CN113355616A - Heat treatment method for inhibiting Al-Mg-Si-Cu-Mn-Cr aluminum alloy deformation recrystallization and coarse grains - Google Patents
Heat treatment method for inhibiting Al-Mg-Si-Cu-Mn-Cr aluminum alloy deformation recrystallization and coarse grains Download PDFInfo
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Abstract
The invention provides a heat treatment method for inhibiting deformation recrystallization and coarse grains of an Al-Mg-Si-Cu-Mn-Cr aluminum alloy, which is characterized in that an alpha-Al (MnCr) Si phase with high density, micro-nano level and uniform distribution is precipitated from an alloy ingot in the homogenization heat treatment process by carrying out multi-stage homogenization heat treatment on the Al-Mg-Si-Cu-Mn-Cr aluminum alloy; therefore, the appearance of coarse recrystallized grains of the alloy in the deformation process is effectively inhibited, and the common coarse recrystallization problem in the production process of the Al-Mg-Si-Cu-Mn-Cr aluminum alloy is effectively solved. The invention conforms to the development direction of high-strength aluminum alloy and solves the industrial application problem of aluminum alloy for transportation.
Description
Technical Field
The invention relates to the technical field of preparation of aluminum alloy materials, in particular to a heat treatment method for inhibiting Al-Mg-Si-Cu-Mn-Cr aluminum alloy deformation recrystallization and coarse grains.
Background
In order to accelerate the process of energy conservation and emission reduction in the automobile industry, the average fuel consumption of a passenger car is reduced to 5L/100km in 2020 specified in 'passenger car fuel consumption limit' in China, and the fuel consumption of the passenger car is directly influenced by the quality of vehicle preparation, so that the requirement of each vehicle enterprise on the light weight of the vehicle is urgent. The development and application of lightweight materials are the most direct and effective methods for achieving lightweight automobiles. Aluminum alloy is used as a light weight material, can reduce the weight of an automobile by 30-60%, and is widely adopted by domestic and foreign vehicle enterprises, such as fuel vehicles of F150 of Ford, A8 of Audi, XF of Jaguar and the like, electric vehicles of Tesla and the like have high aluminizing rate, and particularly, ES8 of Michelia achieves 96.4% aluminizing rate. According to the forecast that the aluminum quantity for automobiles reaches 190 kg/automobile and the aluminum quantity for new energy automobiles reaches 200 kg/automobile in 2020, the aluminum alloy is increasingly becoming the first choice material for automobile manufacturers to lighten the weight. A 6 xxx-series (Al-Mg-Si-Cu-Mn-Cr) aluminum alloy is a preferred aluminum alloy material for automotive parts because of its excellent formability, workability, and corrosion resistance.
The light weight of the automobile chassis is beneficial to reducing oil consumption and improving the comfort of the whole automobile, and is also related to the driving safety of a driver, so that the chassis parts are required to have good comprehensive properties such as strength, rigidity, fatigue resistance and the like. In order to meet the urgent requirements of various vehicle enterprises on high-performance light parts, alloy materials with higher strength and better comprehensive performance are urgently needed to be developed. 6xxx alloys having international leading levels and being used in large numbers in automobiles have been developed in developed countries. At home, the product performance stability is obviously lower than that of the foreign alloy products, particularly the fatigue performance is poor, and the reason is that coarse recrystallized grains are formed. Applicants have effectively inhibited coarse recrystallization through alloying and manufacturing process control to produce higher performance 6xxx aluminum alloys to meet the requirements of automotive chassis parts.
Homogenization is an essential step in the industrial production of aluminum alloys, and aims to eliminate the segregation of elements in the material, dissolve crystalline phases, improve the formability of the material, and the like. The elimination of microsegregation inside the material is particularly important, and due to the microsegregation of elements inside the material, precipitated phases can be precipitated unevenly. In which the segregation of the alpha-Al (MnCr) Si phase is particularly severe and cannot be eliminated by the conventional single-stage homogenization heat treatment system. Since the precipitation of the alpha-Al (MnCr) Si phase is not uniform, the ability of the material to control dislocations and grain boundary movement is reduced, resulting in a reduction in the ability of the material to inhibit recrystallization, and the generation of many grains with large size differences. Non-uniformity in grain size causes a reduction in the overall strength and toughness of the material, and more importantly, the corrosion and fatigue resistance of the material. For automotive structural members, the two properties are particularly critical for long-term load-bearing service in corrosive environments. The method aims at solving the key industrial problem that the mechanical property of the alloy after deformation is low due to the fact that the existing Al-Mg-Si-Cu-Mn-Cr aluminum alloy is easy to generate coarse recrystallization in the deformation process.
Disclosure of Invention
The invention provides a heat treatment method for inhibiting Al-Mg-Si-Cu-Mn-Cr aluminum alloy deformation recrystallization and coarse grains, which controls alpha-Al (MnCr) Si phase nucleation at a low-temperature stage through a novel multi-stage homogenization heat treatment method so as to enable the alpha-Al (MnCr) Si phase to be uniformly precipitated at high density to obtain a micro-nano grade high-density alpha dispersed phase, and inhibits the recrystallization and coarse grains of the alloy after deformation so as to solve the key technical problem in the industrial production of the Al-Mg-Si-Cu-Mn-Cr aluminum alloy.
In order to achieve the purpose, the invention provides the following technical scheme, and the heat treatment method for inhibiting the deformation recrystallization and the coarse grains of the Al-Mg-Si-Cu-Mn-Cr aluminum alloy is characterized by comprising the following steps of:
step one, carrying out primary homogenization treatment on the ingot in a temperature range of 100-350 ℃, wherein the homogenization time is 2-15 h, and the heating rate of a heat treatment furnace is 0.5-10 ℃/min.
Secondly, carrying out secondary homogenization treatment on the cast ingot, wherein the temperature range is 500-580 ℃, the homogenization time is 2-16 h, and the heating rate is 0.5-10 ℃/min;
and step three, after the second-stage homogenization treatment is finished, rapidly cooling the cast ingot to control the cooling rate of the surface and the core of the cast ingot to be 4-20 ℃/min, and standing at room temperature after cooling is finished.
Furthermore, the alloy comprises the following components in percentage by mass: mg: 0.5% -1.1%, Si: 0.6% -1.4%, Cu: 0.05-0.6%, Mn: 0.2% -0.9%, Fe: < 0.2%, Cr: 0.1 to 0.4 percent; ti is less than or equal to 0.1, Zn is less than or equal to 0.2, and the balance is Al.
Furthermore, in the third step, the ingot is discharged from the furnace for 5s-10min after the homogenization is finished, and then is cooled.
Furthermore, the proportion of the alpha-Al (MnCr) Si phase with the equivalent diameter of more than 180-200 nm in the micro-nano alpha-Al (MnCr) Si phase with the coarse grain inhibition obtained by the heat treatment method is less than or equal to 10%.
Furthermore, the alpha-Al (MnCr) Si phase obtained by the heat treatment method is blocky, the length range is 40-200 nm, the width range is 40-200 nm, the length-width ratio is 1-2, the average equivalent diameter range is 40-200 nm, and the proportion of the blocky alpha-Al (MnCr) Si phase is more than or equal to 60%.
Furthermore, the alpha-Al (MnCr) Si phase obtained by the heat treatment method is acicular or flaky, the length-width ratio is 1-10, the average length range is 40-200 nm, and the proportion of the acicular or flaky alpha-Al (MnCr) Si phase is less than or equal to 30%.
Furthermore, the average distance between the alpha-Al (MnCr) Si phases obtained by the heat treatment method is 100-1000 nm, and the number of unit volumes is 80-1000/mu m-3。
The invention uses a novel homogenization heat treatment process under the control of multistage temperature rise and cooling to obtain a micro-nano-scale alpha disperse phase in an alloy matrix, and effectively controls recrystallization and coarse crystal formation after alloy deformation through the coarse crystal inhibition effect of the disperse phase, thereby obviously improving the grain size uniformity of the material, providing favorable conditions for improving the strength, toughness, corrosion resistance and fatigue resistance of the material, and being particularly critical to the fatigue resistance and corrosion resistance of automobile structural parts in the service process for a long time. The key problem that the material performance is influenced in the production process of the Al-Mg-Si-Cu-Mn-Cr aluminum alloy for the vehicle is solved by a simple heat treatment process, and the method has obvious industrial application value.
Drawings
FIGS. 1(a) and 1(b) are a dark-field optical microscope photograph and a transmission electron microscope photograph of the alpha dispersed phase after multi-stage homogenization in example 1, respectively;
FIG. 2 is a photograph showing the grain structure of the alloy after deformation in the multi-stage homogenization in example 1;
FIGS. 3(a) and 3(b) are dark-field optical microscope photographs and transmission electron microscope photographs of an alpha dispersed phase under the conventional processing conditions in comparative example 1;
FIG. 4 is a photograph of a grain structure of the alloy after deformation under conventional heat treatment conditions in comparative example 1;
FIGS. 5(a) and 5(b) are dark-field optical microscope photograph and transmission electron microscope photograph of alpha dispersed phase after multi-stage homogenization in example 2;
FIG. 6 is a photograph of the deformed grain structure of the alloy after the multi-stage homogenization in example 2;
FIGS. 7(a) and 7(b) are dark-field optical microscope photographs and transmission electron microscope photographs of an alpha dispersed phase under the conventional processing conditions in comparative example 2;
FIG. 8 is a photograph of the grain structure of the alloy after deformation under the conventional heat treatment conditions in comparative example 2.
FIGS. 9(a) and 9(b) are a dark-field optical microscope photograph and a transmission electron microscope photograph of the alpha dispersed phase after the multi-stage homogenization in example 3, respectively;
FIG. 10 is a photograph of the deformed grain structure of the alloy after the multi-stage homogenization in example 3;
FIGS. 11(a) and 11(b) are a dark-field optical microscope photograph and a transmission electron microscope photograph of the alpha dispersed phase after the multi-stage homogenization in comparative example 3, respectively;
FIG. 12 is a photograph of the grain structure of the alloy after deformation under the conventional heat treatment conditions in comparative example 3.
Table 1 shows statistics of the dispersed phases of different heat treatment systems in examples and comparative examples and statistics of recrystallization of alloys after deformation.
Detailed Description
The technical solution of the embodiment of the present invention will be clearly and completely described below with reference to the accompanying drawings of the present invention.
The invention provides a heat treatment method for inhibiting Al-Mg-Si-Cu-Mn-Cr aluminum alloy deformation recrystallization and coarse grains, which effectively controls the size and unit density of an alpha-Al (MnCr) Si phase by a novel multi-stage homogenization heat treatment means, provides a heat treatment method for inhibiting coarse grains in the deformation process of Al-Mg-Si-Cu-Mn-Cr aluminum alloy for transportation, and is respectively specifically described in the following embodiments.
Example 1
In the heat treatment method for inhibiting the deformed coarse grains of the Al-Mg-Si-Cu-Mn-Cr aluminum alloy, the alloy comprises the following components in percentage by mass: mg: 0.5%, Si: 0.6%, Cu: 0.05%, Mn: 0.2%, Fe: < 0.2%, Cr: 0.1 percent; ti is less than or equal to 0.1, Zn is less than or equal to 0.2, and the balance is Al. Example 1 a novel multi-stage homogenization system was used to achieve uniform distribution of micro-nano coarse grain suppressed alpha-al (mncr) Si phases. The multistage homogenization heat treatment method comprises the following steps:
step one, the first-stage homogenization treatment is carried out at the temperature of 100 ℃, the homogenization time is 2 hours, and the heating rate of a heat treatment furnace is 0.5 ℃/min.
And step two, carrying out secondary homogenization treatment on the cast ingot, wherein the homogenization time at the temperature of 500 ℃ for the secondary homogenization is required to be 2h, and the temperature rise rate of the secondary homogenization is 0.5 ℃/min.
And step three, after the second-stage homogenization is finished, cooling the ingot within 5s of discharging, wherein the cooling rate of the ingot is 4 ℃/min, and the ingot is placed at room temperature after cooling.
And (3) extruding and thermally deforming the sample after the homogenization post-treatment is finished, wherein the deformation conditions are as follows: the deformation temperature is 500 ℃, the deformation rate is 0.1s-1And the true strain is 0.8, and the grain structure difference of the samples is compared through EBSD detection after deformation.
The source of the aluminum alloy is not particularly required in the invention, and the aluminum alloy from the source known to those skilled in the art can be adopted. In the embodiment of the invention, the aluminum alloy is specifically an aluminum alloy ingot containing the alloy components prepared by an industrial semi-continuous casting method.
Fig. 1(a) and 1(b) are a dark-field optical microscope photograph and a transmission electron microscope photograph of the α dispersed phase after the multi-stage homogenization in example 1, and fig. 2 is a grain structure of the alloy material after the homogenization heat treatment in example 1 after the extrusion deformation process, from which it can be seen that the grain structure is uniform and the grain recrystallization ratio is small.
Comparative example 1
The alloy in the comparative example 1 has the same components as the alloy in the example 1, and the mass percentages and the total amount are as follows: mg: 0.5%, Si: 0.6%, Cu: 0.05%, Mn: 0.2%, Fe: < 0.2%, Cr: 0.1 percent; ti is less than or equal to 0.1, Zn is less than or equal to 0.2, and the balance is Al.
In comparative example 1, an industrially conventional homogenization system was used to compare the differences in the size and density of the α -Al (MnCr) Si phase under the novel heat treatment process. The process method comprises the following steps:
in comparative example 1, the homogenization heat treatment was carried out at 560 ℃ for 10 hours, the heating rate of the heat treatment furnace was 0.5 ℃/min, after the homogenization was completed, air cooling was carried out after the sample was taken out of the furnace, and the sample was left to stand at room temperature after the cooling was completed.
And (3) extruding and thermally deforming the sample after homogenization, wherein the deformation conditions are as follows: the deformation temperature is 500 ℃, the deformation rate is 0.1s-1And the true strain is 0.8, and the grain structure difference of the samples is compared through EBSD detection after deformation.
The source of the aluminum alloy is not particularly required in the invention, and the aluminum alloy from the source known to those skilled in the art can be adopted. In the comparative example of the invention, the aluminum alloy is prepared by an industrial semi-continuous casting method to obtain an aluminum alloy ingot containing the alloy components.
FIGS. 3(a) and (b) are a dark-field optical microscope photograph and a transmission electron microscope photograph of an alpha dispersed phase under a conventional heat treatment condition in comparative example 1, and FIG. 4 is a grain structure of an alloy material after a conventional homogenization heat treatment in comparative example 1 after a press-deformation process, from which it can be seen that the grain structure is not uniform and the grain recrystallization ratio is high.
Example 2
In the heat treatment method for inhibiting Al-Mg-Si-Cu-Mn-Cr strain recrystallization and macrocrystal provided in example 2, the alloy comprises the following components in percentage by mass and in total: mg: 1.1%, Si: 1.4%, Cu: 0.6%, Mn: 0.9%, Fe: < 0.2%, Cr: 0.4 percent; ti is less than or equal to 0.1, Zn is less than or equal to 0.2, and the balance is Al. Example 2 a novel multi-stage homogenization system was used to achieve uniform distribution of micro-nano coarse grain suppressed alpha-al (mncr) Si phase.
The process of example 2 includes the following steps:
step one, the first-stage homogenization treatment is carried out at the temperature of 350 ℃, the homogenization time is 15h, and the heating rate of a heat treatment furnace is 10 ℃/min.
And step two, carrying out secondary homogenization treatment on the cast ingot, wherein the homogenization time of the secondary homogenization temperature is required to be 16h at 580 ℃, and the temperature rise rate of the secondary homogenization is 10 ℃/min.
And step three, after the second-stage homogenization is finished, cooling the ingot within 10min of discharging, wherein the cooling rate of the ingot is 20 ℃/min, and the ingot is placed at room temperature after cooling.
And (3) extruding and thermally deforming the sample after the homogenization post-treatment is finished, wherein the deformation conditions are as follows: the deformation temperature is 500 ℃, the deformation rate is 0.1s-1And the true strain is 0.8, and the grain structure difference of the samples is compared through EBSD detection after deformation.
The source of the aluminum alloy is not particularly required in the invention, and the aluminum alloy from the source known to those skilled in the art can be adopted. In the embodiment of the invention, the aluminum alloy is specifically an aluminum alloy ingot containing the alloy components prepared by an industrial semi-continuous casting method.
Fig. 5(a) and 5(b) are dark field optical microscope photographs and transmission electron microscope photographs of the α dispersed phase after the multi-stage homogenization in example 2. FIG. 6 shows the grain structure of the alloy material after the homogenization heat treatment in example 2 after the extrusion deformation process, which is commonly used in industrial production, showing that the grain structure is uniform and the recrystallization rate of the grains is small.
Comparative example 2
The alloy in the comparative example 2 has the same components as the alloy in the example 2, and the mass percentages and the total amount are as follows: mg: 1.1%, Si: 1.4%, Cu: 0.6%, Mn: 0.9%, Fe: < 0.2%, Cr: 0.4 percent; ti is less than or equal to 0.1, Zn is less than or equal to 0.2, and the balance is Al.
In comparative example 2, an industrially conventional homogenization system was used to compare the differences in the size and density of the α -Al (MnCr) Si phase under the novel heat treatment process. The process of comparative example 2 comprises the following steps:
in comparative example 2, the homogenization heat treatment was carried out at 560 ℃ for 10 hours, the heating rate of the heat treatment furnace was 3 ℃/min, and after the homogenization was completed, water cooling was carried out after the sample was taken out of the furnace, and the sample was left to stand at room temperature after the cooling was completed.
And (3) extruding and thermally deforming the sample after homogenization, wherein the deformation conditions are as follows: the deformation temperature is 500 ℃, the deformation rate is 0.1s < -1 >, the true strain is 0.8, and the grain structure difference of the sample is compared through EBSD detection after deformation.
The source of the aluminum alloy is not particularly required in the invention, and the aluminum alloy from the source known to those skilled in the art can be adopted. In the embodiment of the invention, the aluminum alloy is specifically an aluminum alloy ingot containing the alloy components prepared by an industrial semi-continuous casting method.
Fig. 7(a) and 7(b) are a dark field optical microscope photograph and a transmission electron microscope photograph of an α dispersed phase under a conventional homogenization heat treatment condition. FIG. 8 shows the grain structure of the alloy material after the conventional homogenization heat treatment and after the extrusion deformation process commonly used in industrial production, the grain structure is not uniform, and the proportion of recrystallized grains is high.
Example 3
In the heat treatment method for suppressing Al-Mg-Si-Cu-Mn-Cr strain recrystallization and macrocrystal provided in example 3, the alloy comprises the following components in percentage by mass and in total: mg: 0.8%, Si: 1.0%, Cu: 0.3%, Mn: 0.5%, Fe: < 0.2%, Cr: 0.25 percent; ti is less than or equal to 0.1, Zn is less than or equal to 0.2, and the balance is Al. Example 3 a novel multi-stage homogenization system was used to achieve uniform distribution of micro-nano coarse grain suppressed alpha-al (mncr) Si phase.
The process of example 3 includes the following steps:
step one, the first-stage homogenization treatment is carried out at the temperature of 250 ℃, the homogenization time is 7h, and the temperature rise rate of a heat treatment furnace is 5 ℃/min.
And step two, carrying out secondary homogenization treatment on the cast ingot, wherein the homogenization time of the secondary homogenization temperature is required to be 8h at 540 ℃, and the temperature rise rate of the secondary homogenization is 5 ℃/min.
And step three, after the second-stage homogenization is finished, cooling the ingot within 5min of discharging, wherein the cooling rate of the ingot is 12 ℃/min, and the ingot is placed at room temperature after cooling.
And (3) extruding and thermally deforming the sample after the homogenization post-treatment is finished, wherein the deformation conditions are as follows: the deformation temperature is 500 ℃, the deformation rate is 0.1s < -1 >, the true strain is 0.8, and the grain structure difference of the sample is compared through EBSD detection after deformation.
The source of the aluminum alloy is not particularly required in the invention, and the aluminum alloy from the source known to those skilled in the art can be adopted. In the embodiment of the invention, the aluminum alloy is specifically an aluminum alloy ingot containing the alloy components prepared by an industrial semi-continuous casting method.
Fig. 9(a) and 9(b) are dark field optical microscope photographs and transmission electron microscope photographs of the α dispersed phase after the multi-stage homogenization in example 3. FIG. 10 is a graph showing the grain structure of the alloy material after the homogenization heat treatment in example 3 after the extrusion deformation process, which is commonly used in industrial production, showing that the grain structure is uniform and the recrystallization rate of the grains is small.
Comparative example 3
The alloy in the comparative example 3 has the same components as those in the example 3, and the mass percentages and the total amount are as follows: mg: 0.8%, Si: 1.0%, Cu: 0.3%, Mn: 0.5%, Fe: < 0.2%, Cr: 0.25 percent; ti is less than or equal to 0.1, Zn is less than or equal to 0.2, and the balance is Al.
In comparative example 3, an industrially conventional homogenization system was used to compare the differences in the size and density of the α -Al (MnCr) Si phase under the novel heat treatment process. The process of comparative example 2 comprises the following steps:
in comparative example 3, the homogenization heat treatment was carried out at 540 ℃ for 10 hours, the heating rate of the heat treatment furnace was 5 ℃/min, and after the homogenization was completed, the sample was cooled in air after being taken out of the furnace, and the sample was left to stand at room temperature after being cooled.
And (3) extruding and thermally deforming the sample after homogenization, wherein the deformation conditions are as follows: the deformation temperature is 500 ℃, the deformation rate is 0.1s < -1 >, the true strain is 0.8, and the grain structure difference of the sample is compared through EBSD detection after deformation.
The source of the aluminum alloy is not particularly required in the invention, and the aluminum alloy from the source known to those skilled in the art can be adopted. In the embodiment of the invention, the aluminum alloy is specifically an aluminum alloy ingot containing the alloy components prepared by an industrial semi-continuous casting method.
Fig. 11(a) and 11(b) are a dark field optical microscope photograph and a transmission electron microscope photograph of an α dispersed phase under a conventional homogenization heat treatment condition. FIG. 12 shows the grain structure of the alloy material after the conventional homogenization heat treatment and after the extrusion deformation process commonly used in industrial production, it can be seen that the grain structure is not uniform and the proportion of recrystallized grains is high.
Table 1 shows the precipitation comparison of the dispersed phase and the recrystallization fraction of the strain in examples 1, 2, 3 and comparative examples 1, 2, 3. Compared with the results of the comparative examples 1, 2 and 3, the novel homogenization heat treatment process flow under the control of multi-stage heating and cooling provided by the invention obviously improves the precipitation distribution and size of the alpha-Al (MnCr) Si dispersed phase, and the precipitation size of the alpha-Al (MnCr) Si dispersed phase is smaller, the precipitation number density is higher, the number of blocky dispersed phases is more, so that the recrystallization behavior of the later deformation of the alloy is effectively inhibited, the generation of coarse crystals is reduced, and the important technical problem in the Al-Mg-Si-Cu-Mn-Cr alloy industry is effectively solved.
The technical contents and technical features of the present invention have been provided as above, however, those skilled in the art may still make various substitutions and modifications based on the teaching and disclosure of the present invention without departing from the spirit of the present invention, therefore, the scope of the present invention should not be limited to the disclosure of the embodiments, but should include various substitutions and modifications without departing from the present invention, and are covered by the claims of the present patent application.
TABLE 1 statistical data of alpha-disperse phase and recrystallized grain ratio in examples and comparative examples
Claims (7)
1. A heat treatment method for inhibiting the deformation recrystallization and coarse grains of Al-Mg-Si-Cu-Mn-Cr aluminum alloy is characterized by comprising the following steps:
step one, carrying out primary homogenization treatment on the ingot in a temperature range of 100-350 ℃, wherein the homogenization time is 2-15 h, and the heating rate of a heat treatment furnace is 0.5-10 ℃/min.
Secondly, carrying out secondary homogenization treatment on the cast ingot, wherein the temperature range is 500-580 ℃, the homogenization time is 2-16 h, and the heating rate is 0.5-10 ℃/min;
and step three, after the second-stage homogenization treatment is finished, rapidly cooling the cast ingot to control the cooling rate of the surface and the core of the cast ingot to be 4-20 ℃/min, and standing at room temperature after cooling is finished.
2. The heat treatment method for suppressing wrought macrocrystals of an Al-Mg-Si-Cu-Mn-Cr aluminum alloy according to claim 1, wherein: the alloy comprises the following components in percentage by mass: mg: 0.5% -1.1%, Si: 0.6% -1.4%, Cu: 0.05-0.6%, Mn: 0.2% -0.9%, Fe: < 0.2%, Cr: 0.1 to 0.4 percent; ti is less than or equal to 0.1, Zn is less than or equal to 0.2, and the balance is Al.
3. The heat treatment method for suppressing wrought macrocrystals of an Al-Mg-Si-Cu-Mn-Cr aluminum alloy according to claim 1, wherein: and in the third step, the rapid cooling is carried out within 5s-10min after the ingot is discharged from the furnace.
4. The heat treatment method for suppressing wrought macrocrystals of an Al-Mg-Si-Cu-Mn-Cr aluminum alloy according to claim 1, wherein: the proportion of the alpha-Al (MnCr) Si phase with the equivalent diameter of more than 180-200 nm in the micro-nano alpha-Al (MnCr) Si phase for inhibiting coarse grains obtained by the heat treatment method is less than or equal to 10%.
5. The heat treatment method for suppressing wrought macrocrystals of an Al-Mg-Si-Cu-Mn-Cr aluminum alloy according to claim 1, wherein: the alpha-Al (MnCr) Si phase obtained by the heat treatment method is blocky, the length range is 40-200 nm, the width range is 40-200 nm, the length-width ratio is 1-2, the average equivalent diameter range is 40-200 nm, and the ratio of the blocky alpha-Al (MnCr) Si phase is more than or equal to 60%.
6. The heat treatment method for suppressing wrought macrocrystals of an Al-Mg-Si-Cu-Mn-Cr aluminum alloy according to claim 1, wherein: the alpha-Al (MnCr) Si phase obtained by the heat treatment method is acicular or flaky, the length-width ratio is 1-10, the average length range is 40-200 nm, and the proportion of the acicular or flaky alpha-Al (MnCr) Si phase is less than or equal to 30%.
7. The heat treatment method for suppressing wrought macrocrystals of an Al-Mg-Si-Cu-Mn-Cr aluminum alloy according to claim 1, wherein: the average distance between alpha-Al (MnCr) Si phases obtained by the heat treatment method is 100-1000 nm, and the number of unit volumes is 80-1000 mu m-3。
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