CN112921219B - Aluminum alloy, preparation method thereof and aluminum alloy structural member - Google Patents

Aluminum alloy, preparation method thereof and aluminum alloy structural member Download PDF

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Publication number
CN112921219B
CN112921219B CN202110092933.8A CN202110092933A CN112921219B CN 112921219 B CN112921219 B CN 112921219B CN 202110092933 A CN202110092933 A CN 202110092933A CN 112921219 B CN112921219 B CN 112921219B
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aluminum alloy
content
alloy
structural
strength
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CN112921219A (en
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郭强
王梦得
安维
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BYD Co Ltd
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BYD Co Ltd
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    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C21/00Alloys based on aluminium
    • C22C21/10Alloys based on aluminium with zinc as the next major constituent
    • CCHEMISTRY; METALLURGY
    • C22METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22CALLOYS
    • C22C1/00Making alloys
    • C22C1/02Making alloys by melting
    • C22C1/026Alloys based on aluminium

Abstract

The application provides an aluminum alloy, a preparation method thereof and an aluminum alloy structural member. The aluminum alloy includes; 8.0-13.0 wt% Si; 2.0-3.0 wt% Cu; 3.0-5.0 wt% Zn; 0.6-0.9 wt% Mg; 0.5-0.8 wt% Mn; 0.1-0.3 wt% Fe; 0.05 to 0.35 wt.% Zr; 0.01-0.05 wt% Ti; 0.005-0.04 wt% Sr; 0.001-0.02 wt% Cr; 0.01-0.02 wt% Ga; 0.001-0.35 wt% Er; 0.005-0.1 wt% Ni; the balance of Al and inevitable impurities; wherein the weight content ratio of Er to Zr is 0.01-1.0: 1. The aluminum alloy has high yield strength, good ductility and excellent tensile strength by controlling the composition and content of alloy elements, and is suitable for structural members with high requirements on strength, such as 3C product structural members and the like.

Description

Aluminum alloy, preparation method thereof and aluminum alloy structural member
Technical Field
The application relates to the technical field of materials, in particular to an aluminum alloy, a preparation method thereof and an aluminum alloy structural member.
Background
The aluminum alloy has the characteristics of light weight, good toughness, corrosion resistance, unique metallic luster and the like, and is adopted by more and more parts of electronic appliances, communication equipment, lighting devices, automobiles and the like, such as shells of smart phones, notebook computers and tablet computers, radiators and lamp shades of LED lamps, controller cases of new energy automobiles, driving motor shells and the like. The above applications put higher demands on the strength and toughness of aluminum alloys. The most commonly used cast aluminum alloy at present is Al-Si series cast aluminum alloy which has good casting fluidity and can meet the casting process requirements, but has general mechanical properties and can not meet the aluminum alloy die casting products with higher strength requirements.
Disclosure of Invention
The present application is directed to solving, at least to some extent, one of the technical problems in the related art. Therefore, an object of the present application is to provide an aluminum alloy with high yield strength, good tensile strength and good elongation.
In one aspect of the present application, there is provided an aluminum alloy comprising:
8.0-13.0 wt% Si;
2.0-3.0 wt% Cu;
3.0-5.0 wt% Zn;
0.6-0.9 wt% Mg;
0.5-0.8 wt% Mn;
0.1-0.3 wt% Fe;
0.05 to 0.35 wt.% Zr;
0.01-0.05 wt% Ti;
0.005-0.04 wt% Sr;
0.001-0.02 wt% Cr;
0.01-0.02 wt% Ga;
0.001-0.35 wt% Er;
0.005-0.1 wt% Ni;
the balance of Al and inevitable impurities;
wherein the weight content ratio of Er to Zr is 0.01-1.0: 1.
The aluminum alloy has the advantages that by controlling the composition and content of alloy elements and controlling the weight content ratio of Er to Zr in the aluminum alloy to be 0.01-0.5:1, the obtained aluminum alloy has high yield strength, good tensile strength and good elongation, and is suitable for structural members with high requirements on strength and toughness, such as 3C product structural members and the like.
In another aspect of the present application, there is provided a method of making the foregoing aluminum alloy. According to an embodiment of the application, the method comprises: firstly, heating and melting reaction raw materials for preparing the aluminum alloy to obtain aluminum alloy liquid; and then carrying out deslagging treatment, refining treatment and casting treatment on the aluminum alloy liquid to obtain the aluminum alloy. The method is simple and convenient to operate and easy to implement industrially, and the obtained aluminum alloy has high mechanical strength, tensile strength and elongation.
In yet another aspect of the present application, an aluminum alloy structural member is provided. According to an embodiment of the application, at least a portion of the aluminum alloy structural member is formed from the aluminum alloy described above. The aluminum alloy structural member has all the features and advantages of the aluminum alloy described above, and thus, the description thereof is omitted.
Detailed Description
Embodiments of the present application are described in detail below. The following description of the embodiments is merely exemplary in nature and is in no way intended to limit the present disclosure. The examples, where specific techniques or conditions are not indicated, are to be construed according to the techniques or conditions described in the literature in the art or according to the product specifications. The reagents or instruments used are not indicated by the manufacturer, and are all conventional products commercially available.
In one aspect of the present application, there is provided an aluminum alloy comprising:
8.0-13.0 wt% Si;
2.0-3.0 wt% Cu;
3.0-5.0 wt% Zn;
0.6-0.9 wt% Mg;
0.5-0.8 wt% Mn;
0.1-0.3 wt% Fe;
0.05 to 0.35 wt.% Zr;
0.01-0.05 wt% Ti;
0.005-0.04 wt% Sr;
0.001-0.02 wt% Cr;
0.01-0.02 wt% Ga;
0.001-0.35 wt% Er;
0.005-0.1 wt% Ni;
the balance of Al and inevitable impurities;
wherein the weight content ratio of Er to Zr is 0.01-1.0: 1.
The aluminum alloy is prepared by controlling the composition and content of alloy elements and controlling the weight content ratio of Er to Zr to be 0.01-1.0: 1. The aluminum alloy has high yield strength, high tensile strength and good extensibility, and is suitable for structural members with high requirements on strength, such as 3C product structural members and the like.
Specifically, the content of Si in the aluminum alloy is 8.0-13.0 wt%. Further preferably, the content of Si may be 9.0 to 11.5 wt%, wherein Si is a main element in the aluminum alloy, which may significantly improve the die casting fluidity of the aluminum alloy, reduce the shrinkage of the aluminum alloy, to improve the die casting performance, and may also generate Mg2Si and Al12Fe3Si with Mg and Fe, which may improve the mechanical properties of the aluminum alloy, but when the content of Si is excessive, the elongation of the aluminum alloy may be reduced, and in the above aluminum alloys of the present application, the content of Si may be 8.5 wt%, 9.0 wt%, 9.5 wt%, 10.0 wt%, 10.5 wt%, 11.0 wt%, 11.5 wt%, 12.0 wt%, and 12.5 wt%. When the content of Si is within the range, the casting shrinkage stress of the aluminum alloy is obviously smaller than the bonding force among metal crystal grains, and the aluminum alloy has good yield strength, tensile strength and elongation.
Specifically, the Cu content in the aluminum alloy is 2.0-3.0 wt%. Further preferably 2.3 to 2.8 wt%. Cu may form a solid solution phase Al with Al2Cu, while Al2Cu phase is dispersed and distributed on the grain boundary, so that the strength and the toughness of the aluminum alloy are improved; in addition, Cu is used as an alloy strengthening element and also contributes to improving the mechanical properties of the aluminum alloy. However, excessive addition of the metal compound not only reduces the heat treatment performance of the material, but also impairs the toughness of the material and reduces the elongation at break. In the above-described aluminum alloy of the present application, the content of Cu may be 2.0 wt%, 2.3 wt%, 2.5 wt%, 2.8 wt%, and 3.0 wt%. Cu in the above range can improve the strength, toughness and elongation of the aluminum alloy at the same time.
Specifically, the content of Zn in the aluminum alloy is 3.0 to 5.0 wt%, and more preferably 3.5 to 4.5 wt%. Zn can be dissolved in alpha (Al) to form a solid solution, and the effect of strengthening mechanical properties can be achieved. The Zn content may be 3.0 wt%, 3.5 wt%, 4.0 wt%, 4.5 wt%, and 5.0 wt%. In the above aluminum alloy of the present application, controlling the Zn content within the above range can improve the strength, toughness and elongation of the aluminum alloy at the same time.
Specifically, the content of Mg in the aluminum alloy is 0.6 to 0.9 wt%, and more preferably 0.6 to 0.75 wt%. Mg and Zn are combined to form an MgZn2 strengthening phase which is uniformly and dispersedly distributed at a crystal boundary, so that the crystal boundary energy is improved, the strength of the material is ensured, and the toughness of the material is improved. In a specific embodiment of the present invention, the content of Mg may be 0.6 wt%, 0.65 wt%, 0.7 wt%, 0.75 wt%, 0.8 wt%, 0.85 wt%, and 0.9 wt%. In the above aluminum alloy of the present application, controlling the Mg content within the above range can simultaneously improve the yield strength, tensile strength and elongation of the aluminum alloy.
In the formula, when the weight ratio of the Zn content to the Cu content is 1.2-2.5:1, Cu and Zn are combined to form a CuZn combined phase, so that the material strength is improved, and the elongation of the material is ensured; the yield strength can be improved by about 20 MPa; when the weight ratio of the Zn content to the Cu content is 1.2-2.5:1, the aluminum alloy has good formability, the elongation of the aluminum alloy is more than 4%, and the yield strength of the material can reach 250 MPa. In a specific embodiment of the present invention, the weight ratio of the content of Zn to the content of Cu is 1.2:1, 1.5:1, 1.8:1, 2.0:1, 2.2:1, and 2.5: 1.
Specifically, the content of Mn in the aluminum alloy is 0.5 to 0.8 wt%, and more preferably 0.6 to 0.8 wt%. The content of Cr in the aluminum alloy is 0.001 to 0.02 wt%, and more preferably 0.001 to 0.01 wt%. Mn and Cr can be dissolved in an Al alloy matrix in a solid mode, the performance of the matrix is strengthened, the grain growth of primary Si and alpha-Al is inhibited, the content of the primary Si is distributed among all grains in a dispersion mode, the dispersion strengthening effect is achieved, and the strength and the toughness of the material are improved. For Mn, most Mn is segregated to the grain boundary and combined with Fe to form a needle-shaped AlFeMnSi phase, so that the overall strength of the material can be improved, and when the Mn content is too high, a large number of needle-shaped structures can cause the fracture of a matrix, so that the toughness of the material is reduced. In a specific embodiment of the present invention, the content of Mn may be 0.5 wt%, 0.55 wt%, 0.6 wt%, 0.65 wt%, 0.7 wt%, 0.75 wt%, and 0.8 wt%. The content of Cr may be 0.001 wt%, 0.002 wt%, 0.005 wt%, 0.01 wt%, 0.015 wt%, and 0.02 wt%. When the contents of Mn and Cr are within the above ranges, the yield strength, tensile strength and elongation of the aluminum alloy can be simultaneously improved.
Specifically, the content of Fe in the aluminum alloy is 0.1 to 0.3 wt%, and more preferably 0.1 to 0.2 wt%. The content of Fe is in the range, so that the fluidity of the aluminum alloy can be better improved, and the die sticking tendency of the aluminum alloy is reduced. However, the addition of Fe needs to be proper, and when the content exceeds a certain content, the Fe forms needle-shaped objects, so that the elongation of the aluminum alloy is reduced. In a specific embodiment of the present invention, the content of Fe may be 0.1 wt%, 0.15 wt%, 0.2 wt%, 0.25 wt%, and 0.3 wt%.
Specifically, the Zr content in the aluminum alloy is 0.05 to 0.35 wt%, more preferably 0.15 to 0.3 wt%. Trace Zr element is added into the aluminum alloy, Zr can be dissolved in the Al matrix in the aluminum alloy, a coarse Al3Zr phase is generated in the ingot homogenizing treatment process, and a beta' (Al3Zr) metastable phase and an Al3Zr equilibrium phase can be formed at the same time. Trace Zr element is added into the aluminum alloy, so that the effects of inhibiting recrystallization, pinning dislocation and hindering recrystallization nucleation can be achieved; meanwhile, the strength and the toughness of the alloy can be improved. The addition of Zr can lead the aging time of the material to be advanced, quickly reach the stable state of the performance and be beneficial to the aging stability of the material. In a specific embodiment of the present invention, the zirconium may be contained in an amount of 0.05 wt%, 0.1 wt%, 0.15 wt%, 0.2 wt%, 0.25 wt%, 0.3 wt%, and 0.35 wt%.
Specifically, the content of Ti in the aluminum alloy is 0.01 to 0.05 wt%, and more preferably 0.01 to 0.04 wt%. After a great deal of research by the inventor, the Ti in the aluminum alloy has the main effect of grain refinement, and the refined aluminum alloy material can obtain higher strength and elongation, and has small thermal expansion coefficient and good casting performance. The Ti content in the aluminum alloy is in the range, so that on the basis of higher grain refinement effect, the aluminum alloy has lower brittleness and is not easy to break, and the mechanical property of the aluminum alloy is better. In a specific embodiment of the present invention, the content of titanium may be 0.01 wt%, 0.015 wt%, 0.02 wt%, 0.025 wt%, 0.03 wt%, 0.035 wt%, 0.04 wt%, 0.045 wt%, and 0.05 wt%.
Specifically, the Sr content in the aluminum alloy is 0.005 to 0.04 wt%, and more preferably 0.01 to 0.03 wt%. The Sr can be used as a modifier in the aluminum alloy, so that alpha-Al solid solution and needle-shaped silicon phase can be refined, the aluminum alloy structure is improved, the crystal boundary is purified, and the resistance of electron movement in the aluminum alloy is reduced, so that the mechanical property of the aluminum alloy is further improved. In a specific embodiment of the present invention, the Sr content may be 0.005 wt%, 0.01 wt%, 0.015 wt%, 0.02 wt%, 0.025 wt%, 0.03 wt%, 0.035 wt%, and 0.04 wt%. In the above aluminum alloy of the present application, controlling the strontium content within the above range can simultaneously improve the yield strength, tensile strength and elongation of the aluminum alloy.
Specifically, the Ga content in the aluminum alloy is 0.01-0.02 wt%. The content of Ga within the above range can increase the nucleation rate, reduce the growth rate of crystal nuclei, optimize the intergranular structure, and thus improve the strength of the material, and in an embodiment of the present invention, the content of Ga may be 0.01 wt%, 0.015 wt%, and 0.02 wt%. In the aluminum alloy of the present application, controlling the Ga content within the above range can simultaneously improve the yield strength, tensile strength, and elongation of the aluminum alloy.
Specifically, the content of Er in the aluminum alloy is 0.001 to 0.35 wt%, and more preferably 0.012 to 0.25 wt%. The rare earth Er plays a main role in solid solution strengthening, fine crystal strengthening and Al-formed second phase strengthening such as Al3Er and the like in the aluminum alloy. Rare earth Er is mainly distributed in alpha (Al) phase, phase boundary, grain boundary and dendrite segregation in the aluminum alloy, and is either dissolved in an alpha (Al) matrix or exists in a compound (Al3Er) form to refine dendritic structures and grains. Er provides heterogeneous nucleation during solidification. Most Er is eccentrically gathered at the grain boundary of the alloy to form a coarse intermetallic compound, and part Er and Al generate a secondary intermetallic compound which is dispersed in the matrix to generate the dispersion strengthening effect. When the content of Er is within the above range, the tensile strength of the aluminum alloy is improved as the content of Er increases.
Specifically, the content of Ni in the aluminum alloy is 0.005-0.1 wt%. The solid solubility of Ni in the aluminum alloy is low, Ni-rich phase particles are easy to saturate and precipitate in an aluminum matrix, and the Ni element is added into the aluminum alloy to form a nickel-rich phase with high stability, such as Al3Ni, Al7Cu4Ni, Al3CuNi and the like, and the lattice structure is complex. Meanwhile, Ni and Fe can form Al9FeNi and other precipitated phases, so that part of Fe impurities in the aluminum alloy can be effectively removed. The content of the nickel is within the range, so that the mechanical property of the aluminum alloy can be improved.
Specifically, the weight ratio of Er to Zr in the aluminum alloy is (0.01-1.0):1, and more preferably 0.01-0.8:1, and the inventors of the present invention have found that when the weight ratio of Er to Zr in the aluminum alloy is within the above range, the yield strength of the aluminum alloy is significantly improved, and the yield strength is improved by about 10-20MPa on the basis of the original yield strength without decreasing the elongation. When the weight ratio of Er and Zr in the aluminum alloy is outside the above range, both strength and elongation are reduced. The reason for the phenomenon is preliminarily analyzed that the atomic radius of Er is close to that of Zr, crystal grains can be effectively refined by the Er and the Zr, and the Er is added, so that the Er can be combined with Al to form an Al3Er phase and can also be combined with Zr to form an Al3(ZrxEr1-x) phase with better thermal stability, the strength is improved, and the elongation rate is not reduced. In particular embodiments of the invention, the Er to Zr weight ratio may be 0.01:1, 0.02:1, 0.03:1, 0.04:1, 0.05:1, 0.06:1, 0.07:1, 0.075:1, 0.08:1, 0.09:1, 0.1:1, 0.2:1, 0.3:1, 0.4:1, 0.5:1, 0.6:1, 0.7:1, 0.75:1, 0.8:1, 0.9:1, and 1.0: 1.
Specifically, in the aluminum alloy, the weight ratio of Zr to Ti is (8-15): 1, more preferably (4-15): 1, Ti and Zr have the function of grain refinement, and the single addition and the composite addition of Ti and Zr can generate good grain refinement effect on the alloy. The inventors of the present invention have found through a large number of experiments that the effect of refining when Zr and Ti are added in combination in the above-mentioned ratio is more excellent than when both are added in equal amounts. The possible reason is that the composite addition of Ti and Zr not only has the Al3Zr and Al3Ti particles existing when Ti and Zr are added separately to act as nucleation particles, but also forms a large amount of Al3(Ti, Zr) complex phase nucleation cores, and the particles jointly promote strong refinement of crystal grains. Along with the increase of the composite content of Ti and Zr, the number of nucleation cores is increased continuously, the refining effect on the alloy is gradually enhanced, the refining degree of the grain size of the alloy and the mechanical property are further increased, and tests prove that when the ratio of Zr: ti ═ 8-15: the effect of the combined addition is best when 1 is used. In a specific embodiment of the present invention, the weight ratio of Zr and Ti may be 8: 1. 9: 1. 10: 1. 11: 1. 12: 1. 13: 1. 14: 1 and 15: 1.
according to an embodiment of the present application, the aluminum alloy further includes unavoidable impurities, a content of a single element in the unavoidable impurities is not more than 0.01% by mass and a total content of the unavoidable impurities is not more than 0.02% by mass, based on a total mass of the aluminum alloy. Specifically, since the purity of the raw material is difficult to reach 100%, and impurities are likely to be introduced during the production process, the aluminum alloy generally contains inevitable impurities (such as Co, Pb, etc.), in the present application, the content of individual impurity elements in the aluminum alloy may be specifically 0.01%, 0.009%, 0.008 t%, 0.007%, 0.006%, 0.005%, 0.004%, 0.003%, 0.002%, 0.001%, etc., while the total content of impurity elements may be specifically 0.1%, 0.09%, 0.08%, 0.07%, 0.06%, 0.05%, 0.04%, 0.03%, 0.02%, 0.01%, etc. Specifically, taking the aluminum alloy containing impurity elements such as Co, Pb and the like as an example, the content of each element of Co and Pb is less than 0.01 percent, and the sum of the content of the Co and Pb is less than 0.1 percent. Therefore, various performances of the aluminum alloy can be well ensured to meet the requirements, and negative effects on the aluminum alloy can not be generated.
In another aspect of the present application, there is provided a method of making the foregoing aluminum alloy. According to an embodiment of the application, the method comprises: heating and melting reaction raw materials for preparing the aluminum alloy to obtain aluminum alloy liquid; and carrying out deslagging treatment, refining treatment and casting treatment on the aluminum alloy liquid so as to obtain the aluminum alloy. The method is simple and convenient to operate and easy to implement industrially, and the obtained aluminum alloy has the advantages of high mechanical strength, good ductility and excellent casting formability.
According to the embodiments of the present application, the specific process conditions and parameters of the method are not particularly limited, and those skilled in the art can flexibly select the process conditions and parameters according to actual needs. In some specific embodiments of the present application, the method may specifically include: after the material proportioning calculation, weighing pure Al ingot, pure Zn, pure Mg, pure Cu, pure Fe, Al-Si intermediate alloy, Al-Fe intermediate alloy, Al-Mn intermediate alloy, Al-Sr intermediate alloy, Al-Ni intermediate alloy and Al-Ti intermediate alloy according to the required amount; putting pure Al ingots and Al-Si intermediate alloy into a smelting furnace, heating until the pure Al ingots and the Al-Si intermediate alloy are completely molten, and stirring the melt once every 2-3 min (stirring for about 3-5 times in total); then adding Al-Si intermediate alloy, pure Cu, Al-Mn intermediate alloy, Al-Sr intermediate alloy, Al-Ni intermediate alloy, Al-Ti intermediate alloy and Al-Zr intermediate alloy in sequence and immersing the mixture into the melt until the mixture is molten; and finally, adding pure Zn ingots and pure Mg ingots, and stirring after the pure Zn ingots and the pure Mg ingots are melted to ensure that the components are uniform. Stirring the aluminum alloy liquid uniformly, detecting and adjusting the content of each element component until reaching the required range, adding 0.5 percent of slag removing agent for removing slag, 0.5 percent of refining agent for refining and degassing, slagging off and standing for 10-15 minutes after finishing, then cooling to about 700 ℃ and beginning to cast into ingots. The method is simple and convenient to operate and easy to implement industrially, and the obtained aluminum alloy has the advantages of high mechanical strength, good ductility and excellent casting formability.
According to an embodiment of the application, the method may further comprise: the aluminum alloy is subjected to die-casting molding treatment, so that the aluminum alloy can be processed into various complex shapes, and the use requirements of different environments are met. Specifically, the temperature is 680-720 ℃ (specifically 680 ℃, 700 ℃, 710 ℃, 720 ℃); the speed of the die casting machine is 1.6-2m/s (specifically, 1.6m/s, 1.7m/s, 1.8m/s, 1.9m/s, 2.0m/s, etc.). The heat preservation time is 1-3S. Under the condition, the forming of the aluminum alloy is more facilitated.
In yet another aspect of the present application, an aluminum alloy structural member is provided. According to an embodiment of the application, at least a portion of the aluminum alloy structural member is formed from the aluminum alloy described above. The aluminum alloy structural member has all the features and advantages of the aluminum alloy described above, and thus, the description thereof is omitted.
According to an embodiment of the invention, the aluminium alloy structural part comprises a 3C product structural part. The mobile phone middle frame can be a mobile phone middle frame, a mobile phone rear cover, a mobile phone middle plate and other structural members. Therefore, the structural part has good mechanical strength, plasticity and die-casting performance, can well meet the requirement of a user on high strength of a product, and improves user experience.
Embodiments of the present application are described in detail below.
Example 1
According to the formulation of table 1, an aluminum alloy die casting was obtained according to the following melting steps and die casting parameters:
after the material proportioning calculation, weighing pure Al ingot, pure Zn, pure Mg, Al-Si intermediate alloy, Al-Cu intermediate alloy, Al-Fe intermediate alloy, Al-Mn intermediate alloy, Al-Sr intermediate alloy, Al-Ni intermediate alloy and Al-Ti intermediate alloy according to the required amount; putting pure Al ingots and Al-Si intermediate alloy into a smelting furnace, heating until the pure Al ingots and the Al-Si intermediate alloy are completely molten, and stirring the melt once every 2-3 min (stirring for about 3-5 times in total); then adding Al-Si intermediate alloy, Al-Cu intermediate alloy, Al-Mn intermediate alloy, Al-Sr intermediate alloy, Al-Ni intermediate alloy, Al-Ti intermediate alloy and Al-Zr intermediate alloy in sequence, and immersing the mixture into the melt until the mixture is molten; and finally, adding pure Zn ingots and pure Mg ingots, and stirring after the pure Zn ingots and the pure Mg ingots are melted to ensure that the components are uniform. Stirring the aluminum alloy liquid uniformly, detecting and adjusting the content of each element component until reaching the required range, adding 0.5 percent of slag removing agent for removing slag, 0.5 percent of refining agent for refining and degassing, slagging off and standing for 10-15 minutes after finishing, then cooling to about 700 ℃ and beginning to cast into ingots. And after the cast ingot is cooled, die-casting at 680-720 ℃, at the speed of 1.6-2m/s for 1-3 s.
Examples 2 to 55
An aluminum alloy die cast was obtained by the method of example 1 according to the formulation of table 1.
Comparative examples 1 to 24
An aluminum alloy die cast was obtained by the method of example 1 according to the formulation of table 1.
TABLE 1 formulation of aluminum alloy (unit: parts by weight)
And (3) performance testing:
and (3) mechanical property testing, referring to the first part of GB/T228.1-2010 metal material tensile test: the room temperature test method tests the tensile strength, the yield strength and the elongation, and specific results are shown in the table 2.
Table 2 results of performance testing
As can be seen from Table 2, the aluminum alloy of the present invention has a tensile strength of not less than 410MPa, a yield strength of not less than 280MPa, and an elongation of not less than 4%. That is to say, the aluminum alloy of the invention has good tensile strength, yield strength and elongation at the same time.
In the description herein, reference to the description of the term "one embodiment," "some embodiments," "an example," "a specific example," or "some examples," etc., means that a particular feature, structure, material, or characteristic described in connection with the embodiment or example is included in at least one embodiment or example of the application. In this specification, the schematic representations of the terms used above are not necessarily intended to refer to the same embodiment or example. Furthermore, the particular features, structures, materials, or characteristics described may be combined in any suitable manner in any one or more embodiments or examples. Furthermore, various embodiments or examples and features of different embodiments or examples described in this specification can be combined and combined by one skilled in the art without contradiction.
Although embodiments of the present application have been shown and described above, it is understood that the above embodiments are exemplary and should not be construed as limiting the present application, and that variations, modifications, substitutions and alterations may be made to the above embodiments by those of ordinary skill in the art within the scope of the present application.

Claims (10)

1. An aluminum alloy, characterized in that the aluminum alloy comprises:
8.0-13.0 wt% Si;
2.0-3.0 wt% Cu;
3.0-5.0 wt% Zn;
0.6-0.9 wt% Mg;
0.5-0.8 wt% Mn;
0.1-0.3 wt% Fe;
0.05 to 0.35 wt.% Zr;
0.01-0.05 wt% Ti;
0.005-0.04 wt% Sr;
0.001-0.02 wt% Cr;
0.01-0.02 wt% Ga;
0.001-0.35 wt% Er;
0.005-0.1 wt% Ni;
the balance of Al and inevitable impurities;
wherein the weight content ratio of Er to Zr is 0.01-1.0: 1.
2. The aluminum alloy of claim 1, wherein the ratio of the weight content of Zr to the weight content of Ti is 4-15: 1.
3. An aluminium alloy according to claim 2, wherein the ratio of the weight content of Zr to the weight content of Ti is 8-15: 1.
4. The aluminum alloy of claim 1, wherein the ratio of the weight content of Zn to the weight content of Cu is 1.2-2.5: 1.
5. The aluminum alloy of any one of claims 1 to 4, wherein the aluminum alloy comprises:
9.0-11.5 wt% Si;
2.3-2.8 wt% Cu;
3.5-4.5 wt% Zn;
0.6-0.75 wt% Mg;
0.6-0.8 wt% Mn;
0.1-0.2 wt% Fe;
0.15-0.3 wt% Zr;
0.01-0.04 wt% Ti;
0.01-0.03 wt% of Sr;
0.001-0.01 wt% Cr;
0.01-0.02 wt% Ga;
0.012-0.25 wt% Er;
0.005-0.1 wt% Ni;
the balance of Al and inevitable impurities;
wherein the weight content ratio of Er to Zr is 0.01-0.8: 1.
6. The aluminum alloy of claim 5, wherein the aluminum alloy has a tensile strength of not less than 410MPa, a yield strength of not less than 280MPa, and an elongation of not less than 4%.
7. A method of making the aluminum alloy of any of claims 1-6, comprising:
firstly, heating and melting reaction raw materials for preparing the aluminum alloy to obtain aluminum alloy liquid; and then carrying out deslagging treatment, refining treatment and casting treatment on the aluminum alloy liquid to obtain the aluminum alloy.
8. The method as claimed in claim 7, further comprising die-casting the aluminum alloy at 680-720 ℃, at a speed of 1.6-2m/s and for a holding time of 1-3 s.
9. An aluminum alloy structural member, characterized in that at least a part of the aluminum alloy structural member is formed of the aluminum alloy according to any one of claims 1 to 6.
10. The aluminum alloy structural member of claim 9, wherein the aluminum alloy structural member comprises a 3C product structural member.
CN202110092933.8A 2020-12-24 2021-01-25 Aluminum alloy, preparation method thereof and aluminum alloy structural member Active CN112921219B (en)

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CN105088033A (en) * 2014-05-08 2015-11-25 比亚迪股份有限公司 Aluminium alloy and preparation method thereof
CN105603270A (en) * 2016-01-27 2016-05-25 广西平果铝合金精密铸件有限公司 Die-casting aluminum alloy for engine components and production method of die-casting aluminum alloy
CN108300910A (en) * 2017-08-24 2018-07-20 东莞市金羽丰知识产权服务有限公司 The formula and its smelting key technology of high-strength/tenacity aluminum alloy
CN108977702A (en) * 2017-05-31 2018-12-11 比亚迪股份有限公司 A kind of aluminium alloy and aluminium alloy castings preparation method
CN110396628A (en) * 2018-04-25 2019-11-01 比亚迪股份有限公司 A kind of aluminium alloy and preparation method thereof
CN111041290A (en) * 2019-12-20 2020-04-21 比亚迪股份有限公司 Aluminum alloy and application thereof

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* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH0261025A (en) * 1988-08-26 1990-03-01 Kobe Steel Ltd Al-si alloy plate material having excellent formability and its manufacture
CN105088033A (en) * 2014-05-08 2015-11-25 比亚迪股份有限公司 Aluminium alloy and preparation method thereof
CN105603270A (en) * 2016-01-27 2016-05-25 广西平果铝合金精密铸件有限公司 Die-casting aluminum alloy for engine components and production method of die-casting aluminum alloy
CN108977702A (en) * 2017-05-31 2018-12-11 比亚迪股份有限公司 A kind of aluminium alloy and aluminium alloy castings preparation method
CN108300910A (en) * 2017-08-24 2018-07-20 东莞市金羽丰知识产权服务有限公司 The formula and its smelting key technology of high-strength/tenacity aluminum alloy
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