CN111560547A - Preparation method of 5182-O-state aluminum alloy plate for automobile - Google Patents
Preparation method of 5182-O-state aluminum alloy plate for automobile Download PDFInfo
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- CN111560547A CN111560547A CN202010390301.5A CN202010390301A CN111560547A CN 111560547 A CN111560547 A CN 111560547A CN 202010390301 A CN202010390301 A CN 202010390301A CN 111560547 A CN111560547 A CN 111560547A
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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
- C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
- C22C21/08—Alloys based on aluminium with magnesium as the next major constituent with silicon
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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
- C22C1/026—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
- C22C1/00—Making non-ferrous alloys
- C22C1/06—Making non-ferrous alloys with the use of special agents for refining or deoxidising
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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
- C22F1/047—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 of alloys with magnesium as the next major constituent
Abstract
The invention belongs to the technical field of aluminum alloy manufacturing, and relates to a preparation method of a 5182-O state aluminum alloy plate for an automobile, wherein the aluminum alloy raw material is prepared by the following components in percentage by weight: 0.01-0.08%, Fe: 0.15 to 0.30%, Cu: 0.01-0.1%, Mn: 0.10-0.30%, Mg: 4.5-5.0%, Cr is less than or equal to 0.1%, Zn is less than or equal to 0.05%, Ti is less than or equal to 0.1%, Ni is less than or equal to 0.1%, single impurity is less than or equal to 0.05%, the total is less than or equal to 0.15%, and the balance is Al, the aluminum alloy coiled material which is cold-rolled to an intermediate pass in the cold rolling procedure is subjected to intermediate annealing and heat preservation for 2 hours at 320 ℃, wherein the annealing procedure of the finished aluminum alloy coiled material passes through a continuous air cushion annealing furnace in a single-layer mode, and the coiled material is blown up and suspended in the furnace through hot air, so that the problem that the aluminum alloy plate prepared by the existing aluminum alloy plate preparation process has uneven grain structure inside, and.
Description
Technical Field
The invention belongs to the technical field of aluminum alloy manufacturing, relates to a preparation method of a 5182-O state aluminum alloy plate for an automobile, and particularly relates to a preparation method of a 5182-O state aluminum alloy plate for an automobile with excellent stamping performance.
Background
The conventional automobile materials are mostly processed by deep drawing steel sheets, and the degree of aluminum alloying of automobile parts is increasing with the development of automobile lightweight technology in recent years. Taking a plate as an example, the application of the aluminum alloy plate in the automobile is mainly divided into an automobile outer plate and an automobile inner plate. As the automobile industry pays more and more attention to the attractive appearance and smooth lines of the automobile body, the attractive appearance and the smooth lines are realized by stamping, and thus, the automobile body has extremely high requirements on the forming performance of materials.
5000 series aluminum alloy is often used for manufacturing key parts of airplanes and automobiles, such as automobile hubs, automobile body covering parts, oil tank inner covers, engine hood inner plates, airplane large-scale skins and other components. 5000 series aluminum alloys have many advantages, and have strong heat resistance, excellent press formability, and high strength, and thus are sought after. In recent years, 5182-O state aluminum alloy plate is taken as an example, the sheet material basically meets all forming and application indexes of automobile covering parts, and particularly requires parts with good rigidity and high strength for outer plates and the like.
In order to obtain more excellent comprehensive performance of parts formed by the 5182-O aluminum alloy material, and particularly to obtain better performance in the aspect of stamping deformation, the automobile 5182-O aluminum alloy plate with excellent stamping performance needs to be developed. Due to the characteristics of 5182, the material belongs to a work-hardening high magnesium aluminum alloy, during the stamping process, the rapid hardening of a local deformation area can enable the deformation of the material to be more sufficient and uniform, so that the stamping performance is improved, and a higher n (work hardening index) value can bring a higher hardening rate, so that better stamping performance is brought.
The existing aluminum alloy plate preparation process enables the aluminum alloy plate to be insufficiently recrystallized, crystalline grains are not uniform enough, the size is smaller, the nonuniform structure can cause the local deformation of the material to be nonuniform, the n value is not high enough to reflect on the material, and the problem is caused by cracking of the part with large local deformation amount during stamping. Therefore, a new process is needed to solve the problem of grain uniformity inside the aluminum alloy plate, so as to increase the n value.
Disclosure of Invention
In view of the above, the invention provides a preparation method of a 5182-O state aluminum alloy plate for an automobile, which aims to solve the problem that the local deformation and most parts of the aluminum alloy plate are cracked due to the fact that the internal grain structure of the aluminum alloy plate prepared by the existing aluminum alloy plate preparation process is not uniform.
In order to achieve the aim, the invention provides a preparation method of a 5182-O state aluminum alloy plate for an automobile, which comprises the following steps:
A. preparing materials: the 5182 aluminum alloy raw material is proportioned according to the weight percentage that Si: 0.01-0.08%, Fe: 0.15 to 0.30%, Cu: 0.01-0.1%, Mn: 0.10-0.30%, Mg: 4.5-5.0%, Cr is less than or equal to 0.1%, Zn is less than or equal to 0.05%, Ti is less than or equal to 0.1%, Ni is less than or equal to 0.1%, single impurity is less than or equal to 0.05%, total is less than or equal to 0.15%, and the balance is Al;
B. casting: adding the prepared aluminum alloy raw material into a smelting furnace, uniformly mixing, smelting into liquid aluminum alloy, and performing standing, refining, slagging off, online degassing and filtering to obtain aluminum alloy cast ingot;
C. sawing and milling: cutting off the head and the tail of the cast aluminum alloy ingot and milling a surface crust layer;
D. ingot casting and heating: heating the sawn and milled aluminum alloy cast ingot to 530 +/-10 ℃ and preserving heat for 6 hours, then cooling to 500 ℃ and continuing preserving heat for 2-20 hours;
E. hot rolling: carrying out hot rolling on the heated and heat-preserved aluminum alloy cast ingot on a roller way of a rolling mill, wherein the thickness of an aluminum alloy coiled material after hot rolling is 3.0-5.0 mm, the final rolling temperature is 330 ℃, and the aluminum alloy coiled material after hot rolling is naturally cooled to room temperature;
F. cold rolling: the hot-rolled aluminum alloy coiled material is subjected to 2-pass cold rolling on a cold rolling mill to be 1.9mm in thickness and is subjected to intermediate annealing at 320 ℃ for 2 hours, the intermediate annealing can well release internal stress caused by hot rolling, so that the plate basically reaches a complete recrystallization state, the occupation ratio of cubic texture is greatly reduced, the 0-degree directionality of the finished plate is reduced, and the performances in the directions of 45 degrees and 90 degrees are improved, so that the anisotropy of the finished plate is obviously reduced, the aluminum alloy coiled material is subjected to 2-pass cold rolling on the cold rolling mill to be 1.2mm in thickness after the intermediate annealing, the cold rolling deformation is low, and the over-refinement of crystal grains caused by too much deformation energy storage can be prevented;
G. annealing of a finished product: the aluminum alloy finished product thickness coiled material after cold rolling is annealed and insulated for 40s at 480-530 ℃, and passes through the continuous air cushion annealing furnace in a single-layer mode, and the coiled material is blown to be suspended in the furnace through hot air, so that the heat exchange efficiency is greatly improved, the plate can reach the target temperature within 1 minute, the temperature is rapidly raised, the deformation energy storage can be rapidly consumed, more crystal grain cores are formed, and more uniform finished product tissues are brought.
Further, in the step A, the 5182 aluminum alloy raw material is proportioned according to the weight percentage, namely: si: 0.06%, Fe: 0.179%, Cu: 0.01-0.1%, Mn: 0.10-0.30%, Mg: 4.5-5.0%, Cr is less than or equal to 0.1%, Zn is less than or equal to 0.05%, Ti is less than or equal to 0.1%, Ni is less than or equal to 0.1%, single impurity is less than or equal to 0.05%, total is less than or equal to 0.15%, and the balance is Al.
And further, casting the liquid aluminum alloy into an aluminum alloy ingot by adopting a semi-continuous water-cooling casting mode in the step B.
Further, adding an Al-5Ti-B wire refining agent in the refining process in the step B, adopting double rotors for online degassing, and ensuring that the flow of argon is 3.2-7.1 m3Per hour, chlorine flow rate is 0-0.05 m3And h, the rotating speed of the rotor is 400-700 r/min, and the filtering is performed by adopting a double-layer filter plate.
And further, the aluminum alloy ingot after being sawn and milled in the step D is placed in a heating furnace for preheating, the preheating temperature is 350 ℃ and is kept for 2 hours, in order to ensure that the temperature rising steps of all the ingots in the furnace area are consistent, the aluminum alloy ingot is heated to 530 +/-10 ℃ and is kept for 6 hours, and then the temperature is reduced to 500 ℃ and is kept for 2-20 hours.
And furthermore, the cold rolling deformation rate of the aluminum alloy coil subjected to intermediate annealing in the step F is 37%.
The invention has the beneficial effects that:
1. in the preparation method of the 5182-O state aluminum alloy plate for the automobile, disclosed by the invention, when the alloy content is controlled within a certain range, the performance stability of the material is favorably improved. The following description is given for the practical significance of the control range of the contents of the main alloy elements:
mg element can be well dissolved in an Al body in a solid mode, dislocation is pinned, the content of the Mg element is controlled to be 4.5-5.0%, and the material can have high strength.
The Si element can form a strengthening phase and promote the formation and phase change of a second phase, and the content is controlled to be within the range of 0.01-0.08%.
The recrystallization temperature can be regulated and controlled by Mn element, but excessive Mn can cause the generation of coarse hard and brittle compounds during aluminum liquid casting, the formability is influenced, and the content is generally controlled to be 0.10-0.30%.
Fe element can form FeAl with Al element3The Fe-based alloy has the function of refining recrystallized grains, but the excessive Fe has harmful influence on the casting process of the alloy, so the composition of the alloy is most suitable between 0.15 and 0.30 percent.
2. According to the preparation method of the 5182-O state aluminum alloy plate for the automobile, disclosed by the invention, alloy elements can obviously influence the recrystallization process, the control of the recrystallization process in the production process is a key point for improving the n value, and the structure is comprehensively optimized by adjusting homogenization, hot rolling off-line temperature, cold working rate after annealing in cold rolling, improving final annealing temperature, quenching mode and the like. Compared with the prior art, the method has the advantages that the grain structure is further improved by adding the intermediate annealing process and increasing the annealing temperature in the cold rolling process, so that the n value is increased.
3. According to the preparation method of the 5182-O state aluminum alloy plate for the automobile, disclosed by the invention, internal stress caused by hot rolling can be well released by intermediate annealing, so that the plate basically reaches a complete recrystallization state, the percentage of cubic texture is greatly reduced, the 0-degree directionality of the finished plate is reduced, and the performances in the 45-degree and 90-degree directions are improved, so that the anisotropy of the finished plate is obviously reduced, the deformation amount after intermediate annealing is 37%, the cold rolling deformation is low, and the excessive grain refinement caused by deformation energy storage can be prevented.
4. According to the preparation method of the 5182-O state aluminum alloy plate for the automobile, the equipment adopted for finished product annealing is a continuous air cushion annealing furnace, the equipment allows coil materials to pass through the furnace in a single-layer (non-coil) mode, hot air is provided to blow and suspend the coil materials in the furnace, and therefore the heat exchange is improved to the maximum extent, the materials can quickly reach a high target temperature, the annealing time at the high temperature is short and only needs 40s, the temperature is quickly increased, deformation energy storage can be quickly consumed, more crystal grain cores are formed, and therefore a more uniform finished product structure is brought, and the high heat exchange efficiency brings a more appropriate size and a more uniform structure. The method has the advantages of simple process flow and simple and convenient operation, and finally obtains the product with excellent mechanical property and surface quality.
Additional advantages, objects, and features of the invention will be set forth in part in the description which follows and in part will become apparent to those having ordinary skill in the art upon examination of the following or may be learned from practice of the invention. The objectives and other advantages of the invention may be realized and attained by the means of the instrumentalities and combinations particularly pointed out hereinafter.
Drawings
For the purposes of promoting a better understanding of the objects, aspects and advantages of the invention, reference will now be made to the following detailed description taken in conjunction with the accompanying drawings in which:
FIG. 1 is a process flow diagram of a preparation method of a 5182-O state aluminum alloy plate for an automobile.
Detailed Description
The embodiments of the present invention are described below with reference to specific embodiments, and other advantages and effects of the present invention will be easily understood by those skilled in the art from the disclosure of the present specification. The invention is capable of other and different embodiments and of being practiced or of being carried out in various ways, and its several details are capable of modification in various respects, all without departing from the spirit and scope of the present invention.
The preparation method of the 5182-O state aluminum alloy plate for the automobile shown in figure 1 comprises the following steps:
A. preparing materials: the preparation method comprises the following steps of proportioning 5182 aluminum alloy raw materials in percentage by weight, wherein the aluminum alloy raw materials comprise the following elements in percentage by weight:
| element(s) | Si | Fe | Cu | Mn | Mg | Cr | Zn | Ti | Ni | Impurities | Al |
| Content (wt.) | 0.06 | 0.179 | 0.05 | 0.20 | 4.8 | 0.1 | 0.05 | 0.1 | 0.1 | 0.03 | Balance of |
B. Casting: adding the prepared aluminum alloy raw material into a smelting furnace, uniformly mixing, smelting to obtain liquid aluminum alloy, standing, refining, slagging off, online degassing and filtering, casting the liquid aluminum alloy into aluminum alloy cast ingots, adding an Al-5Ti-B wire refining agent in the molten aluminum refining process, wherein a double rotor is adopted for online degassing, the argon flow is 3.2-7.1 m3Per hour, chlorine flow rate is 0-0.05 m3The rotor speed is 400-700 r/min, and the filtering is carried out by adopting a double-layer filter plate;
C. sawing and milling: cutting off the head and the tail of the cast aluminum alloy ingot and milling a surface crust layer;
D. ingot casting and heating: preheating the sawn and milled aluminum alloy ingot in a heating furnace, keeping the preheating temperature at 350 ℃ for 2h, heating the aluminum alloy ingot to 530 +/-10 ℃ for 6h in order to ensure that the heating steps of all the ingots in a furnace area are consistent, and then cooling to 500 ℃ for continuously keeping the temperature for 2-20 h;
E. hot rolling: carrying out hot rolling on the heated and insulated aluminum alloy cast ingot on a roller way of a rolling mill, wherein the thickness of an aluminum alloy coiled material after the hot rolling is 5.0mm, the finish rolling temperature is 330 ℃, and the aluminum alloy coiled material after the hot rolling is naturally cooled to room temperature;
F. cold rolling: the hot-rolled aluminum alloy coiled material is subjected to 2-pass cold rolling on a cold rolling mill to be 1.9mm in thickness and is subjected to intermediate annealing at 320 ℃ for 2 hours, the internal stress caused by hot rolling can be well released by the intermediate annealing, the plate basically reaches a complete recrystallization state, the percentage of cubic texture is greatly reduced, the 0-degree directionality of the finished plate is reduced, and the performances in the directions of 45 degrees and 90 degrees are improved, so that the anisotropy of the finished plate is obviously reduced, the aluminum alloy coiled material is subjected to 2-pass cold rolling on the cold rolling mill to be 1.2mm in thickness after the intermediate annealing, the cold rolling deformation rate of the aluminum alloy coiled material is 37 percent after the intermediate annealing, the low cold rolling deformation is realized, and the over-refining of crystal grains caused by excessive deformation energy storage can;
G. annealing of a finished product: the aluminum alloy finished product thickness coiled material after cold rolling is annealed and insulated for 40s at 480 ℃, passes through a continuous air cushion annealing furnace in a single-layer mode, and is blown to be suspended in the furnace through hot air, the heat exchange efficiency is greatly improved, the plate can be guaranteed to reach the target temperature within 1 minute, the temperature is rapidly increased, deformation energy storage can be rapidly consumed, more crystal grain cores are formed, more uniform finished product tissues are brought, and the annealed aluminum alloy coiled material is cold-rolled to room temperature through an air cushion type air cooling area on a continuous annealing line.
Example 2
Example 2 differs from example 1 in that the thickness of the hot rolled aluminum alloy coil after step E was 4.0 mm.
Example 3
Example 3 differs from example 1 in that the thickness of the hot rolled aluminum alloy coil after step E was 3.0 mm.
Example 4
Example 4 differs from example 1 in that the aluminum alloy coil after step G cold rolling was annealed at 530 ℃ for 40 s.
Example 5
Example 5 differs from example 2 in that the aluminum alloy coil after step G cold rolling was annealed at 530 ℃ for 40 s.
Example 6
Example 6 differs from example 3 in that the aluminum alloy coil after step G cold rolling was annealed at 530 ℃ for 40 s.
Comparative example 1
Comparative example 1 differs from example 1 in that the aluminium alloy coil hot rolled in step F was cold rolled in a rolling mill in 5 passes to a thickness of 1.2mm with a cold rolling deformation of 76%.
Comparative example 2
Comparative example 2 differs from example 2 in that the aluminium alloy coil hot rolled in step F was cold rolled in a rolling mill in 5 passes to a thickness of 1.2mm with a cold rolling deformation of 70%.
Comparative example 3
Comparative example 3 differs from example 3 in that the hot rolled aluminum alloy coil of step F was cold rolled on a rolling mill in 5 passes to a thickness of 1.2mm with a cold rolling deformation of 60%.
Comparative example 4
Comparative example 4 differs from comparative example 1 in that the aluminum alloy coil after step G cold rolling was annealed at 530 ℃ for 40 s.
Comparative example 5
Comparative example 5 differs from comparative example 2 in that the aluminum alloy coil after step G cold rolling was annealed at 530 ℃ for 40 s.
Comparative example 6
Comparative example 6 differs from comparative example 3 in that the aluminum alloy coil after step G cold rolling was annealed at 530 ℃ for 40 s.
The values of n (work hardening index) of the aluminum alloy coils prepared in examples 1 to 3 and comparative examples 1 to 3 are shown in Table 1:
TABLE 1
| Example 1 | Example 2 | Example 3 | Comparative example 1 | Comparative example 2 | Comparative example 3 | |
| Value of n | 0.34 | 0.34 | 0.33 | 0.32 | 0.31 | 0.31 |
The values of n (work hardening index) of the aluminum alloy coils prepared in examples 4 to 6 and comparative examples 4 to 6 are shown in Table 2:
TABLE 2
| Example 4 | Example 5 | Example 6 | Comparative example 4 | Comparative example 5 | Comparative example 6 | |
| Value of n | 0.36 | 0.36 | 0.35 | 0.33 | 0.32 | 0.32 |
As can be seen from the longitudinal correspondence comparison between examples 1 to 3 in Table 1 and examples 4 to 6 in Table 2 and between comparative examples 1 to 3 in Table 1 and comparative examples 4 to 6 in Table 2, the annealing temperature of the aluminum alloy coil after cold rolling is increased, which contributes to the increase of the n value.
As can be seen from the transverse corresponding comparison of examples 1 to 3 in Table 1 and comparative examples 1 to 3 in Table 1 and examples 4 to 6 in Table 2 and comparative examples 4 to 6 in Table 2, the method of adding the intermediate annealing process in the cold rolling deformation process of the aluminum alloy coil is adopted in the examples, and the n value of the finally prepared aluminum alloy coil is obviously higher than that of the method of not adding the intermediate annealing process in the comparative examples.
It is obvious from the comparison between the examples and the comparative examples that the cold rolling process and the intermediate annealing process can achieve a very obvious effect of increasing the n value, because the intermediate annealing process can well eliminate the tissue directionality caused by the large deformation amount of the hot rolling, and the tissue of the finished product can be more uniform. And the product annealing temperature of 530 ℃ is relative to the product annealing temperature of 480 ℃, so that the rolling deformation energy storage of the material can be better released, the nucleation number of crystal grains is obviously reduced, the size of the crystal grains is obviously increased and more uniform, and the n value is improved.
Finally, the above embodiments are only intended to illustrate the technical solutions of the present invention and not to limit the present invention, and although the present invention has been described in detail with reference to the preferred embodiments, it will be understood by those skilled in the art that modifications or equivalent substitutions may be made on the technical solutions of the present invention without departing from the spirit and scope of the technical solutions, and all of them should be covered by the claims of the present invention.
Claims (6)
1. The preparation method of the 5182-O state aluminum alloy plate for the automobile is characterized by comprising the following steps of:
A. preparing materials: the 5182 aluminum alloy raw material is proportioned according to the weight percentage that Si: 0.01-0.08%, Fe: 0.15 to 0.30%, Cu: 0.01-0.1%, Mn: 0.10-0.30%, Mg: 4.5-5.0%, Cr is less than or equal to 0.1%, Zn is less than or equal to 0.05%, Ti is less than or equal to 0.1%, Ni is less than or equal to 0.1%, single impurity is less than or equal to 0.05%, total is less than or equal to 0.15%, and the balance is Al;
B. casting: adding the prepared aluminum alloy raw material into a smelting furnace, uniformly mixing, smelting into liquid aluminum alloy, and performing standing, refining, slagging off, online degassing and filtering to obtain aluminum alloy cast ingot;
C. sawing and milling: cutting off the head and the tail of the cast aluminum alloy ingot and milling a surface crust layer;
D. ingot casting and heating: heating the sawn and milled aluminum alloy cast ingot to 530 +/-10 ℃ and preserving heat for 6 hours, then cooling to 500 ℃ and continuing preserving heat for 2-20 hours;
E. hot rolling: carrying out hot rolling on the heated and heat-preserved aluminum alloy cast ingot on a roller way of a rolling mill, wherein the thickness of an aluminum alloy coiled material after hot rolling is 3.0-5.0 mm, the final rolling temperature is 330 ℃, and the aluminum alloy coiled material after hot rolling is naturally cooled to room temperature;
F. cold rolling: the hot-rolled aluminum alloy coiled material is subjected to 2-pass cold rolling on a cold rolling mill to be 1.9mm in thickness, intermediate annealing is carried out at 320 ℃ for 2 hours, and the intermediate annealed aluminum alloy coiled material is subjected to 2-pass cold rolling on the cold rolling mill to be 1.2mm in thickness;
G. annealing of a finished product: annealing and insulating the cold-rolled aluminum alloy finished product thickness coil for 40s at 480-530 ℃, passing the cold-rolled aluminum alloy finished product thickness coil in a single-layer mode in a continuous air cushion annealing furnace, blowing the aluminum alloy coil in the furnace by hot air for suspension, and cold-rolling the annealed aluminum alloy coil to room temperature in a continuous annealing line through an air cushion type air cooling area.
2. The preparation method of the 5182-O state aluminum alloy plate for the automobile as claimed in claim 1, wherein the 5182 aluminum alloy raw material in the step A is prepared by the following ingredients by weight percentage: si: 0.06%, Fe: 0.179%, Cu: 0.01-0.1%, Mn: 0.10-0.30%, Mg: 4.5-5.0%, Cr is less than or equal to 0.1%, Zn is less than or equal to 0.05%, Ti is less than or equal to 0.1%, Ni is less than or equal to 0.1%, single impurity is less than or equal to 0.05%, total is less than or equal to 0.15%, and the balance is Al.
3. The method for preparing the 5182-O state aluminum alloy plate for the automobile as claimed in claim 2, wherein step B adopts a semi-continuous water cooling casting mode to melt and cast the liquid aluminum alloy into the aluminum alloy ingot.
4. The preparation method of the 5182-O state aluminum alloy plate for the automobile as claimed in claim 3, wherein Al-5Ti-B wire refining agent is added in the refining process of step B, double rotors are adopted for online degassing, and the flow of argon is 3.2-7.1 m3Per hour, chlorine flow rate is 0-0.05 m3And h, the rotating speed of the rotor is 400-700 r/min, and the filtering is performed by adopting a double-layer filter plate.
5. The preparation method of the 5182-O state aluminum alloy plate for the automobile according to claim 4, wherein the aluminum alloy ingot milled in the step D is placed in a heating furnace for preheating, the preheating temperature is 350 ℃, the heat preservation time is 2 hours, then the temperature of the aluminum alloy ingot is increased to 530 +/-10 ℃, the heat preservation time is 6 hours, and then the temperature is reduced to 500 ℃, and the heat preservation time is continued for 2-20 hours.
6. The method for manufacturing an aluminum alloy sheet for an automobile 5182-O temper according to claim 5, wherein the cold rolling deformation rate of the aluminum alloy coil after the intermediate annealing in the step F is 37%.
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| CN114752828A (en) * | 2022-04-08 | 2022-07-15 | 天津忠旺铝业有限公司 | 5-series aluminum alloy plate for upper cover of automobile power battery pack and preparation method thereof |
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