a metallographic graph of an alloy obtained in comparative example 3, FIG. 2 (b) is a metallographic graph of an alloy obtained in comparative example 1, and FIG. 2 (c) is a metallographic graph of an alloy obtained in example 3;
FIG. 3 shows Al-Mg described in example 3 2 TEM image of Si-Si;
FIG. 4 is a graph showing tensile properties of alloys obtained in examples 1 to 4 and comparative examples 1 to 3;
FIG. 5 is a turbine blade made of the alloy material obtained in example 3;
from FIG. 1, al-Mg with Si particles added can be seen 2 The powder morphology of Si-Si;
as can be seen from fig. 2, (a) is a gold phase diagram printed from an aluminum alloy to which no Si particles are added, and there are a large number of defects such as crack voids; (b) Is Al-Mg without using optimal process parameters 2 A Si-Si printed gold phase diagram, with a certain amount of porosity present; (c) The result of a gold phase diagram printed for adding the optimal Si particles and the optimal process parameters shows that the alloy has no cracks and pores and high relative density;
from FIG. 3, it can be seen that 100-400 nmMg are distributed in a network 2 Si and 100-200 nm Si;
from FIG. 4, the tensile properties of each of the examples and comparative examples can be seen;
from fig. 5, it can be seen that the complex parts with good formability, no cracks and excellent mechanical properties can be prepared by using the optimally added fine powder Si particles and the optimal printing process parameters.
Detailed Description
The present invention will be described in detail below with reference to the drawings and embodiments, and the embodiments of the present invention are not to be considered limited to the description. For those skilled in the art to which the invention pertains, several simple deductions or substitutions can be made without departing from the spirit of the invention, and all shall be considered as belonging to the protection scope of the invention.
Example 1
Al-Mg produced by SLM forming 2 Said Al alloy component of the Si-Si alloy parts is composed of 8% Mg 2 Si,0.5%, the balance Al. The powder is composed of coarse powder Al-Mg with average particle diameter of 30-60 μm 2 Si and 10-25 μm fine powder Si. The alloy solidification interval is 36 ℃, and the heat sensitive factor is 0.24 multiplied by 10 4 DEG C. Mixing Al-Mg 2 The Si-Si alloy powder is laid on the substrate and is printed and formed according to the three-dimensional model to obtain a complex part; wherein the laser parameters include: the main body laser power is 310W, and the main body laser scanning speed is 600mm/s; the filling laser power of the upper surface and the lower surface is 250W, and the scanning speed is 1000mm/s; the filling profile laser power is 220W, and the scanning speed is 100mm/s; the filling profile laser power is 240W, and the scanning speed is 200mm/s; the scanning power of the outer wall is 250W, and the scanning speed is 200mm/s; the scanning distance is 0.1mm, the powder spreading thickness is 0.02mm, the width of a scanning area is 5mm, and the temperature of the substrate is 90 DEG C
The Al alloy shown has a relative density of 99.2%, a maximum tensile strength of 439.2MPa, a yield strength of 352.6MPa, and an elongation of 5.64%.
Example 2
Al-Mg prepared by SLM (Selective laser melting) forming 2 Said Al alloy component of the Si-Si alloy parts is composed of 9% Mg 2 Si,0.5% by weight, si, balance Al. The powder is coarse powder Al-Mg with average particle size of 30-60 μm 2 Si and fine powder Si of 15-25 μm. The alloy solidification interval is 31 deg.C, and the heat sensitive factor is 0.22X 10 4 DEG C. Mixing Al-Mg 2 The Si-Si alloy powder is laid on the substrate and is printed and formed according to the three-dimensional model to obtain a complex part; wherein the laser parameters include: the main body laser power is 330W, and the main body laser scanning speed is 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; the filling profile laser power is 240W, and the scanning speed is 100mm/s; the scanning power of the outer wall is 250W, and the scanning speed is 200mm/s; the scanning distance is 0.1mm, the powder spreading thickness is 0.02mm, the width of a scanning area is 5mm, and the temperature of the substrate is 90 DEG C
The Al alloy shown has a relative density of 99.5%, a maximum tensile strength of 458.2MPa, a yield strength of 345.2MPa, and an elongation of 8.1%.
Example 3
Al-Mg produced by SLM forming 2 Said Al alloy component of the Si-Si alloy parts is composed of 9% Mg 2 Si,1.3% by weight, si, balance Al. The powder is composed of coarse powder Al-Mg with average particle diameter of 30-60 μm 2 Si and 10-25 μm fine powder Si. The alloy solidification interval is 25 ℃, and the heat sensitive factor is 0.19 multiplied by 10 4 DEG C. Mixing Al-Mg 2 The Si-Si alloy powder is laid on the substrate and is printed and formed according to the three-dimensional model to obtain a complex part; wherein the laser parameters include: the laser power of the main body is 330W, and the scanning speed is 650mm/s; the filling laser power of the upper surface and the lower surface is 260W, and the scanning speed is 1100mm/s; the filling profile laser power is 250W, and the scanning speed is 200mm/s; scanning the outer wall with 260W laser at a scanning speed of 250mm/s; the scanning distance is 0.12mm, the powder spreading thickness is 0.02mm, the scanning area width is 6mm, and the substrate temperature is 90 ℃;
the printed complex part was a turbine blade and the Al alloy shown had a relative density of 99.8%, no cracks, a maximum tensile strength of 484.3MPa, a yield strength of 386.1MPa, and an elongation of 7.85%.
Example 4
Al-Mg produced by SLM forming 2 The Al alloy component of the Si-Si alloy part is calculated from 11% of Mg 2 Si,4% Si, the balance Al. The powder is composed of coarse powder Al-Mg with average particle diameter of 30-60 μm 2 Si and 10-25 μm fine powder Si. The alloy solidification interval is 39 ℃, and the heat sensitive factor is 0.26 multiplied by 10 4 DEG C. Mixing Al-Mg 2 The Si-Si alloy powder is laid on the substrate and is printed and formed according to the three-dimensional model to obtain a complex part; wherein the laser parameters include: the laser power of the main body is 350W, and the 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; scanning laser 280W on the outer wall at the scanning speed of 400mm/s; the scanning distance is 0.15mm, the powder spreading thickness is 0.04mm, the scanning area width is 8mm, and the substrate temperature is 90 ℃;
the Al alloy shown has a relative density of 99.1%, a maximum tensile strength of 461.8MPa, a yield strength of 357.8MPa, and an elongation of 5.2%.
Comparative example 1
Al-Mg produced by SLM forming 2 The Al alloy component of the Si-Si alloy part is calculated from 9% of Mg 2 Si,1.3% by weight, si, balance Al. The powder is composed of coarse powder Al-Mg with average particle diameter of 30-60 μm 2 Si and 10-25 μm fine powder Si. The alloy solidification interval is 25 ℃, and the heat sensitive factor is 0.19 multiplied by 10 4 DEG C. Mixing Al-Mg 2 The Si-Si alloy powder is laid on the substrate and is printed and formed according to the three-dimensional model to obtain a complex part; wherein the laser parameters include: the laser power of the main body is 390W, and the scanning speed is 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; scanning the outer wall with laser of 300W at the scanning speed of 400mm/s; the scanning distance is 0.2mm, the powder spreading thickness is 0.05mm, the scanning area width is 6mm, and the substrate temperature is 70 ℃;
the Al alloy shown has a relative density of 99.6%, a maximum tensile strength of 414.0MPa, a yield strength of 328.2MPa, and an elongation of 3.3%.
Comparative example 2
Al-Mg produced by SLM forming 2 The Al alloy component of the Si-Si alloy part is calculated from 9% of Mg 2 Si,6% Si, balance Al. The alloy solidification interval is 45 ℃, and the heat sensitive factor is 0.29 multiplied by 10 4 DEG C. Mixing Al-Mg 2 The Si-Si alloy powder is laid on the substrate and is printed and formed according to the three-dimensional model to obtain a complex part; wherein the laser parameters include: the laser power of the main body is 330W, and the scanning speed is 650mm/s; the filling laser power of the upper surface and the lower surface is 260W, and the scanning speed is 1100mm/s; the filling profile laser power is 250W, and the scanning speed is 200mm/s; scanning the outer wall with 260W laser at a scanning speed of 250mm/s; the scanning distance is 0.12mm, the powder spreading thickness is 0.02mm, the scanning area width is 6mm, and the substrate temperature is 90 ℃;
the Al alloy shown has a relative density of 98.8%, a maximum tensile strength of 392.9MPa, a yield strength of 306.7MPa, and an elongation of 2.8%.
Comparative example 3
Al-Mg produced by SLM forming 2 Said Al alloy component of the Si-Si alloy parts is composed of 9% Mg 2 Si,0% Si, the balance Al. The alloy solidification interval is 45 ℃, and the heat sensitive factor is 0.29 multiplied by 10 4 DEG C. Paving alloy powder on a substrate, and printing and forming according to a three-dimensional model to obtain a complex part; wherein the laser parameters include: the laser power of the main body is 330W, and the scanning speed is 650mm/s; the filling laser power of the upper surface and the lower surface is 260W, and the scanning speed is 1100mm/s; the filling profile laser power is 250W, and the scanning speed is 200mm/s; scanning the outer wall with 260W laser at a scanning speed of 250mm/s; the scanning distance is 0.12mm, the powder spreading thickness is 0.02mm, the scanning area width is 6mm, and the substrate temperature is 90 ℃;
the Al alloy shown has a relative density of 98.2%, a maximum tensile strength of 344.0MPa, a yield strength of 300.2MPa, and an elongation of 1.0%.
Table 1 shows the properties of the samples of examples of the present invention
The detection results shown in table 1 show that the addition of fine powder Si particles can reduce the solidification interval and crack sensitive factors of the aluminum alloy, improve the formability, achieve high relative density and have no cracks and pores, but strictly control the addition amount of Si; simultaneously, selecting laser melting printing parameters; the combination of these two results in high strength and elongation of the aluminum alloy.
The foregoing is only a preferred embodiment of the present invention, and it should be noted that, for those skilled in the art, various improvements and modifications can be made without departing from the principle of the present invention, and these improvements and modifications should also be construed as the protection scope of the present invention.
Claims (10)
1. Crack-free reinforced Al-Mg 2 The preparation method of the Si-Si series alloy material is characterized by comprising the following steps: mixing Al-Mg 2 Uniformly mixing Si alloy powder and Si powder, laying the mixture on a substrate, and printing and forming the mixture by 3d to obtain the product; the Si powder and Al-Mg 2 The mass ratio of the Si alloy powder is 1:24 to 499.
2. The crack-free strengthened Al-Mg as claimed in claim 1 2 The preparation method of the Si-Si series alloy material is characterized by comprising the following steps: the Al-Mg 2 The grain diameter of the Si alloy powder is 30-60 mu m, and the grain diameter 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 to 11% of Mg 2 Si, and the balance being Al; 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. The crack-free strengthened Al-Mg as claimed in claim 1 2 The preparation method of the Si-Si series alloy material is characterized by comprising the following steps: the main parameters of the 3d printing and 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 filling laser power of the upper surface and the lower surface is 250-280W, and the scanning speed is 1000-1200 mm/s; the filling profile laser power is 220-270W, and the scanning speed is 100-300 mm/s; outer wall scanning power 250E300W, and the scanning speed is 200-400 mm/s; the scanning distance 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. The crack-free strengthened Al-Mg as claimed in claim 2 2 The preparation method of the Si-Si series alloy material is characterized by comprising the following steps: the Si powder and Al-Mg 2 The mass ratio of the Si alloy powder is 1:70 to 80 of Al-Mg 2 Mg in Si alloy powder 2 When the Si content is 8.5-9.5%, the main parameters of the 3d printing and forming process are as follows: the main body laser power is 320-340W, and the scanning speed is 600-700 mm/s; the filling laser power of the upper surface and the lower surface is 250-270W, and the scanning speed is 1000-1100 mm/s; the filling profile 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 distance 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. The crack-free strengthened Al-Mg as claimed in claim 4 2 The preparation method of the Si-Si series alloy material is characterized by comprising the following steps: 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 and forming process are as follows: the laser power of the main body is 330W, and the scanning speed is 650mm/s; the filling laser power of the upper surface and the lower surface is 260W, and the scanning speed is 1100mm/s; the power of the filling profile laser is 250W, the scanning speed is 200mm/s, the outer wall of the filling profile laser scans 260W, and the scanning speed is 250mm/s; the scanning distance 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 alloy characterized by: the method according to any one of claims 1 to 5.
7. The crack-free strengthened Al-Mg as claimed in claim 6 2 An Si-Si alloy material characterized by: including principal intensityChemical phase of 100-400 nm Mg 2 Si and the auxiliary strengthening phase is 100-200 nm of Si.
8. The crack-free strengthened Al-Mg as claimed in claim 7 2 An Si-Si alloy material characterized by: the primary strengthening phase is semi-coherent with the Al matrix, and the secondary strengthening phase is precipitated around the cellular structure.
9. The crack-free strengthened Al-Mg as claimed in claim 6 2 An Si-Si alloy material characterized by: the solidification interval is 25-39 deg.C, and the thermal sensitive factor is 0.19-2.6X 10 4 ℃。
10. A crack free strengthened Al-Mg as claimed in claims 6 to 9 2 The application of the Si-Si series alloy material is characterized in that: used for preparing turbine blades.
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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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| 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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