CN112662915B - Aluminum alloy and preparation method and application thereof - Google Patents
Aluminum alloy and preparation method and application thereof Download PDFInfo
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- CN112662915B CN112662915B CN202011493550.3A CN202011493550A CN112662915B CN 112662915 B CN112662915 B CN 112662915B CN 202011493550 A CN202011493550 A CN 202011493550A CN 112662915 B CN112662915 B CN 112662915B
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C49/00—Alloys containing metallic or non-metallic fibres or filaments
- C22C49/02—Alloys containing metallic or non-metallic fibres or filaments characterised by the matrix material
- C22C49/04—Light metals
- C22C49/06—Aluminium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- 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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- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01M—PROCESSES OR MEANS, e.g. BATTERIES, FOR THE DIRECT CONVERSION OF CHEMICAL ENERGY INTO ELECTRICAL ENERGY
- H01M50/00—Constructional details or processes of manufacture of the non-active parts of electrochemical cells other than fuel cells, e.g. hybrid cells
- H01M50/20—Mountings; Secondary casings or frames; Racks, modules or packs; Suspension devices; Shock absorbers; Transport or carrying devices; Holders
- H01M50/218—Mountings; Secondary casings or frames; Racks, modules or packs; Suspension devices; Shock absorbers; Transport or carrying devices; Holders characterised by the material
- H01M50/22—Mountings; Secondary casings or frames; Racks, modules or packs; Suspension devices; Shock absorbers; Transport or carrying devices; Holders characterised by the material of the casings or racks
- H01M50/222—Inorganic material
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
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- Y02E—REDUCTION OF GREENHOUSE GAS [GHG] EMISSIONS, RELATED TO ENERGY GENERATION, TRANSMISSION OR DISTRIBUTION
- Y02E60/00—Enabling technologies; Technologies with a potential or indirect contribution to GHG emissions mitigation
- Y02E60/10—Energy storage using batteries
Abstract
The invention belongs to the technical field of alloys, and particularly relates to an aluminum alloy and a preparation method and application thereof. The aluminum alloy provided by the invention comprises the following elements in percentage by mass: 0.10-0.18% of Cu, 0.33-0.38% of Fe, 1.05-1.10% of Mn, 0.06-0.18% of Si, 0.10-0.20% of Mg, 0.04-0.07% of Zr, 0.03-0.05% of Cr, less than or equal to 0.03% of Ti, and the balance of Al and inevitable impurities; the mass ratio of Mn to Fe is (2.8-3.2): 1, the total content of Mn and Fe is less than or equal to 1.45 wt.%. The embodiment shows that the tensile strength of the aluminum alloy provided by the invention is 182-200 MPa; the product obtained after extrusion or cold drawing has smooth surface, excellent extrusion performance and cold drawing performance and is suitable for thin-wall square shell profiles.
Description
Technical Field
The invention belongs to the technical field of alloys, and particularly relates to an aluminum alloy and a preparation method and application thereof.
Background
The power battery shell needs to have the requirements of excellent corrosion resistance, medium and low temperature resistance, fast heat conduction, good welding performance and medium or higher strength, and the current power battery shell usually adopts an aluminum drawing square tube or a drawing forming aluminum barrel. In the aluminum alloy, the 1000 series aluminum alloy has too low strength, so the 1000 series aluminum alloy has the advantages of high purity and easy extrusion, but cannot meet the basic strength requirement of the power battery shell; 3000 series aluminum alloy belongs to aluminum alloy which can not be strengthened by heat treatment, the strength can be improved only by adopting a cold working method, when the cold working deformation is large, the problem of snapping easily occurs, the mass production performance is low, for example, for a square shell, when the deformation is more than 35%, the snapping easily occurs, and particularly, the snapping and breaking phenomena easily occur at the corner position of the square shell. The conventional aluminum alloy can not realize the production of a thin-wall square shell on the basis of ensuring good strength and drawing performance, and can not meet the production and use requirements of a power battery shell.
Disclosure of Invention
In view of the above, the present invention provides an aluminum alloy and a preparation method thereof, and the aluminum alloy provided by the present invention has characteristics of excellent extrusion performance, excellent cold drawing performance and high tensile strength, and can meet requirements of thin-wall square shell profiles on strength, extrusion performance and cold drawing performance.
In order to achieve the purpose of the invention, the invention provides the following technical scheme:
the invention provides an aluminum alloy which comprises the following elements in percentage by mass:
0.10-0.18% of Cu, 0.33-0.38% of Fe, 1.05-1.10% of Mn, 0.06-0.18% of Si, 0.10-0.20% of Mg, 0.04-0.07% of Zr, 0.03-0.05% of Cr, less than or equal to 0.03% of Ti, and the balance of Al and inevitable impurities;
the mass ratio of Mn to Fe is (2.8-3.2): 1, the total content of Mn and Fe is less than or equal to 1.45 wt.%.
Preferably, the content of single element in the inevitable impurities is less than or equal to 0.05 percent by mass, and the total content of the inevitable impurities is less than or equal to 0.15 percent by mass.
Preferably, the tensile strength of the aluminum alloy is 180-200 MPa.
Preferably, the aluminum alloy is extruded under extrusion conditions: the limit wall thickness is 0.55mm, and the limit circumscribed circle diameter of the square section profile is 140 mm;
the aluminum alloy is prepared by the following steps: the limiting wall thickness is 0.4mm, and the limiting circumcircle diameter of the square section profile is 138.5 mm.
The invention also provides a preparation method of the aluminum alloy in the technical scheme, which comprises the following steps:
smelting and casting the alloy raw materials in sequence to obtain an aluminum alloy ingot;
and carrying out homogenization treatment, extrusion treatment, quenching, aging treatment and cold drawing on the aluminum alloy cast ingot in sequence to obtain the aluminum alloy.
Preferably, the homogenization treatment includes a first homogenization treatment, a second homogenization treatment and a third homogenization treatment which are sequentially performed;
the heat preservation temperature of the first homogenization treatment is 520-540 ℃, and the heat preservation time is 2-4 h;
the heat preservation temperature of the second homogenization treatment is 580-600 ℃, and the heat preservation time is 6-10 hours;
the heat preservation temperature of the third homogenization treatment is 460-480 ℃, and the heat preservation time is 2-4 h.
Preferably, the extrusion treatment temperature is 460-520 ℃, and the extrusion ratio is 30-150.
Preferably, the heat preservation temperature of the aging treatment is 150-170 ℃, and the heat preservation time is 1-3 h.
Preferably, the cold drawing is primary cold drawing, and the deformation amount of the cold drawing is 15-30%.
The invention also provides application of the aluminum alloy in the technical scheme or the aluminum alloy prepared by the preparation method in the technical scheme as a thin-wall square shell profile in a battery shell.
The invention provides an aluminum alloy which comprises the following elements in percentage by mass: 0.10-0.18% of Cu, 0.33-0.38% of Fe, 1.05-1.10% of Mn, 0.06-0.18% of Si, 0.10-0.20% of Mg, 0.04-0.07% of Zr, 0.03-0.05% of Cr, less than or equal to 0.03% of Ti, and the balance of Al and inevitable impurities; the mass ratio of Mn to Fe is (2.8-3.2): 1, the total content of Mn and Fe is less than or equal to 1.45 wt.%.
In the present invention, Al provides a base alloying element; mn is a main alloy element, and Mn and Al form MnAl6The addition of Mn is beneficial to spheroidizing Fe phase hard particles and improving the extrusion processing performance of the alloy; cu is beneficial to improving the strength of the aluminum alloy; mg is beneficial to refining the grain size of the aluminum alloy and improving the strength; fe is beneficial to forming a (FeMn) Al6 phase, and can effectively refine aluminum alloy grains; al, Si and Mn may form ternary phase Al12Mn3Si2When ternary phase Al12Mn3Si2After Fe is dissolved, quaternary phase AlFeMnSi can be formed, and the invention controls the content of Fe and Si to ensure that Fe and Si can still be generated on the basis of forming ternary phase and quaternary phaseThe function of refining or solution strengthening the aluminum alloy grains is exerted; cu, Si and Mg all have the function of solid solution strengthening, and the Si and the Mg can precipitate Mg2The Si strengthening phase is beneficial to enhancing the strength of the aluminum alloy; zr and Cr are microalloying elements of aluminum alloy, and AlCr formed by Zr, Cr and Al7And AlZr3The aluminum alloy is a thermodynamically stable fine disperse phase, and is beneficial to inhibiting the recrystallization and grain growth of the aluminum alloy; ti is advantageous for refining the cast grains.
In addition, the Mn content is controlled to be 1.05-1.10 wt.%, so that the plasticity, the weldability, the heat resistance and the corrosion resistance of the aluminum alloy are improved, and meanwhile, the large extrusion deformation resistance is avoided, and the severe deterioration of the extrusion performance is prevented; controlling Si, Mg and Cu in corresponding content range is favorable to ensure the strength of aluminum alloy, avoids the great extrusion deformation resistance of aluminum alloy, prevents the deterioration of extrusion performance and can ensure the formation of Mg2The Si strengthening phase prevents the beneficial effect of Fe from being weakened; meanwhile, the content of Zr and Cr is controlled, so that the aluminum alloy is favorably ensured to have a fibrous crystal structure, a mixed grain structure with a coarse recrystallization structure and a fibrous crystal structure coexisting is prevented from being formed, and the deterioration of the strength and the extrusion performance of the aluminum alloy is avoided; the content relation of Mn and Fe is controlled, which is beneficial to avoiding forming a large amount of coarse flaky (FeMn) Al6The ductility of the aluminum alloy is prevented from being reduced, the relationship between the strength and the extrusion performance of the aluminum alloy is balanced, and the requirements of the thin-wall square shell on the strength and the extrusion performance are met.
The test result of the embodiment shows that the tensile strength of the aluminum alloy provided by the invention is 182-200 MPa; the extruded product after extrusion has a smooth surface (the extruded product is a square shell with the wall thickness of 0.5-0.65 mm and the circumscribed circle of 128 mm), and has excellent extrusion performance; the surface of a cold-drawn product after cold drawing is smooth (the cold-drawn product is a square shell with the wall thickness of 0.4-0.5 mm and the circumscribed circle of 128 mm), and the cold drawing performance is excellent.
The invention also provides a preparation method of the aluminum alloy, which comprises the following steps: smelting and casting the alloy raw materials in sequence to obtain an aluminum alloy ingot; and carrying out homogenization treatment, extrusion treatment, quenching, aging treatment and cold drawing on the aluminum alloy cast ingot in sequence to obtain the aluminum alloy. In the present invention, the homogenization is performedThe method is favorable for eliminating macro-micro segregation of alloy elements in the ingot, so that the alloy elements and coarse compounds are fully dissolved in the solution, and fine dispersoids are formed at the same time; the aging treatment contributes to strengthening phases (Mg) in the aluminum alloy2Si) is precipitated, and the strength of the aluminum alloy is improved.
Drawings
FIG. 1 is a flow chart of a method of making an aluminum alloy according to the present invention;
FIG. 2 is a gold phase diagram of the aluminum alloy of example 1;
FIG. 3 is an EBSD photograph of the aluminum alloy of example 1;
FIG. 4 is an SEM photograph of an aluminum alloy in example 1;
FIG. 5 is an EDS chart of the aluminum alloy in example 1;
FIG. 6 is a dimensional chart of a sample in a squeeze test;
fig. 7 is a dimensional chart of the test piece in the cold drawing test.
Detailed Description
The invention provides an aluminum alloy which is characterized by comprising the following elements in percentage by mass:
0.10-0.18% of Cu, 0.33-0.38% of Fe, 1.05-1.10% of Mn, 0.06-0.18% of Si, 0.10-0.20% of Mg, 0.04-0.07% of Zr, 0.03-0.05% of Cr, less than or equal to 0.03% of Ti, and the balance of Al and inevitable impurities;
the mass ratio of Mn to Fe is (2.8-3.2): 1, the total content of Mn and Fe is less than or equal to 1.45 wt.%.
The aluminum alloy comprises, by mass, 0.10-0.18% of Cu, preferably 0.11-0.17%, and more preferably 0.12-0.16%. In the invention, Cu has the function of solid solution strengthening, which is beneficial to improving the strength of the aluminum alloy; the Cu is controlled within the content range, so that the strength of the aluminum alloy is favorably ensured, the large extrusion deformation resistance of the aluminum alloy is avoided, and the deterioration of the extrusion performance is prevented.
The aluminum alloy comprises 0.33-0.38% of Fe by mass percentage, preferably 0.335-0.375% and more preferably 0.34-0.37%. In the present invention, Fe favors the formation of (FeMn) Al6And the aluminum alloy grains can be effectively refined.
The aluminum alloy comprises 1.05-1.10% of Mn in percentage by mass, preferably 1.055-1.095%, and more preferably 1.06-1.09%. In the present invention, Mn is a main alloying element, and Mn forms MnAl with Al6The addition of Mn is beneficial to spheroidizing Fe phase hard particles and improving the extrusion processing performance of the alloy; the Mn content is controlled to be 1.05-1.10 wt.%, so that the improvement of the plasticity, the weldability, the heat resistance and the corrosion resistance of the aluminum alloy is facilitated, meanwhile, the large extrusion deformation resistance is avoided, and the severe deterioration of the extrusion performance is prevented.
The aluminum alloy comprises, by mass, 0.06-0.18% of Si, preferably 0.07-0.17%, and more preferably 0.08-0.16%. In the invention, Si has the function of solid solution strengthening, and Al, Si and Mn can form ternary phase Al12Mn3Si2When ternary phase Al12Mn3Si2After dissolving Fe, a quaternary phase alfermnsi is formed.
The aluminum alloy comprises, by mass, 0.10-0.20% of Mg, preferably 0.11-0.19%, and more preferably 0.12-0.18%. In the invention, Mg has the function of solid solution strengthening, and is beneficial to refining the grain size of the aluminum alloy and improving the strength; furthermore, Si and Mg may precipitate Mg2The Si strengthening phase is beneficial to enhancing the strength of the aluminum alloy; controlling Si and Mg in corresponding content ranges is favorable for ensuring the strength of the aluminum alloy, avoids the large extrusion deformation resistance of the aluminum alloy, prevents the deterioration of the extrusion performance and can ensure the formation of Mg2Si strengthens the phase, avoiding weakening the beneficial effects of Fe.
The aluminum alloy comprises, by mass, 0.04-0.07% of Zr, preferably 0.045-0.065%, and more preferably 0.05-0.06%. In the present invention, Zr is a microalloying element of an aluminum alloy, and AlZr formed of Zr and Al3The aluminum alloy is a thermodynamically stable fine disperse phase, and is beneficial to inhibiting the recrystallization and grain growth of the aluminum alloy; the content of Zr is controlled, which is favorable for ensuring that the aluminum alloy has a fibrous crystal structure, preventing the formation of a mixed grain structure with thick recrystallization structure and fibrous crystal structure, and avoiding the strength and extrusion of the aluminum alloyDeterioration of the pressing property.
The aluminum alloy comprises, by mass, 0.03-0.05% of Cr, preferably 0.033-0.048%, and more preferably 0.035-0.045%. In the present invention, Cr is a microalloyed element of aluminum alloy, and AlCr is formed by Cr and Al7The aluminum alloy is a thermodynamically stable fine disperse phase, and is favorable for inhibiting recrystallization and grain growth of the aluminum alloy. The control of the content of Cr is beneficial to ensuring that the aluminum alloy has a fibrous crystal structure, preventing the formation of a mixed grain structure with a coarse recrystallization structure and a fibrous crystal structure, and avoiding the deterioration of the strength and the extrusion performance of the aluminum alloy.
The aluminum alloy comprises, by mass, not more than 0.03% of Ti, preferably 0.001-0.028%, and more preferably 0.01-0.02%. In the present invention, Ti contributes to refinement of cast grains.
The aluminum alloy of the present invention includes, in mass percentage, the balance of Al and inevitable impurities.
In the present invention, Al is a base alloy element.
In the present invention, the content of a single element in the inevitable impurities is preferably 0.05% or less, more preferably 0.03% or less, and still more preferably 0.01% or less, in mass percentage; the total content of the inevitable impurities is preferably 0.15% or less, more preferably 0.1% or less, still more preferably 0.05% or less. In the present invention, the inevitable impurities preferably include one or more of V, Ca and Na.
In the invention, the mass ratio of Mn to Fe is (2.8-3.2): 1, preferably (2.85-3.15): 1, more preferably (2.9 to 3.1): 1; the total content of Mn and Fe is preferably ≦ 1.45 wt.%, more preferably ≦ 1.40%. The content relation of Mn and Fe is controlled in the invention, which is beneficial to avoiding forming a large amount of coarse flaky (FeMn) Al6The ductility of the aluminum alloy is prevented from being reduced, the relationship between the strength and the extrudability of the aluminum alloy is balanced, and the requirements of the thin-wall square shell profile on the strength and the extrusion performance are met.
In the invention, the tensile strength of the aluminum alloy is preferably 180-200 MPa. In the present invention, the aluminum alloy is extruded under conditions of: the limit wall thickness is preferably 0.55mm, and the limit circumcircle diameter of the square section profile is preferably 140 mm. In the present invention, the aluminum alloy is, under drawing conditions: the limit wall thickness is preferably 0.4mm, and the limit circumcircle diameter of the square section profile is preferably 138.5 mm.
The invention also provides a preparation method of the aluminum alloy in the technical scheme, which comprises the following steps:
smelting and casting the alloy raw materials in sequence to obtain an aluminum alloy ingot;
and carrying out homogenization treatment, extrusion treatment, quenching, aging treatment and cold drawing on the aluminum alloy cast ingot in sequence to obtain the aluminum alloy.
Fig. 1 is a flow chart of a method for preparing an aluminum alloy according to the present invention, and the method for preparing an aluminum alloy according to the present invention is described in detail below with reference to fig. 1.
The alloy raw materials are sequentially smelted and cast to obtain the aluminum alloy ingot.
The alloy raw material is not particularly limited, and any alloy raw material which can meet the composition requirement of the aluminum alloy element for the thin-wall square shell can be adopted.
In the invention, the smelting temperature is preferably 740-780 ℃, and more preferably 750-760 ℃; the smelting time is preferably 2-4 h, and more preferably 2-3 h. In the present invention, the melting facility is preferably a tilting melting furnace.
In the invention, the casting temperature is preferably 690-740 ℃, and more preferably 700-720 ℃.
After the aluminum alloy cast ingot is obtained, the aluminum alloy cast ingot is subjected to homogenization treatment, extrusion treatment, quenching, aging treatment and cold drawing in sequence to obtain the aluminum alloy for the thin-wall square shell.
The aluminum alloy ingot is subjected to homogenization treatment to obtain a homogenized ingot.
In the present invention, the homogenization treatment preferably includes a first homogenization treatment, a second homogenization treatment, and a third homogenization treatment, which are performed in this order. In the invention, the homogenization treatment is beneficial to eliminating macro-micro segregation of alloy elements in the ingot, so that the alloy elements and coarse compounds are fully dissolved in a solid manner, and fine dispersoids are formed at the same time.
In the invention, the heat preservation temperature of the first homogenization treatment is preferably 520-540 ℃, and more preferably 525-535 ℃; the heat preservation time is preferably 2-4 h, and more preferably 2.5-3.5 h. In the present invention, the holding temperature of the first homogenization treatment is preferably obtained by raising the temperature to room temperature; the heating rate is preferably 2-5 ℃/min, and more preferably 3-4 ℃/min. In the invention, the first homogenization treatment is beneficial to completely eliminating the macro-microsegregation of Si, Mg and Cu elements in the ingot.
In the invention, the heat preservation temperature of the second homogenization treatment is preferably 580-600 ℃, and more preferably 585-595 ℃; the heat preservation time is preferably 6-10 h, and more preferably 6.5-9.5 h. In the present invention, the holding temperature of the second homogenization treatment is preferably obtained by raising the holding temperature of the first homogenization treatment; the heating rate is preferably 2-5 ℃/min, and more preferably 3-4 ℃/min. In the invention, the second homogenization treatment is beneficial to promoting the spheroidization of the Fe phase and the re-solid solution of the high-temperature precipitated phase precipitated by the first homogenization treatment, so as to prepare for the subsequent third-stage precipitation.
In the invention, the heat preservation temperature of the third homogenization treatment is preferably 460-480 ℃, and more preferably 465-475 ℃; the heat preservation time is preferably 2-4 h, and more preferably 2.5-3.5 h. In the invention, the heat preservation temperature of the third homogenization treatment is preferably obtained by reducing the heat preservation temperature of the second homogenization treatment; the cooling rate is preferably 0.5-2 ℃/min, and more preferably 1-1.5 ℃/min. In the invention, the third homogenization treatment is beneficial to ensuring high-temperature precipitated phases AlCr7, AlZr3 and MnAl6Fully and finely dispersed and precipitated. In the invention, if the parameters of the homogenization treatment are not in the parameter range of the invention, the deformation resistance of the aluminum alloy is too large, the extrusion is difficult, and the subsequent extrusion treatment process can form a mixed crystal state with coexisting fiber crystals and coarse crystal grains, thus greatly influencing the strength of the aluminum alloy product.
After the third homogenization treatment, the obtained homogenized cast ingot is preferably cooled to room temperature; the cooling is preferably air cooling.
After obtaining the homogenized cast ingot, the homogenized cast ingot is sequentially extruded and quenched to obtain the wrought aluminum alloy.
In the invention, the temperature of the extrusion treatment is preferably 460-520 ℃, and more preferably 465-515 ℃. In the present invention, the temperature of the extrusion treatment is preferably obtained by raising the temperature to room temperature; the heating rate is not particularly limited, and any heating rate can be adopted. In the present invention, the extrusion ratio of the extrusion treatment is preferably 30 to 150, and more preferably 40 to 80. In the present invention, the apparatus for the extrusion process is preferably a forward single-action extruder. In the invention, the extrusion treatment is favorable for realizing solid solution of the alloy strengthening phase, and the extrusion treatment is combined with the extrusion die to obtain a product prototype, thereby being favorable for realizing accurate process control.
In the present invention, the quenching is preferably an in-line air-cooled quenching. In the invention, the cooling rate of quenching is preferably more than or equal to 100 ℃/min, and more preferably 100-120 ℃/min. In the present invention, the quenching facilitates the retention of Mg and Si in the product as a supersaturated solid solution.
After the wrought aluminum alloy is obtained, the invention carries out aging treatment on the wrought aluminum alloy to obtain the aged aluminum alloy.
In the invention, the heat preservation temperature of the aging treatment is preferably 150-170 ℃, and more preferably 155-165 ℃; the heat preservation time is preferably 1-3 h, and more preferably 1.5-2.5 h. In the present invention, the temperature of the aging treatment is preferably obtained by raising the temperature to room temperature; the heating rate is preferably 3-10 ℃/min, and more preferably 7-10 ℃/min. In the present invention, the aging treatment helps to make the strengthening phase (Mg) in the aluminum alloy2Si) is separated out, and the strength of the aluminum alloy is improved; within the condition range of the aging treatment, the invention is beneficial to simultaneously ensuring the strength and the drawing capability of the aluminum alloy and preventing the strength reduction or the drawing difficulty of the aluminum alloy.
After the aged aluminum alloy is obtained, the aged aluminum alloy is drawn to obtain the aluminum alloy.
In the present invention, the cold drawing is preferably a single cold drawing. In the present invention, the cold-drawing deformation amount is preferably 15 to 30%, and more preferably 18 to 28%. In the invention, the drawing is beneficial to being matched with aging treatment, and the strength, the extrusion performance and the drawing performance of the aluminum alloy are improved in a synergistic manner; meanwhile, the forming performance of the thin-wall square shell of the aluminum alloy is ensured.
The invention also provides application of the aluminum alloy in the technical scheme or the aluminum alloy prepared by the preparation method in the technical scheme as a thin-wall square shell profile in a battery shell.
In the invention, the application is preferably that the aluminum alloy is directly used as a profile alloy, the thin-wall square shell profile is formed, and the formed thin-wall square shell profile is used as a battery shell.
In order to further illustrate the present invention, the following examples are provided to describe an aluminum alloy and its preparation method and application in detail, but they should not be construed as limiting the scope of the present invention. It is to be understood that the described embodiments are merely exemplary of the invention, and not restrictive of the full scope of the invention. All other embodiments, which can be derived by a person skilled in the art from the embodiments given herein without making any creative effort, shall fall within the protection scope of the present invention.
Example 1
The aluminum alloy is designed to have the element composition of 0.10 percent of Cu, 0.33 percent of Fe, 1.05 percent of Mn, 0.06 percent of Si, 0.10 percent of Mg, 0.04 percent of Zr, 0.03 percent of Cr, 0.02 percent of Ti, and the balance of Al and inevitable impurities according to the mass percentage; the content of single inevitable impurities is less than or equal to 0.05 percent, and the total content is less than or equal to 0.15 percent;
preparing an aluminum alloy: smelting alloy raw materials conforming to the composition of the design elements at 750 ℃ for 3h, and casting the obtained melt at 710 ℃ to obtain an aluminum alloy ingot;
heating the aluminum alloy cast ingot to 530 ℃ at the speed of 3.5 ℃/min, preserving heat for 3h at 530 ℃, then heating to 580 ℃ at the speed of 3.5 ℃/min, preserving heat for 8h at 580 ℃, cooling to 460 ℃ at the speed of 1.0 ℃/min, preserving heat for 2h at 460 ℃, and air-cooling to room temperature to obtain a homogenized cast ingot; then heating the obtained homogenized cast ingot to 480 ℃, extruding with the extrusion ratio of 50, and then carrying out on-line air cooling quenching at the cooling rate of 100 ℃/min to obtain a wrought aluminum alloy; heating the obtained wrought aluminum alloy to 150 ℃ at the speed of 5 ℃/min, and preserving heat at 150 ℃ for 2h for aging treatment to obtain aged aluminum alloy; and carrying out primary cold drawing on the obtained aging aluminum alloy with the deformation of 25% to obtain the aluminum alloy.
Metallographic microscope observation of the aluminum alloy obtained in example 1 was carried out, and the obtained metallographic image is shown in FIG. 2. The aluminum alloy obtained in example 1 was subjected to electron back-scattering diffraction test, and the EBSD photograph is shown in FIG. 3. As can be seen from FIGS. 2 to 3, the aluminum alloy provided by the present invention has fine crystal grains and a fibrous crystal structure.
The aluminum alloy obtained in example 1 was subjected to scanning electron microscope test, and the SEM image is shown in FIG. 4. As can be seen from figure 4, in the aluminum alloy provided by the invention, the insoluble primary second phase (spheroidized white particles in the figure) is fine and dispersed, the soluble second phase MgSi is not generated, and AlCr is precipitated at high temperature7、AlZr3And MnAl6And (4) uniformly dispersing and distributing.
The X-ray energy spectrum analysis was performed on the "spectrum 1" site in FIG. 4, and the obtained EDS chart is shown in FIG. 5. As can be seen from FIG. 5, the "spectrum 1" site of FIG. 4 contains mainly Mn and Al, forming MnAl6A phase precipitated.
Example 2
The aluminum alloy is designed to have the element composition of 0.18 percent of Cu, 0.38 percent of Fe, 1.10 percent of Mn, 0.18 percent of Si, 0.20 percent of Mg, 0.07 percent of Zr, 0.05 percent of Cr, 0.02 percent of Ti, and the balance of Al and inevitable impurities according to the mass percentage; the content of single inevitable impurities is less than or equal to 0.05 percent, and the total content is less than or equal to 0.15 percent;
preparing an aluminum alloy: smelting alloy raw materials conforming to the composition of the design elements at 760 ℃ for 3h, and casting the obtained molten liquid at 710 ℃ to obtain an aluminum alloy ingot;
heating the aluminum alloy cast ingot to 530 ℃ at the speed of 3.5 ℃/min, preserving heat for 3h at 530 ℃, then heating to 580 ℃ at the speed of 3.5 ℃/min, preserving heat for 8h at 580 ℃, cooling to 460 ℃ at the speed of 1.0 ℃/min, preserving heat for 2h at 460 ℃, and air-cooling to room temperature to obtain a homogenized cast ingot; then heating the obtained homogenized cast ingot to 480 ℃, extruding with the extrusion ratio of 40, and then carrying out on-line air cooling quenching at the cooling rate of 100 ℃/min to obtain a wrought aluminum alloy; heating the obtained wrought aluminum alloy to 150 ℃ at the speed of 5 ℃/min, and carrying out aging treatment at the temperature of 150 ℃ for 2h to obtain an aging aluminum alloy; and carrying out primary cold drawing on the obtained aged aluminum alloy with the deformation of 25% to obtain the aluminum alloy.
Example 3
The aluminum alloy is designed to have the element composition of 0.15% of Cu, 0.38% of Fe, 1.07% of Mn, 0.10% of Si, 0.17% of Mg, 0.05% of Zr, 0.05% of Cr, 0.02% of Ti, and the balance of Al and inevitable impurities by mass percentage; the content of single inevitable impurities is less than or equal to 0.05 percent, and the total content is less than or equal to 0.15 percent;
preparing an aluminum alloy: smelting alloy raw materials conforming to the composition of the design elements at 750 ℃ for 3h, and casting the obtained melt at 710 ℃ to obtain an aluminum alloy ingot;
heating the aluminum alloy cast ingot to 530 ℃ at the speed of 3 ℃/min, preserving heat for 3h at 530 ℃, then heating to 580 ℃ at the speed of 3 ℃/min, preserving heat for 8h at 580 ℃, cooling to 460 ℃ at the speed of 0.8 ℃/min, preserving heat for 2h at 460 ℃, and air-cooling to room temperature to obtain a homogenized cast ingot; then heating the obtained homogenized cast ingot to 480 ℃, extruding with the extrusion ratio of 30, and then carrying out on-line air cooling quenching at the cooling rate of 100 ℃/min to obtain a wrought aluminum alloy; heating the obtained wrought aluminum alloy to 150 ℃ at the speed of 5 ℃/min, and preserving heat at 150 ℃ for 2h for aging treatment to obtain aged aluminum alloy; and carrying out primary cold drawing on the obtained aged aluminum alloy with the deformation of 25% to obtain the aluminum alloy.
Example 4
The aluminum alloy is designed to have the element composition of, by mass, 0.12% of Cu, 0.34% of Fe, 1.05% of Mn, 0.09% of Si, 0.16% of Mg, 0.04% of Zr, 0.03% of Cr, 0.02% of Ti, and the balance of Al and unavoidable impurities; the content of single inevitable impurities is less than or equal to 0.05 percent, and the total content is less than or equal to 0.15 percent;
preparing an aluminum alloy: smelting alloy raw materials conforming to the composition of the design elements at 760 ℃ for 4h, and casting the obtained molten liquid at 720 ℃ to obtain an aluminum alloy ingot;
heating the aluminum alloy cast ingot to 530 ℃ at the speed of 3.5 ℃/min, preserving heat for 3h at 530 ℃, then heating to 580 ℃ at the speed of 3.5 ℃/min, preserving heat for 8h at 580 ℃, cooling to 460 ℃ at the speed of 1.0 ℃/min, preserving heat for 2h at 460 ℃, and air-cooling to room temperature to obtain a homogenized cast ingot; then heating the obtained homogenized cast ingot to 480 ℃, extruding with the extrusion ratio of 50, and then carrying out on-line air cooling quenching at the cooling rate of 100 ℃/min to obtain a wrought aluminum alloy; heating the obtained wrought aluminum alloy to 150 ℃ at the speed of 5 ℃/min, and preserving heat at 150 ℃ for 2h for aging treatment to obtain aged aluminum alloy; and carrying out primary cold drawing on the obtained aged aluminum alloy with the deformation of 25% to obtain the aluminum alloy.
Comparative example 1
The aluminum alloy is designed to have the element composition of 0.15% of Cu, 0.30% of Fe, 1.06% of Mn, 0.10% of Si, 0.17% of Mg, 0.02% of Zr, 0.02% of Cr, 0.02% of Ti, and the balance of Al and inevitable impurities by mass percentage; the content of single inevitable impurities is less than or equal to 0.05 percent, and the total content is less than or equal to 0.15 percent;
the preparation method of the aluminum alloy was the same as that of example 1 to obtain an aluminum alloy.
Comparative example 2
The aluminum alloy is designed to have the element composition of 0.15% of Cu, 0.38% of Fe, 1.07% of Mn, 0.10% of Si, 0.17% of Mg, 0.05% of Zr, 0.05% of Cr, 0.02% of Ti, and the balance of Al and inevitable impurities by mass percentage; the content of single inevitable impurities is less than or equal to 0.05 percent, and the total content is less than or equal to 0.15 percent;
in the preparation method of the aluminum alloy, the uniform treatment comprises the following steps: heating the aluminum alloy ingot to 530 ℃ at the speed of 3 ℃/min, preserving heat for 3h at 530 ℃, then heating to 580 ℃ at the speed of 3 ℃/min, preserving heat for 8h at 580 ℃, and air-cooling to room temperature to obtain a homogenized ingot; the rest of the technical means are consistent with those of the example 3, and the aluminum alloy is obtained.
Comparative example 3
The aluminum alloy is designed to have the element composition of, by mass, 0.15% of Cu, 0.38% of Fe, 1.07% of Mn, 0.10% of Si, 0.17% of Mg, 0.05% of Zr, 0.05% of Cr, 0.02% of Ti, and the balance of Al and inevitable impurities; the content of single inevitable impurities is less than or equal to 0.05 percent, and the total content is less than or equal to 0.15 percent;
in the preparation method of the aluminum alloy, the aluminum alloy is obtained without aging treatment, and the other technical means are the same as those in the embodiment 3.
Comparative example 4
The aluminum alloy is designed to have the element composition of 0.15% of Cu, 0.38% of Fe, 1.07% of Mn, 0.10% of Si, 0.17% of Mg, 0.05% of Zr, 0.05% of Cr, 0.02% of Ti, and the balance of Al and inevitable impurities by mass percentage; the content of single inevitable impurities is less than or equal to 0.05 percent, and the total content is less than or equal to 0.15 percent;
in the preparation method of the aluminum alloy, the uniform treatment comprises the following steps: heating the aluminum alloy ingot to 530 ℃ at the speed of 3 ℃/min, preserving heat for 3 hours at 530 ℃, then heating to 560 ℃ at the speed of 3 ℃/min, preserving heat for 8 hours at 560 ℃, then cooling to 460 ℃ at the speed of 0.8 ℃/min, preserving heat for 2 hours at 460 ℃, and air-cooling to room temperature to obtain a homogenized ingot; the rest of the technical means are consistent with those of the example 3, and the aluminum alloy is obtained.
Comparative example 5
The aluminum alloy is designed to have the element composition of 0.10 percent of Cu, 0.33 percent of Fe, 1.05 percent of Mn, 0.06 percent of Si, 0.10 percent of Mg, 0.10 percent of Cr, 0.02 percent of Ti and the balance of Al and inevitable impurities according to the mass percentage; the content of single inevitable impurities is less than or equal to 0.05 percent, and the total content is less than or equal to 0.15 percent;
the preparation method of the aluminum alloy was the same as that of example 1 to obtain an aluminum alloy.
Respectively observing an extruded product obtained by extrusion treatment in the preparation process of the aluminum alloy obtained in the embodiment 1-3 and the aluminum alloy obtained in the comparative example 1-5 and a cold-drawn product obtained by cold drawing, wherein the size of the extruded product is shown in figure 6, and the extruded product obtained by extrusion is a square shell with the wall thickness of 0.50-0.65 mm and the circumscribed circle diameter of 128 mm; the size of a cold-drawn product obtained by cold drawing is shown in figure 7, and the cold-drawn product obtained by cold drawing is a square shell with the wall thickness of 0.40-0.50 mm and the diameter of an external circle of 128 mm; the aluminum alloys obtained in examples 1 to 3 and comparative examples 1 to 5 were subjected to tensile strength tests using a universal material testing machine according to the room temperature test method of part 1 of the tensile test of the metal material of GB T228.1-2010, and the test results are shown in Table 1.
TABLE 1 test results of Performance of aluminum alloys obtained in examples 1 to 3 and comparative examples 1 to 5
Note: in Table 1, "/" indicates: cold drawing is a post-extrusion procedure, and cold drawing and subsequent tensile strength testing cannot be performed because comparative example 4 fails to extrude.
As can be seen from the table 1, the aluminum alloy for the thin-wall square shell provided by the invention has good extrusion performance and cold drawing performance; the tensile strength can reach 182-200 MPa, and the tensile strength is high.
The foregoing is only a preferred embodiment of the present invention, and it should be noted that, for those skilled in the art, various modifications and decorations can be made without departing from the principle of the present invention, and these modifications and decorations should also be regarded as the protection scope of the present invention.
Claims (9)
1. The aluminum alloy is characterized by comprising the following elements in percentage by mass:
0.10-0.18% of Cu, 0.33-0.38% of Fe, 1.05-1.10% of Mn, 0.06-0.18% of Si, 0.10-0.20% of Mg, 0.04-0.07% of Zr, 0.03-0.05% of Cr, less than or equal to 0.03% of Ti, and the balance of Al and inevitable impurities;
the mass ratio of Mn to Fe is (2.8-3.2): 1, the total content of Mn and Fe is less than or equal to 1.45 wt.%;
the content of single element in the inevitable impurities is less than or equal to 0.05 percent, and the total content of the inevitable impurities is less than or equal to 0.15 percent;
the preparation method of the aluminum alloy comprises the following steps:
smelting and casting the alloy raw materials in sequence to obtain an aluminum alloy ingot;
and carrying out homogenization treatment, extrusion treatment, quenching, aging treatment and cold drawing on the aluminum alloy cast ingot in sequence to obtain the aluminum alloy.
2. The aluminum alloy of claim 1, wherein the aluminum alloy has a tensile strength of 180 to 200 MPa.
3. The aluminum alloy of claim 1, wherein the aluminum alloy is extruded under extrusion conditions: the limit wall thickness is 0.55mm, and the limit circumscribed circle diameter of the square section profile is 140 mm;
the aluminum alloy is prepared by the following steps: the limit wall thickness is 0.4mm, and the limit circumcircle diameter of the square section profile is 138.5 mm.
4. A method for producing an aluminum alloy as recited in any one of claims 1 to 3, comprising the steps of:
smelting and casting the alloy raw materials in sequence to obtain an aluminum alloy ingot;
and carrying out homogenization treatment, extrusion treatment, quenching, aging treatment and cold drawing on the aluminum alloy cast ingot in sequence to obtain the aluminum alloy.
5. The production method according to claim 4, wherein the homogenization treatment includes a first homogenization treatment, a second homogenization treatment, and a third homogenization treatment which are performed in this order;
the heat preservation temperature of the first homogenization treatment is 520-540 ℃, and the heat preservation time is 2-4 h;
the heat preservation temperature of the second homogenization treatment is 580-600 ℃, and the heat preservation time is 6-10 hours;
the heat preservation temperature of the third homogenization treatment is 460-480 ℃, and the heat preservation time is 2-4 h.
6. The method according to claim 4, wherein the extrusion temperature is 460 to 520 ℃ and the extrusion ratio is 30 to 150.
7. The preparation method according to claim 4, wherein the temperature of the aging treatment is 150-170 ℃ and the time of the aging treatment is 1-3 h.
8. The production method according to claim 4, wherein the cold drawing is primary cold drawing, and the deformation amount of the cold drawing is 15-30%.
9. Use of the aluminum alloy according to any one of claims 1 to 3 or the aluminum alloy prepared by the preparation method according to any one of claims 4 to 8 as a thin-walled square shell profile in a battery case.
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| JPH116044A (en) * | 1997-06-13 | 1999-01-12 | Aisin Keikinzoku Kk | High strength/high toughness aluminum alloy |
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