CN115383133A - 3D printing aluminum alloy and modification method thereof - Google Patents
3D printing aluminum alloy and modification method thereof Download PDFInfo
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- CN115383133A CN115383133A CN202211053060.0A CN202211053060A CN115383133A CN 115383133 A CN115383133 A CN 115383133A CN 202211053060 A CN202211053060 A CN 202211053060A CN 115383133 A CN115383133 A CN 115383133A
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
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- B22F10/00—Additive manufacturing of workpieces or articles from metallic powder
- B22F10/60—Treatment of workpieces or articles after build-up
- B22F10/64—Treatment of workpieces or articles after build-up by thermal means
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B33—ADDITIVE MANUFACTURING TECHNOLOGY
- B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3-D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3-D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
- B33Y40/00—Auxiliary operations or equipment, e.g. for material handling
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- B—PERFORMING OPERATIONS; TRANSPORTING
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- B33Y—ADDITIVE MANUFACTURING, i.e. MANUFACTURING OF THREE-DIMENSIONAL [3-D] OBJECTS BY ADDITIVE DEPOSITION, ADDITIVE AGGLOMERATION OR ADDITIVE LAYERING, e.g. BY 3-D PRINTING, STEREOLITHOGRAPHY OR SELECTIVE LASER SINTERING
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- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
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Abstract
The invention provides a 3D printing aluminum alloy and a modification method thereof, which comprises the following steps: s1, forming an aluminum alloy sample by adopting a 3D printing technology; s2, carrying out solid solution treatment on the aluminum alloy sample, then carrying out aging treatment, and then carrying out water cooling; and S3, carrying out high-pressure torsional deformation on the aluminum alloy sample obtained in the step S2 to obtain the modified 3D printing aluminum alloy. The alloy has high hardness and high corrosion resistance.
Description
Technical Field
The invention relates to a 3D printing aluminum alloy and a modification method thereof, and belongs to the technical field of aluminum alloys.
Background
Because the aluminum alloy has the characteristics of low density, higher specific strength and specific stiffness, excellent processability and the like, the dosage of the aluminum alloy is second to that of steel. Wherein, the 7xxx aluminum alloy is mainly added with alloy elements Zn, mg and a small amount of Cu, belongs to the heat treatment strengthening medium and high strength aluminum alloy, and is widely applied to the fields of automobiles, aerospace, buildings, decoration and the like.
The problems of complex manufacturing process, long development period, serious material waste and the like exist in the process of forming the aluminum-based alloy part with a complex shape by using the traditional methods of milling, cutting, forging, electric machining and the like, and the SLM forming technology in 3D printing has great advantage in the aspect of directly manufacturing high-performance complex aluminum-based alloy parts. The SLM technology can realize the rapid adjustment of alloy formula, the rapid molding and manufacturing of material tissue, the manufacture of special-shaped components which cannot be obtained by the traditional manufacturing method, the composite molding of various materials and irreplaceable advancement. However, the reasonable SLM forming process of the aluminum-based alloy is still incomplete, the forming process is easy to be accompanied by cracking, oxidation, pores and the like, so that the formed part has serious defects, and meanwhile, the mechanical strength and the corrosion resistance of the formed alloy are difficult to be considered, the aluminum-based alloy part with complex high performance is difficult to be formed, and the SLM forming quality and deep popularization are seriously influenced.
Therefore, it is urgently needed to develop a modification method for 3D printing aluminum alloy to improve the comprehensive performance of the aluminum alloy.
Disclosure of Invention
The invention provides a 3D printing aluminum alloy and a modification method thereof, which can effectively solve the problems.
The invention is realized by the following steps:
a modification method of 3D printing aluminum alloy comprises the following steps:
s1, forming an aluminum alloy sample by adopting a 3D printing technology;
s2, carrying out solid solution treatment on the aluminum alloy sample, then carrying out aging treatment, and then carrying out water cooling;
and S3, carrying out high-pressure torsional deformation on the aluminum alloy sample obtained in the step S2 to obtain the modified 3D printing aluminum alloy.
In some embodiments, the aluminum alloy is a 7xxx series aluminum alloy.
In some embodiments, the 3D printing technology is to place the aluminum alloy powder in a 3D printing device, adjust the preheating temperature of the substrate and the powder spreading thickness of the aluminum alloy powder, perform powder spreading printing after performing scanning irradiation with laser, perform scanning irradiation with laser again after sintering, and annihilate the black oxide layer after the first laser irradiation.
In some embodiments, the printing parameters of the 3D printing technique are: the preheating temperature of the substrate is 120-180 ℃, the laser power is 350-390W, the scanning speed is 1100-1300mm/s, the scanning interval is 0.08-0.10mm, and the powder spreading thickness is 0.02-0.04mm.
In some embodiments, the aluminum alloy specimens were ground to a thickness of 0.85mm prior to solution treatment.
In some embodiments, the solution treatment is performed in a box-type resistance furnace at 480-500 ℃ for 1.5-2.5 hours.
In some embodiments, the aging treatment is carried out at a temperature of 110-130 ℃ for 22-26h.
In some embodiments, the high pressure torsional deformation is performed at a rotation speed of 0.5-5 revolutions and a pressure of 700-800MPa.
The 3D printing aluminum alloy prepared by the method.
The beneficial effects of the invention are:
according to the invention, the forming quality is improved through 3D printing of the aluminum alloy and through the processes of solution treatment, aging treatment and high-pressure torsional deformation, the sensitivity of the aluminum alloy to corrosion is effectively changed, the corrosion resistance and the mechanical strength of the alloy are improved, and the aluminum alloy with stronger mechanical property and better corrosion resistance is obtained.
Drawings
In order to more clearly illustrate the technical solutions of the embodiments of the present invention, the drawings that are required to be used in the embodiments will be briefly described below, it should be understood that the following drawings only illustrate some embodiments of the present invention and therefore should not be considered as limiting the scope, and for those skilled in the art, other related drawings can be obtained according to the drawings without inventive efforts.
Fig. 1 is a graph of vickers hardness of different samples 7075 made by SLM with respect to center distance according to an embodiment of the present invention.
FIG. 2 is a TEM image of a sample provided by an embodiment of the present invention. (a) TEM image of the untreated raw sample of comparative example 1; (b) TEM images of T6 heat treated and severely plastically deformed samples of example 1.
FIG. 3 is a Tafel curve of an electrochemical test of 7075 aluminum alloy manufactured by SLM according to an embodiment of the present invention.
Detailed Description
In order to make the objects, technical solutions and advantages of the embodiments of the present invention more apparent, the technical solutions of the embodiments of the present invention will be described clearly and completely with reference to the accompanying drawings of the embodiments of the present invention, and it is obvious that the described embodiments are some, but not all embodiments of the present invention. All other embodiments, which can be obtained by a person skilled in the art without any inventive step based on the embodiments of the present invention, are within the scope of the present invention. Thus, the following detailed description of the embodiments of the present invention, presented in the figures, is not intended to limit the scope of the invention, as claimed, but is merely representative of selected embodiments of the invention. All other embodiments, which can be obtained by a person skilled in the art without inventive efforts based on the embodiments of the present invention, are within the scope of protection of the present invention.
In the description of the present invention, the terms "first" and "second" are used for descriptive purposes only and are not to be construed as indicating or implying relative importance or implying any number of technical features indicated. Thus, a feature defined as "first" or "second" may explicitly or implicitly include one or more of that feature. In the description of the present invention, "a plurality" means two or more unless specifically defined otherwise.
The embodiment of the invention provides a modification method for 3D printing of aluminum alloy, which comprises the following steps:
s1, forming an aluminum alloy sample by adopting a 3D printing technology;
s2, carrying out solid solution treatment on the aluminum alloy sample, then carrying out aging treatment, and then carrying out water cooling;
and S3, carrying out high-pressure torsional deformation on the aluminum alloy sample obtained in the step S2 to obtain the modified 3D printing aluminum alloy.
In some embodiments, the 3D printing technology is an SLM printing technology, and the printing parameters are determined through multiple orthogonal experiments to solve the problem of high oxidation degree.
In some embodiments, the aluminum alloy is a 7xxx series aluminum alloy. The traditional 7xxx series aluminum alloy mainly has two main problems in the using process, one is that the corrosion resistance of the alloy is relatively poor, and the use safety of components can be seriously influenced by the corrosion behaviors of intergranular corrosion, stress corrosion and the like occurring at crystal boundaries; the other is the contradiction between stress corrosion Sensitivity (SCC) and strength of the 7xxx series aluminum alloy, namely, when the stress corrosion resistance of the alloy is better, the strength of the alloy is not high. The traditional heat treatment (solid solution + aging) can make the alloy obtain high mechanical properties, but the corrosion resistance is lower.
According to the embodiment of the invention, the grain size in the alloy is refined to be micron or nanometer in a mode of violent plastic deformation, a large amount of dislocation is introduced into the alloy by a deformation process, more nucleation particles are provided for the precipitation of eta' phase and eta phase in the next aging process, the rapid precipitation of a strengthening phase is promoted, and the strength of the alloy is greatly improved; in addition, the high density of dislocations introduced by the deformation hinders the movement of the precipitated phase, and similarly, the strength of the alloy can be improved. Therefore, the embodiment of the invention exerts the synergistic effect by the synergistic cooperation of deformation, solid solution and aging processes, regulates and controls the precipitated phase and dislocation in the aluminum alloy accurately, thereby improving the forming quality of the aluminum alloy, effectively changing the sensitivity of the aluminum alloy to corrosion, and improving the comprehensive properties of the alloy, such as corrosion resistance, mechanical strength and the like.
In some embodiments, the 3D printing technology is to place the aluminum alloy powder in a 3D printing device, adjust the preheating temperature of the substrate and the powder spreading thickness of the aluminum alloy powder, perform powder spreading printing after scanning irradiation with laser, perform scanning irradiation with laser again after sintering, annihilate the black oxide layer after the first laser irradiation, and bond the powder sintered entity with the substrate.
In some embodiments, the printing parameters of the 3D printing technique are: the preheating temperature of the substrate is 120-180 ℃, the laser power is 350-390W, the scanning speed is 1100-1300mm/s, the scanning interval is 0.08-0.10mm, and the powder spreading thickness is 0.02-0.04mm. The printing parameters can solve the problem of high oxidation degree and other defects.
In some embodiments, the aluminum alloy coupons were ground to a thickness of 0.85mm prior to solution treatment.
In some embodiments, the solution treatment is performed in a box-type resistance furnace, and the temperature of the solution treatment is 480-500 ℃, more preferably 480 ℃, 485 ℃, 490 ℃, 495 ℃, 500 ℃; the time of the solution treatment is 1.5-2.5h, preferably 1.5h, 1.8h, 2h, 2.2h and 2.5h.
In some embodiments, the aging treatment is carried out at a temperature of 110-130 ℃ for 22-26h. The temperature is more preferably 110 ℃, 115 ℃, 120 ℃, 125 ℃, 130 ℃. The time is more preferably 22h, 23h, 24h, 25h, and 26h.
In some embodiments, the high pressure torsional deformation has a rotation number of 0.5 to 5 rotations, and further preferably 0.5 rotation, 1 rotation, 2 rotations, 3 rotations, 5 rotations; the pressure is 700-800MPa, preferably 700MPa, 720MPa, 750MPa, 780MPa, 800MPa.
The embodiment of the invention provides a 3D printing aluminum alloy prepared by the method.
Experimental example 1: T6-R (490 ℃ for 2h solution treatment, 120 ℃ for 12h aging treatment, and severe plastic deformation 1T) heat treatment samples.
This experimental example provides a 7075 aluminum alloy powder, the 7075 aluminum alloy powder having the chemical composition (wt%): 0.4% Si, 0.5% Fe, 1.2-2.0% Cu, 0.3% Mn, 2.1-2.9% Mg, 0.2-0.3% Cr, 5.1-6.1% Zn, 0.2% Ti, and the balance Al.
The preparation method comprises the following steps:
(1) The experimental raw material is 7075 aluminum alloy powder, the aluminum alloy powder is molded by an SLM technology, the printing parameters are 150 ℃ substrate preheating, 385W laser power, scanning speed of 1200mm/s, powder laying thickness of 0.03mm, scanning distance of 0.09mm, twice repeated scanning, and the scanning parameters are the same. The test specimens were then cut off with a wire cutter and the thickness was ground to 0.85mm.
(2) Putting the sample into a box-type resistance furnace, carrying out solution treatment at 490 ℃ for 2h, then carrying out water cooling and taking out, carrying out aging treatment at 120 ℃ for 12h, and taking out after furnace cooling.
(3) And (3) carrying out severe plastic deformation on the sample, twisting for 1 turn and keeping the pressure at 750Mpa.
Comparative example 1: the non T6 (raw without T6 heat treatment) samples.
This comparative example provides a 7075 aluminum alloy powder, the 7075 aluminum alloy powder having a chemical composition (wt.%): 0.4% Si, 0.5% Fe, 1.2-2.0% Cu, 0.3% Mn, 2.1-2.9% Mg, 0.2-0.3% Cr, 5.1-6.1% Zn, 0.2% Ti, and the balance Al.
The preparation method comprises the following steps:
the experimental raw material is 7075 aluminum alloy powder, the aluminum alloy powder is molded by an SLM technology, the printing parameters are 150 ℃ substrate preheating, 385W laser power, scanning speed of 1200mm/s, powder laying thickness of 0.03mm, scanning distance of 0.09mm, twice repeated scanning, and the scanning parameters are the same. The test specimens were then cut off with a wire cutter and the thickness was ground to 0.85mm.
Comparative example 2: t6 (490 ℃, 2h solution treatment, 120 ℃ 12h aging treatment) heat treatment sample.
This experimental example provides a 7075 aluminum alloy powder, the 7075 aluminum alloy powder having the chemical composition (wt%): 0.4% Si, 0.5% Fe, 1.2-2.0% Cu, 0.3% Mn, 2.1-2.9% Mg, 0.2-0.3% Cr, 5.1-6.1% Zn, 0.2% Ti, and the balance Al.
The preparation method comprises the following steps:
(1) The experimental raw material is 7075 aluminum alloy powder, the aluminum alloy powder is molded by an SLM technology, the printing parameters are 150 ℃ substrate preheating, 385W laser power, scanning speed of 1200mm/s, powder laying thickness of 0.03mm, scanning distance of 0.09mm, twice repeated scanning, and the scanning parameters are the same. The test specimens were then cut off with a wire cutter and the thickness was ground to 0.85mm.
(2) Putting the sample into a box-type resistance furnace, carrying out solution treatment at 490 ℃ for 2h, then carrying out water cooling and taking out, carrying out aging treatment at 120 ℃ for 12h, and taking out after furnace cooling.
Comparative example 3: samples of NonT6-R (untreated + severe plastic deformation 0.5 revolutions).
This experimental example provides a 7075 aluminum alloy powder, the 7075 aluminum alloy powder having the chemical composition (wt%): 0.4% Si, 0.5% Fe, 1.2-2.0% Cu, 0.3% Mn, 2.1-2.9% Mg, 0.2-0.3% Cr, 5.1-6.1% Zn, 0.2% Ti, and the balance Al.
The preparation method comprises the following steps:
(1) The experimental raw material is 7075 aluminum alloy powder, the aluminum alloy powder is molded by an SLM technology, the printing parameters are 150 ℃ substrate preheating, 385W laser power, scanning speed of 1200mm/s, powder laying thickness of 0.03mm, scanning distance of 0.09mm, twice repeated scanning, and the scanning parameters are the same. The test specimens were then cut off with a wire cutter and the thickness was ground to 0.85mm.
(2) The sample is subjected to severe plastic deformation for 0.5 revolution under 750MPa.
Test example 1
Vickers hardness test
The load used in this experiment was 200kgf and the retention time was 10s. And determining the hardness of the sample by adopting a four-line method for the obtained indentation, and ensuring that the opposite vertexes of the obtained indentation are on the same straight line when determining the hardness value by adopting the four-line method. If the position does not deviate, the image can be adjusted by adjusting the camera.
In the experiment, 8 diameters are taken on the surface of a sample, and 19 equidistant points are selected on each diameter for hardness test so as to reduce errors and ensure the accuracy of the obtained hardness. The results of the experiment are shown in FIG. 1.
TEM experiment
Preparation of transmission sample a sample with original thickness of 7mm is polished to a sheet of 150 μm by using metallographic abrasive paper, and then a small piece with diameter of 3mm is obtained by punching; and then thinning the sample by using a double-spraying instrument, adding electrolyte into an electrolytic cell of the double-spraying electrolytic thinning device, wherein the solution used by double spraying is as follows: 25% nitric acid +75% methanol (volume fraction). Inserting the sample clamp into the center of an electrolytic cell, controlling the operating temperature to be about-25 ℃, adding liquid nitrogen into the electrolytic cell to rapidly cool, wherein the double-spraying voltage is 22V, the liquid flow is 41, and the light sensation value is 100. Tissue observation was performed using a FEI Talos F200S high resolution TEM at an acceleration voltage of 200KV. The results of the experiment are shown in FIG. 2.
Electrochemical corrosion
Polishing the surface of a 7075 aluminum alloy sample by using 240# to 2000# metallographic abrasive paper, removing an oxide layer and enabling the scratch directions to be consistent; the cleaning is carried out by using deionized water and alcohol wiping in sequence. And then cold inlaying, grinding a copper wire to remove a paint layer, connecting a copper wire to the surface of the test piece in a soldering manner, sleeving a heat-shrinkable tube, sleeving a layer of heat-shrinkable tube after the heat-shrinkable tube is heated and shrunk by a lighter, adjusting the wire to be vertical to the test piece, placing the test piece in a cold inlaying mold, weighing cold inlaying materials, pouring the materials after rapid mixing, and detecting whether the cold inlaying sample is conductive or not by a universal meter after curing and demolding.
The open circuit potential, electrochemical impedance profile and polarization curve were measured using an electrochemical method to study the behavior of 7075 aluminum alloy in 3.5wt% NaCl corrosion solution. The experimental alloy specimens were electrochemically tested using the IVIUM electrochemical workstation. A three-electrode system was used: working electrode, (saturated calomel) reference electrode and (platinum) auxiliary electrode, and each electrode wire is connected with the corresponding output end of the electrochemical workstation. Firstly, soaking in a sample solution for 3600s to obtain a final stable value as an open-circuit potential; after balancing, electrochemical impedance spectroscopy is performed to measure the frequency range 10 5 ～10 -2 Hz; then, potentiodynamic polarization scanning is carried out in the potential range of-0.2V to-1.8V. The medium solution is a 3.5wt% NaCl solution prepared by deionized water. And (5) subsequent data processing, selecting a corresponding fitting circuit according to the impedance graph, fitting by means of Zview software, and recording data and errors. The results of the experiment are shown in FIG. 3.
As can be seen from fig. 1, T6 (heat treated only) has a greater hardness than non T6 (original sample); the hardness of the NonT6-R (subjected to severe plastic deformation only) was greater than that of the NonT6 (original sample); the hardness of T6-R (heat treated and severe plastic deformation) was greater than that of NonT6 (original sample), and greater than that of both T6 (heat treated only) and NonT6-R (severe plastic deformation only). Therefore, the heat treatment and the severe plastic deformation both have a remarkable hardness enhancing effect on the SLM 7075 aluminum alloy, and the heat treatment and the severe plastic deformation are cooperated to play a role in enhancing the hardness.
As can be seen from fig. 2, (a) is a TEM image of 7075 aluminum alloy (untreated raw sample) of comparative example 1, and (b) is a TEM image of 7075 aluminum alloy after T6 heat treatment and severe plastic deformation of experimental example 1. It can be seen that after T6 heat treatment, a large amount of dislocations appear on the sample, the dislocations are increased due to severe plastic deformation, the phase pinning dislocations are precipitated to make slippage difficult due to mutual obstruction of dislocation movement, and the heat treatment and the severe plastic deformation play a synergistic effect, so that the strength is improved.
As can be seen from the electrochemical polarization curve of fig. 3, T6 (heat treated only) has a greater corrosion resistance potential than non T6 (original sample); the corrosion resistance potential of the NonT6-R (subjected to only severe plastic deformation) is greater than that of the NonT6 (original sample); the corrosion resistance potential of T6-R (subjected to heat treatment and severe plastic deformation) was higher than that of NonT6 (original sample), and was higher than that of both T6 (subjected to heat treatment only) and NonT6-R (subjected to severe plastic deformation only), and thus it was found that both heat treatment and severe plastic deformation could improve the corrosion resistance of the SLM 7075 aluminum alloy. The sum of the increase in T6 over NonT6 and the increase in NonT6-R over NonT6 was less than the increase in T6-R over NonT6, indicating that both heat treatment and severe plastic deformation act synergistically.
The above description is only a preferred embodiment of the present invention and is not intended to limit the present invention, and various modifications and changes may be made by those skilled in the art. Any modification, equivalent replacement, or improvement made within the spirit and principle of the present invention should be included in the protection scope of the present invention.
Claims (9)
1. A modification method for 3D printing aluminum alloy is characterized by comprising the following steps:
s1, forming an aluminum alloy sample by adopting a 3D printing technology;
s2, carrying out solid solution treatment on the aluminum alloy sample, then carrying out aging treatment, and then carrying out water cooling;
and S3, carrying out high-pressure torsional deformation on the aluminum alloy sample obtained in the step S2 to obtain the modified 3D printing aluminum alloy.
2. The method of claim 1, wherein the aluminum alloy is a 7xxx series aluminum alloy.
3. The method of claim 1, wherein the 3D printing technology comprises the steps of placing aluminum alloy powder in a 3D printing device, adjusting the preheating temperature of the substrate and the powder laying thickness of the aluminum alloy powder, performing scanning irradiation by using laser, performing powder laying printing, performing scanning irradiation by using laser again after sintering, and annihilating the black oxide layer after the first laser irradiation.
4. The method of claim 3, wherein the printing parameters of the 3D printing technique are: the preheating temperature of the substrate is 120-180 ℃, the laser power is 350-390W, the scanning speed is 1100-1300mm/s, the scanning interval is 0.08-0.10mm, and the powder spreading thickness is 0.02-0.04mm.
5. The method of claim 1, wherein the aluminum alloy coupon is ground to a thickness of 0.85mm prior to solution treatment.
6. The method according to claim 1, characterized in that the solution treatment is carried out in a box-type resistance furnace at a temperature of 480-500 ℃ for a time of 1.5-2.5h.
7. The method according to claim 1, wherein the ageing treatment is carried out at a temperature of 110-130 ℃ for a time of 22-26 hours.
8. The method according to claim 1, wherein the high pressure torsional deformation is performed at a rotation speed of 0.5-5 revolutions and a pressure of 700-800Mpa.
9. A 3D printed aluminum alloy produced by the method of any of claims 1 to 8.
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Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
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| US20170204503A1 (en) * | 2016-01-14 | 2017-07-20 | Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) | Aluminum alloy structural part, method for producing the same, and aluminum alloy sheet |
| CN108998709A (en) * | 2018-08-21 | 2018-12-14 | 南京理工大学 | A kind of preparation method of aluminium alloy |
| CN111842914A (en) * | 2020-06-30 | 2020-10-30 | 同济大学 | 3D printing process method of high-strength aluminum-copper alloy |
| CN111922347A (en) * | 2020-07-31 | 2020-11-13 | 飞而康快速制造科技有限责任公司 | Heat treatment method for 3D printing aluminum alloy |
| CN113774297A (en) * | 2021-09-08 | 2021-12-10 | 厦门理工学院 | Method for improving corrosion resistance and mechanical property of aluminum alloy based on severe plastic deformation and high-performance corrosion-resistant aluminum alloy |
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- 2022-08-31 CN CN202211053060.0A patent/CN115383133A/en active Pending
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| US20170204503A1 (en) * | 2016-01-14 | 2017-07-20 | Kabushiki Kaisha Kobe Seiko Sho (Kobe Steel, Ltd.) | Aluminum alloy structural part, method for producing the same, and aluminum alloy sheet |
| CN108998709A (en) * | 2018-08-21 | 2018-12-14 | 南京理工大学 | A kind of preparation method of aluminium alloy |
| CN111842914A (en) * | 2020-06-30 | 2020-10-30 | 同济大学 | 3D printing process method of high-strength aluminum-copper alloy |
| CN111922347A (en) * | 2020-07-31 | 2020-11-13 | 飞而康快速制造科技有限责任公司 | Heat treatment method for 3D printing aluminum alloy |
| CN113774297A (en) * | 2021-09-08 | 2021-12-10 | 厦门理工学院 | Method for improving corrosion resistance and mechanical property of aluminum alloy based on severe plastic deformation and high-performance corrosion-resistant aluminum alloy |
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