CN115094276A - Aluminum alloy and preparation method and application thereof - Google Patents

Aluminum alloy and preparation method and application thereof Download PDF

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Publication number
CN115094276A
CN115094276A CN202210756008.5A CN202210756008A CN115094276A CN 115094276 A CN115094276 A CN 115094276A CN 202210756008 A CN202210756008 A CN 202210756008A CN 115094276 A CN115094276 A CN 115094276A
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percent
aluminum alloy
temperature
equal
less
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CN115094276B (en
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丁小理
李信
许南
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Guangdong Hoshion Industrial Aluminium Co ltd
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Guangdong Hoshion Industrial Aluminium Co ltd
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Priority to PCT/CN2022/134073 priority patent/WO2024001012A1/en
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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
    • 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
    • C22F1/002—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working by rapid cooling or quenching; cooling agents used therefor
    • 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
    • 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
    • H01M50/224—Metals
    • 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
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • 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

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Inorganic Chemistry (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Electrochemistry (AREA)
  • General Chemical & Material Sciences (AREA)
  • Extrusion Of Metal (AREA)
  • Sealing Battery Cases Or Jackets (AREA)

Abstract

The invention discloses an aluminum alloy and a preparation method and application thereof, and relates to the technical field of aluminum alloys. The aluminum alloy consists of the following elements in percentage by mass: less than or equal to 0.05 percent of Cu, less than or equal to 0.12 percent of Fe, 1.05 to 1.50 percent of Mn1.12 to 0.25 percent of Si, 0.10 to 0.20 percent of Mg0.08 to 0.15 percent of Ce0.03 to 0.07 percent of La0.02 to 0.06 percent of B, less than or equal to 0.01 percent of Cr, less than or equal to 0.03 percent of Ti, less than or equal to 0.15 percent of impurity and the balance of Al. The invention balances the relationship between the strength, the fluidity and the quenching sensitivity of the aluminum alloy through the proportion of each element, and the aluminum alloy has good corrosion resistance, excellent heat conduction performance, laser weldability and applicable strength. The method is particularly suitable for manufacturing square or round aluminum alloy power battery shells with different wall thicknesses and thin walls.

Description

Aluminum alloy and preparation method and application thereof
Technical Field
The invention relates to the technical field of aluminum alloy, in particular to aluminum alloy and a preparation method and application thereof.
Background
The replacement of steel with aluminum for power battery cases has been an irreversible trend due to weight reduction requirements. Meanwhile, in order to improve space utilization and charge capacity, aluminum alloy power battery cases have also become an irreversible trend toward being lighter and thinner. The thickness of the shell of the battery shell is gradually reduced from the initial 1.4mm, and at the present stage, the thickness of the shell is mostly a square battery shell with the thickness of 0.5 mm-0.7mm and a circular battery shell with the thickness of about 0.3 mm. Among them, the square battery case is particularly preferred because of its high space utilization. Because the existing thin-wall battery case cannot meet the safety requirement, in order to improve the safety, an explosion-proof sheet needs to be directly installed on the case, and therefore the requirement direction of the battery case is gradually changed from the original constant-wall-thickness product to a product with unequal wall thickness.
The manufacturing method of the aluminum alloy power battery shell in the prior art comprises the following steps: firstly, 3003 material or improved alloy is selected and rolled into thin plate, and then is cut and deep-drawn to form the alloy; secondly, 3003 material or improved alloy is selected and extruded into a plate, and then the plate is cut and then is extruded reversely; selecting 3003 material or improved alloy, hot extruding into square shell or round tube, and cold drawing to obtain the final product; and fourthly, 6063 alloy or modified alloy is selected and extruded and then aged. The first, second and third manufacturing methods all comprise cold working hardening processes, the manufacturing process is long, the yield of the superposition process is high, and the cost is high. Wherein, the first and second manufacturing methods can not produce the aluminum alloy power battery shell with unequal wall thickness. In the third manufacturing method, although the aluminum alloy power battery shell with different wall thicknesses can be manufactured, because the wall thicknesses of two adjacent edges of the power battery shell are different, wavy lines, wrinkles and even breakage often occur at the positions of the different wall thicknesses, so that the drawing cannot be carried out. The fourth manufacturing procedure of the manufacturing method is shortest, but because the hot extrusion molding belongs to hot working, the manufacturing method is also very difficult to prepare the power battery shell with unequal wall thickness, thin size (the thinnest reaches 0.3mm) and high dimensional precision.
Therefore, it is desirable to provide an aluminum alloy which has good corrosion resistance, thermal conductivity, laser weldability and applicable strength, and can be used for preparing power battery cases with different wall thicknesses.
Disclosure of Invention
The present invention is directed to solving at least one of the problems of the prior art. Therefore, the aluminum alloy provided by the invention can be used for preparing power battery cases with different wall thicknesses while ensuring good corrosion resistance, heat conductivity, laser weldability and applicable strength.
The invention also provides a preparation method of the aluminum alloy.
The invention also provides application of the aluminum alloy.
An aluminum alloy according to an embodiment of the first aspect of the invention consists of, in mass percent: less than or equal to 0.05 percent of Cu, less than or equal to 0.12 percent of Fe, 1.05 to 1.50 percent of Mn1.12 to 0.25 percent of Si, 0.10 to 0.20 percent of Mg0.08 to 0.15 percent of Ce0.03 to 0.07 percent of La0.02 to 0.06 percent of B, less than or equal to 0.01 percent of Cr, less than or equal to 0.03 percent of Ti, less than or equal to 0.15 percent of impurity and the balance of Al.
The aluminum alloy provided by the embodiment of the invention has at least the following beneficial effects:
the aluminum alloy of the embodiment of the invention balances the relationship between the strength of the aluminum alloy and the fluidity and quenching sensitivity through the proportion of each element. The aluminum alloy has good corrosion resistance and excellent heat conductivity, and has laser weldability and application strength. The method is particularly suitable for manufacturing square or round aluminum alloy power battery shells with different wall thicknesses and thin walls (the thinnest wall thickness is 0.3-0.7 mm, and the local thickness is 1.2-2.0 mm).
The aluminum alloy of the embodiment of the invention takes manganese (Mn) as a main alloy element, and Mn and aluminum (Al) form MnAl 6 And (4) phase(s). Silicon (Si) and magnesium (Mg) have solid solution strengthening effect in aluminum alloy, and Mg can be precipitated 2 A Si strengthening phase. Aluminum alloy strength dependent on Mn content, Mg 2 The Si content increases, but the increase in strength tends to increase the resistance to press deformation, resulting in a serious deterioration in the press-formability. The invention ensures the extrudability of the aluminum alloy and good weldability, thermal conductivity and corrosion resistance by limiting the use amounts of Mn, Mg and Si.
Cerium (Ce) and lanthanum (La) eliminate coarse compounds in the cast ingot, improve the shape of precipitates, reduce the hot extrusion force and provide certain alloy fluidity. At the same time, Ce, La and Al form Al 11 La 3 、Al 4 La、Al 11 Ce 3 And A1 4 The granular or rod-shaped second phase of Ce plays a role in dispersion strengthening, and the mechanical property is further improved.
Boron (B) can suitably improve the heat-conducting property of the aluminum alloy. However, when the element B exceeds a certain amount, B and Ti easily form hard particles, thereby affecting the high-temperature fluidity of the material. The invention ensures the high-temperature fluidity and the thermal conductivity of the aluminum alloy by limiting the dosage of B.
Copper (Cu) can improve the strength of aluminum alloys, but can reduce the corrosion resistance, increase the extrusion deformation resistance, and significantly improve the quenching sensitivity. The invention controls the addition of Cu on the premise of ensuring high strength.
Chromium (Cr) is a microalloying element of the aluminum alloy, can obviously improve the quenching sensitivity of the alloy and improve the extrusion deformation resistance of the alloy, but the Cr and the Al generate phase change reaction during homogenization treatment to form AlCr 7 Is a thermodynamically stable fine dispersed phase which inhibits recrystallization and grain growth.
According to some embodiments of the invention, the composition consists of, in mass percent: less than or equal to 0.05 percent of Cu, less than or equal to 0.09 percent of Fe, 1.25 to 1.38 percent of Mn1.20 to 0.25 percent of Si, 0.12 to 0.20 percent of Mg0.10 to 0.12 percent of Ce0.10 to 0.12 percent of La0.05 to 0.07 percent of B, less than or equal to 0.01 percent of Cr, 0.01 to 0.02 percent of Ti0.02 percent of impurity, less than or equal to 0.15 percent of Al and the balance of Al.
According to some embodiments of the invention, the impurities are elements other than Cu, Fe, Mn, Si, Mg, Ce, La, B, Cr, Ti and Al.
According to some embodiments of the invention, the mass percentage of a single said impurity is ≦ 0.05%.
According to some embodiments of the invention, the sum of the mass percentages of all the impurities is 0.15% or less.
According to some embodiments of the invention, the aluminum alloy further comprises at least one of magnesium, aluminum, and magnesium 2 The mass percent of Si is 0.16-0.32%.
According to some embodiments of the invention, the excess Si in the aluminum alloy is ≦ 0.19%. Although Si has a certain effect of improving the strength of the aluminum alloy, the ductility of the material is significantly reduced by the excess Si.
By controlling the dosage of Si and Mg, a certain precipitation strengthening effect is ensured, and no excess Mg exists. The welding defects that small holes are formed and air holes are easily generated due to the fact that Mg element is evaporated and steam pressure is high when the aluminum alloy power battery shell is subjected to subsequent welding treatment are effectively avoided.
According to some embodiments of the invention, the sum of the mass percentages of Fe and Mn in the aluminum alloy is less than or equal to 1.5%. If the sum of the mass percentages of iron (Fe) and Mn is outside this range, a large number of coarse flaky (FeMn) AL is formed 6 Thereby reducing the ductility of the aluminum alloy.
According to some embodiments of the invention, the aluminum alloy comprises 0.01% to 0.03% by mass of Cu.
According to some embodiments of the invention, the aluminum alloy has a Cu content of 0.02% by mass.
According to some embodiments of the invention, the aluminum alloy comprises 0.05% to 0.09% Fe by mass.
According to some embodiments of the invention, the aluminum alloy comprises 0.07% to 0.09% by mass of Fe.
According to some embodiments of the invention, the aluminum alloy has a Fe content of 0.08% by mass.
According to some embodiments of the invention, the aluminum alloy comprises 0.23 to 0.25% by mass of Si.
According to some embodiments of the invention, the aluminum alloy comprises 0.18 to 0.20 mass% Mg.
According to some embodiments of the invention, the mass percentage of Ce in the aluminum alloy is 0.10% to 0.12%.
According to some embodiments of the invention, the aluminum alloy comprises 0.03 to 0.07% by mass of La.
According to some embodiments of the invention, the aluminum alloy comprises 0.01% to 0.03% by mass of B.
According to some embodiments of the invention, the aluminum alloy comprises 0.007% to 0.009% Cr by weight.
According to some embodiments of the invention, the aluminum alloy has a Cr content of 0.008% to 0.009% by mass.
According to some embodiments of the invention, the aluminum alloy has a Cr content of 0.009% by mass.
According to some embodiments of the invention, the aluminum alloy comprises 0.01 to 0.02 mass% Ti.
According to some embodiments of the invention, the aluminum alloy has a Ti content of 0.013% to 0.017% by mass.
According to some embodiments of the invention, the aluminum alloy has a tensile strength of 180MPa or more.
According to some embodiments of the invention, the aluminum alloy has a tensile strength of 210MPa to 230 MPa.
According to some embodiments of the invention, the aluminum alloy has a yield strength ≧ 170 MPa.
According to some embodiments of the invention, the aluminum alloy has a yield strength of 170 to 190 MPa.
According to some embodiments of the invention, the aluminum alloy has an elongation after fracture of ≧ 12%.
According to some embodiments of the invention, the aluminum alloy has an elongation after fracture of 12% to 20%.
The preparation method of the aluminum alloy comprises the following steps:
s1: after an additive containing the alloy elements is added into the aluminum melt, casting is carried out to form an ingot A;
s2: homogenizing the ingot A to obtain an ingot B;
s3: preheating the cast ingot B to a first temperature, and then heating to a second temperature for extrusion and quenching treatment to obtain an extruded aluminum alloy C;
the first temperature is T- (5-20) DEG C; the second temperature is T +/-5 ℃; the T is 460-520 ℃; the first temperature is lower than the second temperature;
s4: and carrying out aging treatment on the extruded aluminum alloy C.
The preparation method of the aluminum alloy provided by the embodiment of the invention has at least the following beneficial effects:
by the preparation method, the power battery shell with high dimensional precision can be directly obtained by extrusion, and additional size finishing and straightening treatment of cold machining is not needed; and the strength requirement of the aluminum alloy power battery shell can be met without cold work hardening. The preparation method of the embodiment of the invention adopts all technical schemes of the aluminum alloy of the embodiment, so that the preparation method at least has all beneficial effects brought by the technical schemes of the embodiment.
According to some embodiments of the invention, the additive comprises an additive of silicon, manganese, magnesium, boron, lanthanum, cerium and copper.
According to some embodiments of the invention, the additive of silicon comprises an Al-Si master alloy.
According to some embodiments of the invention, the additive to silicon is an Al-Si12 master alloy.
According to some embodiments of the invention, the additive of manganese comprises an Al-Mn master alloy.
According to some embodiments of the invention, the additive of manganese is an Al-Mn10 master alloy.
According to some embodiments of the invention, the additive of magnesium comprises a magnesium ingot.
According to some embodiments of the invention, the boron additive comprises an Al-B master alloy.
According to some embodiments of the invention, the boron additive is an Al-B1 master alloy.
According to some embodiments of the invention, the lanthanum cerium additive comprises a misch metal.
According to some embodiments of the invention, step S1 specifically includes the following steps:
s1 a: melting the aluminum ingot to obtain a melt;
s1 b: adding Al-Si intermediate alloy, magnesium ingot, Al-Mn intermediate alloy, Al-B intermediate alloy, mixed rare earth and Al-Ti-B intermediate alloy into the melt obtained in the step S1 a;
s1 c: adding a refining agent into the melt obtained in the step S1b for refining;
s1 d: adjusting the components of the melt obtained in the step S1 c;
s1 e: the melt obtained in step S1d is cast, and an Al-Ti-B alloy is added to the melt in the casting.
According to some embodiments of the invention, the heating temperature of step S1a is 730 ℃ to 770 ℃.
According to some embodiments of the invention, the heating temperature of step S1a is 740 ℃ to 760 ℃.
According to some embodiments of the invention, the heating temperature of step S1a is 750 ℃.
According to some embodiments of the invention, the refining temperature of step S1c is 730 ℃ to 750 ℃.
According to some embodiments of the invention, the refining temperature of step S1c is 735 ℃ to 745 ℃.
According to some embodiments of the invention, the refining time of step S1c is 10min to 40 min.
According to some embodiments of the invention, the refining time of step S1c is 10min to 30 min.
According to some embodiments of the invention, the refining time of step S1c is 15min to 25 min.
According to some embodiments of the invention, the number of refinements of step S1c is 2. The time interval between two refining processes is more than 30 min.
According to some embodiments of the invention, the refining agent of step S1c is added in an amount of: 1kg-2.5kg refining agent is added to each ton of melt.
According to some embodiments of the invention, the refining agent of step S1c is added in an amount of: 1.5kg-2kg of refining agent is added to each ton of melt.
According to some embodiments of the invention, the refining agent of step S1c is added in an amount of: 1.5kg of refining agent per ton of melt was added.
In some embodiments of the present invention, in step S1c, argon gas is introduced from the bottom of the melt during the refining process, and the obtained melt is subjected to stirring, degassing and slagging-off operations.
In some embodiments of the invention, the effect of the composition adjustment in step S1d is to ensure that the resulting melt is the same composition (except for titanium) as the aluminum-based material to be produced.
According to some embodiments of the invention, in step S1d, the Al-Ti-B master alloy is Al-Ti5-B1 alloy.
According to some embodiments of the invention, the casting step S1 further includes adding an Al-Ti-B alloy to the melt. m is
According to some embodiments of the invention, the temperature of the casting is 690 ℃ -730 ℃ in step S1.
According to some embodiments of the invention, the temperature of the casting is 700 ℃ to 720 ℃ in step S1.
According to some embodiments of the invention, the temperature of the casting is 705 ℃ to 715 ℃ in step S1.
According to some embodiments of the invention, the temperature of the casting is 710 ℃ in step S1.
According to some embodiments of the present invention, step S1 is performed in a regenerative flame reflection energy saving furnace.
According to some embodiments of the invention, in step S1, the casting method is semi-continuous water-cooled casting.
According to some embodiments of the invention, step S1 further includes melt purity processing. The melt purity treatment comprises furnace purification and online melt purification treatment. Except for the common conventional furnace purification measures, the method is matched with the online box degassing and the melt purity treatment measure of the ceramic filter plate series tubular filter to realize that the H content is less than or equal to 0.12ml/100 gAl. Therefore, the high purity of the cast ingot is realized, the corrosion resistance of the product is favorably improved, and the defects of air holes and the like can be avoided.
According to some embodiments of the invention, in step S2, the homogenization treatment includes a first homogenization treatment and a second homogenization treatment.
According to some embodiments of the invention, the temperature of the first homogenization treatment in step S2 is 560 ℃ to 580 ℃.
According to some embodiments of the invention, in step S2, the temperature of the first homogenization treatment is 560 ℃ to 570 ℃.
According to some embodiments of the invention, the temperature of the first homogenization treatment in step S2 is 565 ℃ to 575 ℃.
According to some embodiments of the invention, the temperature of the first homogenization treatment in step S2 is 570 ℃.
According to some embodiments of the invention, in step S2, the holding time of the first homogenization treatment is 4h to 8 h.
According to some embodiments of the invention, in step S2, the holding time of the first homogenization treatment is 5h to 7 h.
According to some embodiments of the invention, in step S2, the holding time of the first homogenization treatment is 5.5h to 6.5 h.
According to some embodiments of the invention, the holding time of the first homogenization treatment in step S2 is 6 h.
According to some embodiments of the invention, in step S2, the temperature of the second homogenization treatment is 430 ℃ to 460 ℃.
According to some embodiments of the invention, in step S2, the temperature of the second homogenization treatment is 440 ℃ to 460 ℃.
According to some embodiments of the invention, the temperature of the second homogenization treatment in step S2 is 440 ℃ to 450 ℃.
According to some embodiments of the invention, in step S2, the holding time of the second homogenization treatment is 2 to 5 hours.
According to some embodiments of the invention, in step S2, the holding time of the second homogenization treatment is 2 to 4 hours.
According to some embodiments of the invention, in step S2, the holding time of the second homogenization treatment is 3 to 4 hours.
By the homogenization treatment, macro-micro segregation of the alloy elements in the ingot can be eliminated, and the alloy elements and coarse compounds are fully dissolved in the solution. Meanwhile, the alloy of the invention has a large amount of high-temperature precipitated dispersed MnAl 6 Under this treatment, the dispersed phase MnAl is dispersed 6 Can form fine dispersoid, thereby avoiding the large casting stress of the cast ingot from causing large resistance to subsequent extrusion deformation, and MnAl 6 Abnormal precipitation or coarse and large failure of dispersoid, resulting in difficult extrusion, and fibrous crystal and coarse particles formed in the subsequent extrusion processThe mixed crystal state of the coexisting crystal grains influences the strength of the product.
The first homogenization treatment can completely eliminate the macro-micro segregation of Si, Mg and Cu elements in the ingot and promote the spheroidization of Fe phase. The second homogenization treatment can ensure MnAl 6 Fully separated out in a fine and dispersed state.
According to some embodiments of the invention, the homogenizing process further comprises cooling after the second homogenizing process in step S2.
According to some embodiments of the invention, in step S2, the cooling is water mist cooling.
According to some embodiments of the invention, in step S3, preheating the ingot B to T- (7-15) ℃, and then heating to T ± 5 ℃ for extrusion and quenching treatment to obtain an extruded aluminum alloy C; the T is 460-520 ℃.
Through the accurate management and control to ingot B extrusion temperature, be favorable to the homogeneity management and control of extrusion forming power battery shell size precision on the one hand, on the other hand collocation extrusion intensifies, and Mg 2 The solid solution of the Si strengthening phase is realized in the extrusion process so as to ensure the subsequent age precipitation hardening. Further, MnAl 6 The size of the dispersoid is 0.001-0.01 mu m, the dispersoid does not aggregate and grow up, the extrusion deformation resistance is minimum, and the extrusion is facilitated.
According to some embodiments of the invention, in step S3, T is 460 ℃ to 490 ℃.
According to some embodiments of the invention, in step S3, T is 460 ℃ to 480 ℃.
According to some embodiments of the invention, in step S3, the T is 465 ℃ to 475 ℃.
According to some embodiments of the invention, in step S3, the T is 470 ℃.
According to some embodiments of the invention, the cooling rate of the quenching is greater than 100 ℃/min in step S3.
According to some embodiments of the invention, in step S3, the quenching is air-cooled quenching.
According to some embodiments of the invention, in step S3, the final temperature of the quenching is 160 ℃ to 200 ℃.
According to some embodiments of the invention, the final temperature of the quenching is 170 ℃ to 190 ℃ in step S3.
According to some embodiments of the invention, the final temperature of the quenching is 180 ℃ in step S3.
According to some embodiments of the invention, the extrusion speed is 18 m/min to 30 m/min in step S3.
According to some embodiments of the invention, the extrusion speed is 20 m/min to 27 m/min in step S3.
According to some embodiments of the invention, the extrusion speed is 22 m/min to 25 m/min in step S3.
According to some embodiments of the invention, in the step S3, the extrusion ratio of the extrusion process is 30-50.
According to some embodiments of the invention, in the step S3, the extrusion ratio of the extrusion process is 35-45.
According to some embodiments of the invention, in the step S3, the extrusion ratio of the extrusion treatment is 37-42.
According to some embodiments of the invention, in step S3, the pressing ratio of the pressing process is 40.
According to some embodiments of the invention, in step S4, the aging treatment is performed by keeping the temperature at 180 ℃ to 220 ℃ for 0.5h to 4 h.
According to some embodiments of the invention, the aging temperature is 185-215 ℃ in step S4.
According to some embodiments of the invention, the temperature of the aging treatment in step S4 is 190 ℃ to 210 ℃.
According to some embodiments of the invention, in step S4, the aging temperature is 195 ℃ to 205 ℃.
According to some embodiments of the invention, the temperature of the aging treatment in step S4 is 200 ℃.
According to some embodiments of the invention, in step S4, the aging treatment is performed for 1 to 3 hours.
According to some embodiments of the invention, in step S4, the aging treatment is performed for a holding time of 1.5h to 2.5 h.
According to some embodiments of the invention, in step S4, the aging treatment is performed for 2 hours.
According to the preparation method of the aluminum alloy, the performance requirement of the power battery shell can be met only by simple aging treatment without a complex cold processing method with high process cost, and the process is short.
Use of the above aluminium alloy according to an embodiment of the third aspect of the present invention.
According to some embodiments of the present invention, the aluminum alloy of the above embodiments can be used in any field of battery, automobile, machinery manufacturing, electronic products, and chemical industry.
According to some embodiments of the invention, the battery field is in particular battery cases.
According to some embodiments of the present invention, the aluminum alloys of the above embodiments may be used to prepare battery cases of unequal wall thickness.
The battery case with unequal wall thickness is a battery case comprising a thick wall section and a thin wall section and is used for meeting different functional requirements. For example: the battery case is square in cross section, one side is a thick-wall section, the other three sides are thin-wall sections, the circumferential sections of 1/5-1/3 are thick-wall sections, the rest are thin-wall sections, and the thick-wall sections and the thin-wall sections have thickness transition. The battery case with unequal wall thicknesses can be provided with the explosion-proof sheet at the thick wall part, so that the use safety of the battery can be effectively improved. If the cross section of the battery case is circular, the thick wall section and the thin wall section can be respectively as follows: the thickness of the circumferential section of about 1/5 ~ 1/3 is thick wall section, and the rest is thin wall section, and thick wall section and thin wall section have thickness transition.
According to some embodiments of the invention, the battery case is a power battery case.
According to some embodiments of the invention, the battery case is obtained by die pressing.
Additional features and advantages of the invention will be set forth in the description which follows, and in part will be obvious from the description, or may be learned by practice of the invention.
Detailed Description
The concept and technical effects of the present invention will be clearly and completely described below in conjunction with the embodiments to fully understand the objects, features and effects of the present invention. It is obvious that the described embodiments are only a part of the embodiments of the present invention, and not all embodiments, and other embodiments obtained by those skilled in the art without inventive efforts are within the protection scope of the present invention based on the embodiments of the present invention.
The examples, in which specific conditions are not specified, were conducted under conventional conditions or conditions recommended by the manufacturer. The reagents or instruments used are not indicated by the manufacturer, and are all conventional products available commercially. The process is not particularly illustrated, and the process parameters conventional in the art are adopted.
If not specifically stated, in the embodiment of the present invention, the room temperature is 20 to 40 ℃;
the refining agent is a PROMAG RI granular refining agent;
degassing is performed on the box body, specifically, degassing is performed through a degassing box, the degassing box is of a box body structure, 99.99% argon inert gas is introduced into the aluminum melt through an internal special structure, and then the hydrogen content in the aluminum melt is brought out through the principle of partial pressure difference, so that the degassing effect is achieved;
the double-stage filtration comprises plate filtration and tubular filtration, and specifically comprises the steps of sequentially carrying out two low-level and high-level filtration processes on a launder in the casting process of an aluminum melt, wherein the former stage is low-level filtration of a 40-80 ppi filter plate, and the latter stage is high-level filtration of a tubular filter.
Example 1
The aluminum alloy prepared in the embodiment comprises the following components in percentage by mass:
cu: 0.02%, Fe: 0.08%, Mn: 1.30%, Si: 0.23%, Mg: 0.18%, Ce: 0.11%, La: 0.07%, B: 0.02%, Cr: 0.009%, Ti: 0.015%, the balance being Al and unavoidable impurities;
wherein, the content of single inevitable impurity is less than or equal to 0.05 percent, and the content of all inevitable impurities is less than or equal to 0.15 percent.
The preparation method comprises the following steps:
s1, preparing materials according to the proportion and then casting to form an ingot A. The method comprises the following specific steps:
s1 a: and heating the aluminum ingot to 750 ℃ in a heat accumulating type flame reflection energy-saving furnace to melt the aluminum ingot to obtain a melt.
S1 b: and adding Al-Si12 master alloy, magnesium ingot, Al-Mn10 master alloy, Al-B1 master alloy and misch metal to the melt obtained in the step S1 a.
S1 c: adding 1.5 kg/ton refining agent into the melt obtained in the step S1b, refining, wherein the refining temperature is 735-745 ℃, the refining time is 15-25 min, and the refining is carried out twice, and the interval of each time is more than 30 min;
and introducing high-purity argon (with the purity of 99.99%) into the aluminum melt through the furnace bottom air brick during refining, stirring, exhausting, and then slagging off.
S1 d: the melt of step S1c was subjected to compositional adjustment to ensure that the elements other than Ti in the resulting melt were the same as the composition of the aluminum alloy to be produced.
S1 e: and (3) casting the melt obtained in the step S1d by a semi-continuous water-cooling casting method, wherein the casting temperature is 710 ℃, and after Al-Ti5-B1 alloy is added into the melt in the casting process (so as to achieve the purpose of fine grains and control the content of Ti in the obtained cast ingot to be 0.015%), degassing and double-stage filtering are sequentially carried out.
S2, homogenizing:
and (5) heating the ingot A obtained in the step S1 to 570 ℃ and preserving heat for 6h, then cooling to 450 ℃ and preserving heat for 3h, and then cooling to room temperature by water mist to obtain an ingot B.
S3, extrusion and quenching treatment:
preheating the aluminum alloy ingot B obtained in the step S2 to 460 ℃, and then precisely heating the aluminum alloy ingot B to 470 +/-5 ℃ through a power frequency induction furnace. Then carrying out extrusion forming through a square extrusion forming die with unequal wall thickness, carrying out on-line air cooling quenching (the cooling rate is more than 100 ℃/min), passing through a quenching area, and then obtaining the extruded aluminum alloy C, wherein the temperature of the section bar is 180 ℃, the extrusion speed is 25 m/min, and the extrusion ratio is 40.
S4, aging treatment:
and heating the extruded aluminum alloy C of the step S3 to 200 ℃ and keeping the temperature for 2 h.
Example 2 (different from example 1 in the content of Mn, Si and Mg)
The aluminum alloy prepared in the embodiment comprises the following components in percentage by mass:
cu: 0.02%, Fe: 0.08%, Mn: 1.05%, Si: 0.25%, Mg: 0.20%, Ce: 0.11%, La: 0.07%, B: 0.02%, Cr: 0.009%, Ti: 0.015%, the balance being Al and unavoidable impurities;
wherein, the content of single inevitable impurity is less than or equal to 0.05 percent, and the content of all inevitable impurities is less than or equal to 0.15 percent.
The preparation method comprises the following steps:
s1, preparing materials according to the proportion and then casting to form an ingot A. The method comprises the following specific steps:
s1 a: and heating the aluminum ingot to 750 ℃ in a heat accumulating type flame reflection energy-saving furnace to melt the aluminum ingot to obtain a melt.
S1 b: and adding Al-Si12 master alloy, magnesium ingot, Al-Mn10 master alloy, Al-B1 master alloy and misch metal to the melt obtained in the step S1 a.
S1 c: adding 1.5 kg/ton refining agent into the melt obtained in the step S1b, refining, wherein the refining temperature is 735-745 ℃, the refining time is 15-25 min, and the refining is carried out twice, and the interval of each time is more than 30 min;
and introducing high-purity argon (with the purity of 99.99%) into the aluminum melt through the furnace bottom air brick during refining, stirring, exhausting, and then slagging off.
S1 d: the melt of step S1c was subjected to compositional adjustment to ensure that the elements other than Ti in the resulting melt were the same as the composition of the aluminum alloy to be produced.
S1 e: and (2) casting the melt obtained in the step S1d by a semi-continuous water-cooling casting method, wherein the casting temperature is 710 ℃, and degassing and double-stage filtration are sequentially carried out after Al-Ti5-B1 alloy is added into the melt in the casting process (so as to achieve the purpose of fine grain and control the content of Ti in the obtained cast ingot to be 0.015%).
S2, homogenizing:
and (5) heating the ingot A obtained in the step S1 to 570 ℃ and preserving heat for 6h, then cooling to 450 ℃ and preserving heat for 3h, and then cooling to room temperature by water mist to obtain an ingot B.
S3, extrusion and quenching treatment:
preheating the aluminum alloy ingot B obtained in the step S2 to 460 ℃, and then precisely heating the aluminum alloy ingot B to 470 +/-5 ℃ through a power frequency induction furnace. Then carrying out extrusion forming through a square extrusion forming die with unequal wall thickness, carrying out on-line air cooling quenching (the cooling rate is more than 100 ℃/min), passing through a quenching area, and then obtaining the extruded aluminum alloy C, wherein the temperature of the section bar is 180 ℃, the extrusion speed is 25 m/min, and the extrusion ratio is 40.
S4, aging treatment:
and heating the extruded aluminum alloy C of the step S3 to 200 ℃ and keeping the temperature for 2 h.
Example 3 (different from example 1 in the content of Ce and La and the extrusion speed)
The aluminum alloy prepared in the embodiment comprises the following components in percentage by mass:
cu: 0.02%, Fe: 0.08%, Mn: 1.30%, Si: 0.23%, Mg: 0.18%, Ce: 0.08%, La: 0.03%, B: 0.02%, Cr: 0.009%, Ti: 0.015%, the balance being Al and unavoidable impurities;
wherein, the content of single inevitable impurity is less than or equal to 0.05 percent, and the content of all inevitable impurities is less than or equal to 0.15 percent.
The preparation method comprises the following steps:
s1, preparing materials according to the proportion and then casting to form an ingot A. The method comprises the following specific steps:
s1 a: and heating the aluminum ingot to 750 ℃ in a heat accumulating type flame reflection energy-saving furnace to melt the aluminum ingot to obtain a melt.
S1 b: and adding Al-Si12 master alloy, magnesium ingot, Al-Mn10 master alloy, Al-B1 master alloy and misch metal to the melt obtained in the step S1 a.
S1 c: adding 1.5 kgkg/ton of refining agent into the melt obtained in the step S1b, refining, wherein the refining temperature is 735-745 ℃, the refining time is 15-25 min, and the refining is carried out twice, and the interval of each time is more than 30 min;
and introducing high-purity argon (with the purity of 99.99%) into the aluminum melt through the furnace bottom air brick during refining, stirring, exhausting, and then slagging off.
S1 d: the melt of step S1c was subjected to compositional adjustment to ensure that the elements other than Ti in the resulting melt were the same as the composition of the aluminum alloy to be produced.
S1 e: and (2) casting the melt obtained in the step S1d by a semi-continuous water-cooling casting method, wherein the casting temperature is 710 ℃, and degassing and double-stage filtration are sequentially carried out after Al-Ti5-B1 alloy is added into the melt in the casting process (so as to achieve the purpose of fine grain and control the content of Ti in the obtained cast ingot to be 0.015%).
S2, homogenizing treatment:
and (5) heating the ingot A obtained in the step S1 to 570 ℃ and preserving heat for 6h, then cooling to 450 ℃ and preserving heat for 3h, and then cooling to room temperature by water mist to obtain an ingot B.
S3, extrusion and quenching treatment:
preheating the aluminum alloy ingot B obtained in the step S2 to 460 ℃, and then accurately heating to 470 +/-5 ℃ through a power frequency induction furnace. Then carrying out extrusion forming through a square extrusion forming die with unequal wall thickness, carrying out on-line air cooling quenching (the cooling rate is more than 100 ℃/min), wherein the temperature of the section passing through a quenching area is 180 ℃, and the extrusion speed is as follows: 22 m/min, and an extrusion ratio of 40 to obtain an extruded aluminum alloy C.
S4, aging treatment:
heating the extruded aluminum alloy C of the step S3 to 200 ℃ and keeping the temperature for 2 h.
Example 4 (different from example 1 in the homogenization treatment conditions)
The aluminum alloy prepared in the embodiment comprises the following components in percentage by mass:
cu: 0.02%, Fe: 0.08%, Mn: 1.30%, Si: 0.23%, Mg: 0.18%, Ce: 0.11%, La: 0.07%, B: 0.02%, Cr: 0.009%, Ti: 0.015%, the balance being Al and unavoidable impurities;
wherein, the content of single inevitable impurity is less than or equal to 0.05 percent, and the content of all inevitable impurities is less than or equal to 0.15 percent.
The preparation method comprises the following steps:
s1, preparing materials according to the proportion and then casting to form an ingot A. The method comprises the following specific steps:
s1 a: and heating the aluminum ingot to 750 ℃ in a heat accumulating type flame reflection energy-saving furnace to melt the aluminum ingot to obtain a melt.
S1 b: and adding Al-Si12 master alloy, magnesium ingot, Al-Mn10 master alloy, Al-B1 master alloy and misch metal to the melt obtained in the step S1 a.
S1 c: adding 1.5 kg/ton of refining agent into the melt obtained in the step S1b, refining, wherein the refining temperature is 735-745 ℃, the refining time is 15-25 min, and the refining is carried out twice, and the interval of each time is more than 30 min;
and introducing high-purity argon (with the purity of 99.99%) into the aluminum melt through the furnace bottom air brick during refining, stirring, exhausting, and then slagging off.
S1 d: the melt from step S1c was subjected to chemical composition analysis by sampling and composition adjustment to ensure that the elements other than Ti in the resulting melt were the same as in the composition of the aluminum alloy to be produced.
S1 e: and (2) casting the melt obtained in the step S1d by a semi-continuous water-cooling casting method, wherein the casting temperature is 710 ℃, and degassing and double-stage filtration are sequentially carried out after Al-Ti5-B1 alloy is added into the melt in the casting process (so as to achieve the purpose of fine grain and control the content of Ti in the obtained cast ingot to be 0.015%).
S2, homogenizing:
and (5) heating the ingot A obtained in the step S1 to 570 ℃ and preserving heat for 6 hours, then cooling to 440 ℃ and preserving heat for 4 hours, and then cooling with water mist to room temperature to obtain an ingot B.
S3, extrusion and quenching treatment:
preheating the aluminum alloy ingot B obtained in the step S2 to 460 ℃, and then precisely heating the aluminum alloy ingot B to 470 +/-5 ℃ through a power frequency induction furnace. Then carrying out extrusion forming through a square extrusion forming die with unequal wall thickness, carrying out on-line air cooling quenching (the cooling rate is more than 100 ℃/min), passing through a quenching area, and then obtaining the extruded aluminum alloy C, wherein the temperature of the section is 180 ℃, the extrusion speed is 25 m/min, and the extrusion ratio is 40.
S4, aging treatment:
and heating the extruded aluminum alloy C of the step S3 to 200 ℃ and keeping the temperature for 2 h.
Comparative example 1
This comparative example prepared an aluminum alloy, and the specific process differed from example 1 only in that: the raw materials for preparation do not contain Ce, La and B.
Specifically, the aluminum alloy consists of the following components in percentage by mass:
cu: 0.02%, Mn: 1.30%, Si: 0.23%, Mg: 0.18%, Cr: 0.009%, Ti: 0.015%, the balance being Al and unavoidable impurities;
wherein, the content of single inevitable impurity is less than or equal to 0.05 percent, and the content of all inevitable impurities is less than or equal to 0.15 percent.
Comparative example 2
This comparative example prepared an aluminum alloy, and the specific procedure differed from example 1 only in that: the aluminum alloy has different formulas.
Specifically, the aluminum alloy consists of the following components in percentage by mass:
cu: 0.02%, Mn: 0.50%, Si: 0.4%, Mg: 0.35%, V: 0.01%, Cr: 0.20%, Ti: 0.015%, the balance being Al and unavoidable impurities;
wherein the content of single unavoidable impurities is less than or equal to 0.05 percent, and the content of all the unavoidable impurities is less than or equal to 0.15 percent.
Comparative example 3
This comparative example prepared an aluminum alloy, and the specific procedure differed from example 1 only in that: the extrusion and quenching processes of step S3 are different.
Specifically, the extrusion and quenching treatment process of step S3 is as follows:
the aluminum alloy ingot B of step S2 was heated to 470 ℃. Then carrying out extrusion forming through a square extrusion forming die with unequal wall thickness, and carrying out online air cooling quenching (the cooling rate is more than 100 ℃/min), wherein the extrusion speed is as follows: 25 m/min to obtain the extruded aluminum alloy C.
Comparative example 4
This comparative example prepared an aluminum alloy, and the specific procedure differed from example 1 only in that: different contents of Ce and La
Specifically, the aluminum alloy consists of the following components in percentage by mass:
cu: 0.02%, Mn: 1.30%, Si: 0.23%, Mg: 0.18%, Ce: 0.05%, La: 0.03%, B: 0.02%, Cr: 0.009%, Ti: 0.015%, the balance being Al and unavoidable impurities;
wherein, the content of single inevitable impurity is less than or equal to 0.05 percent, and the content of all inevitable impurities is less than or equal to 0.15 percent.
Comparative example 5
This comparative example prepared an aluminum alloy, and the specific procedure differed from example 1 only in that: the homogenization processing in step S2 differs.
Specifically, the homogenization treatment process of step S2 is as follows:
and (5) heating the ingot A obtained in the step S1 to 570 ℃, preserving heat for 6 hours, and then cooling the ingot A to room temperature by water mist to obtain an ingot B.
Example of detection
This example further examined the performance of the aluminum alloys of examples 1-4 and comparative examples 3-5.
The test method specifically comprises the following steps:
the test method of the tensile strength, the yield strength and the elongation after fracture comprises the following steps: GB/T228.1-2010 metallic Material tensile test part 1: room temperature test methods.
The test method of the corrosion resistance comprises the following steps: the Neutral Salt Spray (NSS) test of GB/T10125 and 2012 salt spray test for artificial atmosphere corrosion test has the test time of 720 h; the rating is carried out by referring to the standard in GB/T6461-2002 rating of test pieces and test pieces after corrosion tests of metals and other inorganic coatings on metal substrates.
The test method of the heat conductivity coefficient comprises the following steps: GB/T22588-.
The test method of laser weldability comprises the following steps: ISO 15614-1:2004 metallic Material welding Process Specification and qualification-welding Process test.
The dimensional accuracy of the unequal wall thickness square shells prepared in each example was measured by using a vernier caliper with an accuracy of 0.01 mm. When the side length is 105 plus or minus 0.1mm, the side width is 32 plus or minus 0.1mm, the thin side wall thickness is 0.6 plus or minus 0.05mm, and the thick side wall thickness is 1.5 plus or minus 0.05mm, the judgment is that the requirements are met.
The specific test results are shown in table 1.
TABLE 1
Figure BDA0003722534530000141
As can be seen from table 1, the aluminum alloy for power batteries provided in embodiments 1 to 4 of the present invention meets the requirements for dimensional accuracy, and has good tensile strength, yield strength, elongation after fracture, corrosion resistance, thermal conductivity, and laser weldability.
Comparative example 1 during preparation, the situation that the extrusion speed of the first support rod is low, the flow difference between the thick-wall edge and the thin-wall edge of the product is large, and the mold is plugged occurs, and extrusion forming cannot be performed, so that the square aluminum alloy power battery shell with different wall thicknesses is obtained. This is probably because comparative example 1 does not contain proper amounts of Ce and La, the cast ingot has large rheological stress, and particularly when an asymmetric profile is extruded, the difference between the resistance of the thick-walled edge and the resistance of the thin-walled edge is large, so that the difference between the extrusion speeds of various parts is large, and the part with high flow is pulled by the part with low flow to form blockage, so that the continuous extrusion cannot be carried out. In addition, the aluminum alloy of comparative example 1 does not contain B, so that the thermal conductivity is reduced and the thermal conductivity is deteriorated.
In the preparation of comparative example 2, the extrusion speed of the first support rod is low, the flow difference between the thick-wall edge and the thin-wall edge of the product is large, and the aluminum alloy power battery square shell with different wall thicknesses cannot be obtained by extrusion under the condition of die plugging. This is probably because the main alloying elements of the aluminum alloy of this comparative example were 0.50% Mn, 0.4% Si and 0.35% Mg, and MnAl was precipitated mainly by dispersion 6 、Mg 2 Si to improve the strength of the product. The aluminum alloy has general fluidity, can be used for extruding products with equal wall thickness or integral wall thickness, and when the aluminum alloy is used for extruding products with asymmetric unequal wall thickness and the thinnest wall thickness is very thin (such as 0.3mm-0.7mm), the cast ingot has large rheological stress and large difference between the resistance of a thick wall section and the resistance of a thin wall section, so that each part of the product is subjected to large flow stressThe extrusion speed difference is large, and the part with high flow is pulled by the part with low flow to form blockage, so that the extrusion can not be continuously carried out.
The square shell of the aluminum alloy power battery prepared in the comparative example 3 has the advantages of wavy surface, uneven surface and large wall thickness deviation. The reason for this is probably that the aluminum alloy ingot B is directly heated to 470 ℃ in the comparative example 3, the heating is not carried out through the secondary heating process, and the heating process is not strictly controlled (actually measured single ingot head and tail temperature is 465-572 ℃, and the temperature range between the whole batch of ingots is 462-578 ℃), so that the temperature difference of the ingots in the same batch is large, the temperature change influences the metal rheological stress in the extrusion process, the metal rheological stress is fast when the temperature is high, and the metal rheological stress is slow when the temperature is low. In the case of continuous production using the same set of dies, the extruded product is dimensionally unstable, especially in terms of differences in wall thickness.
Comparative example 4 does not have the condition of mold plugging in the preparation, and the square aluminum alloy power battery shell can be prepared, but the thin edge wall thickness of the square aluminum alloy power battery shell does not meet the requirement, and the situation of scratching occurs. This is probably because the added Ce and La elements are not suitable in content, so that the rheological stress of the cast ingot is still high.
Comparative example 5 does not have the mould blocking condition in the preparation, can prepare and obtain aluminum alloy power battery square shell, but aluminum alloy power battery square shell featheredge wall thickness does not accord with the requirement, and the condition of puting appears. This is probably because comparative example 5 did not perform the secondary homogenization treatment process- "further cool to 450 ℃ and preserve heat for 3 h". Under the process condition, MnAl 6 The precipitation growth affects the structure of the product in the extrusion process, so that coarse crystal and fiber crystal mixed crystal grains are formed, the mechanical property and the corrosion resistance of the product are further affected, and welding cracks are caused. Coarse MnAl 6 When the precipitated phase is the same, the rheological stress of the material is improved, so that the extruded product is easy to scratch.
The embodiments of the present invention have been described in detail, but the present invention is not limited to the embodiments, and various changes can be made without departing from the gist of the present invention within the knowledge of those skilled in the art.

Claims (10)

1. The aluminum alloy is characterized by comprising the following elements in percentage by mass: less than or equal to 0.05 percent of Cu, less than or equal to 0.12 percent of Fe, 1.05 to 1.50 percent of Mn1.12 to 0.25 percent of Si, 0.10 to 0.20 percent of Mg0.08 to 0.15 percent of Ce0.03 to 0.07 percent of La0.02 to 0.06 percent of B, less than or equal to 0.01 percent of Cr, less than or equal to 0.03 percent of Ti, less than or equal to 0.15 percent of impurity and the balance of Al.
2. The aluminum alloy of claim 1, consisting of, in mass percent: less than or equal to 0.05 percent of Cu, less than or equal to 0.09 percent of Fe, 1.25 to 1.38 percent of Mn1.20 to 0.25 percent of Si, 0.12 to 0.20 percent of Mg0.10 to 0.12 percent of Ce0.10 to 0.12 percent of La0.05 to 0.07 percent of B, less than or equal to 0.01 percent of Cr, 0.01 to 0.02 percent of Ti0.02 percent of impurity, less than or equal to 0.15 percent of Al and the balance of Al.
3. The method for producing an aluminum alloy according to claim 1 or 2, characterized by comprising the steps of:
s1: after an additive containing the alloy elements is added into the aluminum melt, casting is carried out to form an ingot A;
s2: homogenizing the ingot A to obtain an ingot B;
s3: preheating the cast ingot B to a first temperature, and then heating to a second temperature for extrusion and quenching treatment to obtain an extruded aluminum alloy C;
the first temperature is T- (5-20) DEG C; the second temperature is T +/-5 ℃; the T is 460-520 ℃; the first temperature is lower than the second temperature;
s4: and carrying out aging treatment on the extruded aluminum alloy C.
4. The production method according to claim 1, wherein in step S2, the homogenization treatment includes a first homogenization treatment and a second homogenization treatment; preferably, the temperature of the first homogenization treatment is 560-570 ℃; preferably, the temperature of the second homogenization treatment is 430-460 ℃.
5. The production method according to claim 3, wherein in step S3, the temperature of the extrusion process is 455-480 ℃; preferably, the temperature of the extrusion process is 465 ℃ to 475 ℃.
6. The method according to claim 4, wherein in step S3, the cooling rate of the quenching is more than 100 ℃/min; preferably, the quenching mode is air cooling quenching; preferably, the final temperature of the extrudate after the quenching is from 170 ℃ to 190 ℃.
7. The method according to claim 4, wherein in step S3, the speed of the extrusion process is 18 m/min to 30 m/min; preferably, the speed of the extrusion treatment is 22-25 m/min; preferably, in step S3, the extrusion ratio of the extrusion process is 30 to 50.
8. The preparation method according to claim 4, wherein in step S4, the temperature of the aging treatment is 170-220 ℃; preferably, the holding time is 0.5h to 4 h.
9. Use of the aluminum alloy of claim 1 or 2 in any of the fields of batteries, automobiles, mechanical manufacturing, electronic products, and chemical industry.
10. Use of an aluminium alloy according to claim 1 or 2 for the production of battery cans of unequal wall thickness.
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