Novel solid solution heating-step quenching process for high-magnesium-content aluminum alloy

Abstract

The invention discloses a novel high-magnesium-content aluminum alloy solid solution heating-step quenching process which comprises the following steps: (1) preparing a novel high-magnesium-content aluminum alloy thermal deformation processing material in a rolling or extruding manner, and carrying out solid solution heating and heat preservation treatment at 460-545 DEG C / 30-150 min; (2) an air cooling mode is adopted for carrying out first-stage quenching on the thermal deformation machining material subjected to solid solution heating, the thermal deformation machining material is cooled to 420-450 DEG C, the cooling speed is 2-8 DEG C / s, and the transfer time from solid solution to first-stage quenching does not exceed 15 s; (3) carrying out second-stage quenching on the thermal deformation processing material after the first-stage quenching is finished, and cooling to 180-230 DEG C at the cooling speed of 40-75 DEG C / s; (4) carrying out third-stage quenching on the thermal deformation processing material after the second-stage quenching is finished, and cooling to 30-50 DEG C at the cooling speed of 2-8 DEG C / s; and (5) pre-deformation and aging treatment are conducted on the machined material subjected to step quenching. According to the solid solution heating-step quenching process disclosed by the invention, the quenching cracking risk of the processed material can be obviously reduced.

Description

Technical Field

[0001] This invention relates to the quenching process of aluminum alloy materials, specifically to a novel solution heating-stage quenching process for high magnesium content aluminum alloys. Background Technology

[0002] Aluminum alloys, with their advantages of light weight, high specific strength, ease of processing, low cost, and high recyclability, are widely used in aerospace, transportation, and other fields. To meet the future development needs of high-end equipment in various fields, key components must shift towards lightweight, high-performance, and low-cost designs. Therefore, further research and development of new aluminum alloys with excellent comprehensive performance is necessary.

[0003] Typical high-strength and high-toughness aluminum alloys, represented by aluminum-zinc-magnesium (copper) alloys, have a specific strength of up to 150 MPa / g·cm. 3 The overall performance is well-matched, but the high zinc content increases density, which is not conducive to lightweight requirements. Among all commercially available wrought aluminum alloys, magnesium content is the highest and density is the lowest, with density decreasing by nearly 0.4% for every 1 wt.% increase in magnesium content. Therefore, by reducing the zinc content and increasing the magnesium content in aluminum-zinc-magnesium (copper) alloys, a new high-magnesium-content aluminum-magnesium-zinc alloy system is formed, achieving a reduction in alloy density while maintaining essentially unchanged overall performance. Unlike aluminum-zinc-magnesium (copper) alloys, its main precipitated strengthening phase is TMg. 32 (Al,Zn) 49 It is a precipitate phase, not an η-MgZn2 precipitate phase.

[0004] Similar to aluminum-zinc-magnesium (copper) alloys, the new high-magnesium-content aluminum-magnesium-zinc alloy system is also a highly alloyed alloy. During solution quenching, on the one hand, when the quenching cooling rate is too fast, the alloy material is prone to quenching cracks, and residual stress is inevitably introduced during quenching. The faster the quenching cooling rate, the greater the residual stress, affecting the subsequent machining accuracy of the material. On the other hand, when the quenching cooling rate is reduced, large-sized T-phase phases will precipitate during quenching, affecting the overall properties of the alloy material, such as strength and corrosion resistance. Summary of the Invention

[0005] The purpose of this invention is to provide a novel solution heating-stage quenching process for high magnesium content aluminum alloys, which prevents quenching cracks in the aluminum alloy processed material and reduces the size of the precipitated phases and residual quenching stress.

[0006] To achieve the above objectives, the present invention adopts the following technical solution: A novel solution heating-stage quenching process for a high-magnesium-content aluminum alloy, wherein the aluminum alloy is composed of the following components: Mg 6.0~9.9wt%, Zn 1.1~3.01wt%, Si 0.1~1.15wt%, and at least one of Mn, Cu, Zr, Sc, and Ti with a total content not exceeding 0.8wt%, the remainder being Al and unavoidable impurities; the process includes the following steps: (1) The novel high-magnesium aluminum alloy hot-deformed material is prepared by rolling or extrusion and subjected to solution heating and heat preservation treatment at 460~545℃ / 30~150min; (2) The heat-deformed material heated by solution cooling is subjected to first-stage quenching by air cooling, and the temperature is cooled to 420~450℃. The cooling rate is 2~8℃ / s, and the transfer time from solution cooling to first-stage quenching does not exceed 15s. (3) Perform a second quenching on the hot-deformed material after the first quenching, and cool it to 180~230℃ at a rate of 40~75℃ / s; (4) After the second-stage quenching, the hot-deformed material is subjected to a third-stage quenching and cooled to 30~50℃ at a rate of 2~8℃ / s. (5) The processed material after graded quenching is subjected to pre-deformation and aging treatment.

[0007] Preferably, the aluminum alloy is composed of the following components: Mg 6.3~9.9wt%, Zn 1.1~2.9wt%, Si 0.15~1.0wt%, and at least one of Mn, Cu, Zr, Sc and Ti elements with a total content not exceeding 0.6wt%, with the remainder being Al and unavoidable impurities.

[0008] Preferably, in step (1), the heat preservation temperature of the solution heating is 485~535℃, the heat preservation time is 60~120min, and the heating rate of the heat-deformed material from room temperature to solution temperature is 15~20℃ / h.

[0009] Preferably, in step (2), during the first-stage quenching process, the final cooling temperature of the hot-deformed material is 430~440℃, the wind speed is 40~60m / s, the nozzle height is 50~80mm, and the angle between the nozzle and the horizontal plane of the hot-deformed material is 30~45°.

[0010] Preferably, in step (3), during the second-stage quenching process, the final cooling temperature of the hot-deformed material is 190~210℃, the quenching medium pressure is 4~7 bar both above and below, the quenching medium temperature is 20~30℃, the nozzle height is 50~80mm, and the angle between the nozzle and the horizontal plane of the hot-deformed material is 30~40°.

[0011] Preferably, in step (4), during the third-stage quenching process, the final cooling temperature of the hot-deformed material is 30~40℃, the wind speed is 40~60m / s, the nozzle height is 50~80mm, and the angle between the nozzle and the horizontal plane of the hot-deformed material is 30~45°.

[0012] Preferably, in step (3), during the second-stage quenching process, the quenching medium is a water-based quenching liquid, which, by mass, includes: 10% polyethylene glycol, 10% butyl acrylate, 2% styrene, 3% acrylic acid, 5% isododecyl alcohol, 0.3% preservative, 0.1% defoamer, 0.5% antioxidant, and the balance is water; the preservative is nitrite, the defoamer is polyether-modified silicone, and the antioxidant is tert-butylhydroquinone.

[0013] Preferably, in step (5), the pre-deformation amount of the hot-deformed material is 2~4.5%, the deformation rate is 0.5~1.0 mm / min, the pressure holding time is 50~100s, and the time interval between graded quenching and pre-deformation does not exceed 5h.

[0014] Preferably, in step (5), the aging treatment of the heat-deformed material is a two-stage artificial aging process. The first stage is an aging treatment at 60~105℃ for 12~48h, and the second stage is an aging treatment at 135~190℃ for 1~24h. The time interval between the pre-deformation and the two-stage artificial aging treatment is 5~60 days.

[0015] Preferably, in step (4), after the third-stage quenching is completed, the hot-deformed material does not experience quenching cracking, and the size of the AlZnMg desolventized precipitate in the alloy matrix does not exceed 350 nm.

[0016] A novel high-magnesium-content aluminum alloy processed material, prepared by the aforementioned process, exhibits a quenching residual stress that is reduced by more than 50 MPa compared to that obtained by direct single-stage spray quenching.

[0017] The beneficial effects of this invention are: This invention provides a solution heating-stage quenching process for a novel high-magnesium-content aluminum alloy, which can significantly reduce the risk of quenching cracking in the processed material, ensuring that the size of the AlZnMg desolventized precipitates in the alloy matrix does not exceed 350 nm and the quenching residual stress does not exceed 160 MPa. Attached Figure Description

[0018] Figure 1 This is a schematic diagram of temperature control in the solution heating-stage quenching process of the novel high-magnesium content aluminum alloy of the present invention. Detailed Implementation

[0019] This invention employs a multi-element alloying composition ratio to develop a novel high-magnesium-content aluminum alloy by reducing zinc and increasing magnesium content in aluminum-zinc-magnesium (copper) alloys. Compared with aluminum-zinc-magnesium (copper) alloys, this alloy exhibits significantly lower density while maintaining comparable overall performance, and its main precipitated strengthening phase is TMg. 32 (Al,Zn) 49 Precipitated phases. For this novel high-magnesium-content aluminum alloy, an innovative method of low heating rate and high solution holding temperature is employed for solution heating. This ensures that the matrix is ​​dissolved before the overheating temperature of the second phase in the alloy is reached during the heating process. During the solution holding process, the alloy matrix forming a supersaturated solid solution does not overheat. A method combining precise control of staged quenching with a special quenching medium is used to prevent quenching cracking in the alloy, significantly reducing the size of precipitated phases and residual quenching stress.

[0020] The novel high-magnesium aluminum alloy described in this invention is composed of the following components: Mg 6.0~9.9wt%, Zn 1.1~3.01wt%, Si 0.1~1.15wt%, and at least one of Mn, Cu, Zr, Sc and Ti elements with a total content not exceeding 0.8wt%, with the remainder being Al and unavoidable impurities.

[0021] Further preferred, the novel high-magnesium content aluminum alloy is composed of the following components: Mg 6.3~9.9wt%, Zn 1.1~2.9wt%, Si 0.15~1.0wt%, Mn≤0.1wt%, Cu≤0.1wt%, Zr≤0.15wt%, Sc≤0.1wt%, Ti≤0.1wt%, with the remainder being Al and unavoidable impurities.

[0022] like Figure 1 As shown, the novel solution heating-stage quenching process for high-magnesium-content aluminum alloys provided by this invention sequentially involves slow heating, solution treatment, first-stage quenching, second-stage quenching, third-stage quenching, pre-deformation, and aging treatment. Specifically, it includes the following steps: (1) Solution insulation Any hot-deformed material prepared by rolling or extrusion of a new high-magnesium aluminum alloy is subjected to solution heating and holding treatment at 460~545℃ for 30~150min, with the heating rate of the hot-deformed material from room temperature to solution temperature being 15~20℃ / h.

[0023] Further preferred, the solution heating temperature of the novel high magnesium content aluminum alloy hot-deformed material in step (1) is 485~535℃, the holding time is 60~120min, and the heating rate of the hot-deformed material from room temperature to solution temperature is 15~20℃ / h.

[0024] (2) First stage quenching The heat-deformed material heated by solution treatment is cooled from 460~545℃ to 420~450℃ using air cooling. The first-stage quenching transfer time from solution treatment to air cooling does not exceed 15s.

[0025] Further optimization, in step (2) during the first stage of quenching, the final cooling temperature of the hot-deformed material is 430~440℃, the wind speed is 40~60m / s, the nozzle height is 50~80mm, the angle between the nozzle and the horizontal plane of the hot-deformed material is 30~45°, and the cooling rate is 2~8℃ / s.

[0026] (3) Second-stage quenching Spray cooling is used to cool the hot-deformed material after the first stage of quenching from 420~450℃ to 180~230℃.

[0027] Further optimization: In step (3), during the second-stage quenching process, the final cooling temperature of the hot-deformed material is 190~210℃, the quenching medium pressure is 4~7 bar both above and below, the quenching medium temperature is 20~30℃, the nozzle height is 50~80mm, the angle between the nozzle and the horizontal plane of the hot-deformed material is 30~40°, and the cooling rate is 40~75℃ / s. The quenching medium is a water-based quenching liquid, which, by mass, includes: 10% polydiol, 10% butyl acrylate, 2% styrene, 3% acrylic acid, 5% isododecyl alcohol, 0.3% preservative, 0.1% defoamer, 0.5% antioxidant, and the balance is water; the preservative is nitrite, the defoamer is polyether-modified silicone, and the antioxidant is tert-butylhydroquinone.

[0028] (4) Third-stage quenching Air cooling is used to cool the hot-deformed material after the second-stage quenching from 180~230℃ to 30~50℃.

[0029] Further preferred, in the third-stage quenching process described in step (4), the final cooling temperature of the hot-deformed material is 30~40℃, the wind speed is 40~60m / s, the nozzle height is 50~80mm, the angle between the nozzle and the horizontal plane of the hot-deformed material is 30~45°, and the cooling rate is 2~8℃ / s.

[0030] (5) Pre-deformation and aging treatment The processed material after graded quenching undergoes pre-deformation and aging treatment. The pre-deformation amount is 2-4.5%, the deformation rate is 0.5-1.0 mm / min, and the holding pressure is maintained for 50-100 seconds. The time interval between graded quenching and pre-deformation should not exceed 5 hours. The aging treatment is a two-stage artificial aging process. The first stage is carried out at 60-105℃ for 12-48 hours, and the second stage is carried out at 135-190℃ for 1-24 hours. The time interval between pre-deformation and the two-stage artificial aging treatment is 5-60 days.

[0031] The following embodiments and accompanying drawings are used to describe in detail the implementation of the present invention, so that the process of how the present invention uses technical means to solve technical problems and achieve technical effects can be fully understood and implemented accordingly.

[0032] Example 1 This embodiment provides a novel solution heating-stage quenching process for high-magnesium-content aluminum alloys, implemented through the following steps: (1) The new high magnesium content aluminum alloy is a hot-rolled plate with a thickness of 50 mm. The alloy mass ratio is 7.5wt%Mg, 2.9wt%Zn, 0.2wt%Si, Mn≤0.1%, Cu≤0.1%, Zr≤0.15%, Sc≤0.1%, Ti≤0.1%, and the remainder is Al and unavoidable impurities.

[0033] (2) The new high magnesium content aluminum alloy rolled plate in step (1) is subjected to solution heat preservation treatment. The solution heating temperature is 520℃, the heat preservation time is within the range of 90~120min, and the heating rate of the hot rolled plate from room temperature to solution temperature is within the range of 15~20℃ / h.

[0034] (3) The hot-rolled plate heated by solution heating in step (2) is cooled from 510℃ to 430℃ by air cooling. The wind speed is 50m / s, the nozzle height is 70mm, the angle between the nozzle and the horizontal plane of the hot-rolled plate is 45°, and the cooling rate is controlled within the range of 4~6.5℃ / s.

[0035] (4) The hot-rolled plate after the first-stage quenching in step (3) is cooled to 190°C by spray cooling. The quenching medium pressure is 5 bar at both the top and bottom, the quenching medium temperature is 30°C, the nozzle height is 70 mm, the angle between the nozzle and the horizontal plane of the hot-rolled plate is 30°, and the cooling rate is within the range of 65~70°C / s. The quenching medium is a water-based quenching liquid, which, by mass, includes: 10% polyethylene glycol, 10% butyl acrylate, 2% styrene, 3% acrylic acid, 5% isododecyl alcohol, 0.3% preservative, 0.1% defoamer, 0.5% antioxidant, and the balance is water; the preservative is nitrite, the defoamer is polyether modified silicone, and the antioxidant is tert-butylhydroquinone.

[0036] (5) The hot-rolled plate after the second-stage quenching in step (4) is cooled from 190°C to 30°C by air cooling. The air speed is 50m / s, the nozzle height is 70mm, the angle between the nozzle and the horizontal plane of the hot-rolled plate is 45°, and the cooling rate is in the range of 2.5~4°C / s.

[0037] (6) The hot-rolled sheet after the graded quenching in step (5) is subjected to pre-deformation and aging treatment. The pre-deformation amount is in the range of 3.2% to 4.0%, the deformation rate is 1.0 mm / min, the holding pressure is in the range of 50 to 100 s, and the time interval between graded quenching and pre-deformation does not exceed 5 hours. The aging treatment is a two-stage artificial aging treatment. The first stage is an aging treatment at 105℃ for 36 hours, and the second stage is an aging treatment at 175℃ for 12 hours. The time interval between pre-deformation and the two-stage artificial aging treatment is 14 days.

[0038] Tests and analyses were conducted on the hot-rolled plates after graded quenching. No quenching cracks were observed. The size of the AlZnMg desolventized precipitates in the alloy matrix was approximately 150 nm, and the average value of the residual stress after surface quenching was 137.3 MPa.

[0039] Example 2 This embodiment provides a novel solution heating-stage quenching process for high-magnesium-content aluminum alloys, implemented through the following steps: (1) A novel high-magnesium-content aluminum alloy "T" profile with a cross-sectional area of ​​8500 mm² was prepared. 2 The alloy composition is as follows: 7.0wt%Mg, 2.0wt%Zn, 0.15wt%Si, Mn≤0.1%, Cu≤0.1%, Zr≤0.15%, Sc≤0.1%, Ti≤0.1%, with the remainder being Al and unavoidable impurities.

[0040] (2) The new high magnesium content aluminum alloy extruded profile in step (1) is subjected to solution heat preservation treatment. The solution heating temperature is 530℃, the heat preservation time is in the range of 60~90min, and the heating rate of the extruded profile from room temperature to solution temperature is in the range of 15~17℃ / h.

[0041] (3) The extruded profile heated by solution in step (2) is cooled from 530°C to 435°C by air cooling. The air speed is 50m / s, the nozzle height is 70mm, the angle between the nozzle and the horizontal plane of the extruded profile is 45°, and the cooling rate is within the range of 3.5~6°C / s.

[0042] (4) The extruded profile after the first stage of quenching in step (3) is cooled to 190°C by spray cooling. The quenching medium pressure is 5 bar at both the top and bottom, the quenching medium temperature is 30°C, the nozzle height is 50 mm, the angle between the nozzle and the horizontal plane of the extruded profile is 30°, and the cooling rate is within the range of 65~75°C / s. The quenching medium is a water-based quenching liquid, which, by mass, includes: 10% polyethylene glycol, 10% butyl acrylate, 2% styrene, 3% acrylic acid, 5% isododecyl alcohol, 0.3% preservative, 0.1% defoamer, 0.5% antioxidant, and the balance is water; the preservative is nitrite, the defoamer is polyether modified silicone, and the antioxidant is tert-butylhydroquinone.

[0043] (5) The extruded profile after the second-stage quenching in step (4) is cooled from 190°C to 30°C by air cooling. The air speed is 50m / s, the nozzle height is 70mm, the angle between the nozzle and the horizontal plane of the extruded profile is 45°, and the cooling rate is in the range of 2.3~5°C / s.

[0044] (6) The extruded profile after graded quenching in step (5) is subjected to pre-deformation and aging treatment. The pre-deformation amount is 2.0%, the deformation rate is 1.0 mm / min, and the holding pressure is within the range of 50~100s. The time interval between graded quenching and pre-deformation is no more than 5 hours. The aging treatment is a two-stage artificial aging treatment. The first stage is an aging treatment at 70℃ for 18 hours, and the second stage is an aging treatment at 150℃ for 24 hours. The time interval between pre-deformation and the two-stage artificial aging treatment is 30 days.

[0045] Tests and analyses were conducted on the extruded profiles after graded quenching. No quenching cracks were observed. The size of the AlZnMg desolventized precipitates in the alloy matrix was approximately 110 nm, and the average value of the residual stress after surface quenching was 156.4 MPa.

[0046] Comparative Example 1 The difference between this comparative example and Example 1 is that the novel high-magnesium content aluminum alloy prepared in step (1) is a 50mm thick hot-rolled sheet with the following alloy mass ratios: Mg 9.5wt%, Zn 3.5wt%, Si 0.5wt%, Mn≤0.1wt%, Cu≤0.1wt%, Zr≤0.15wt%, Sc≤0.1wt%, Ti≤0.1wt%, and the remainder being Al and unavoidable impurities. The other steps are the same as in Example 1. The hot-rolled sheet after staged quenching was tested and analyzed. Through-cracks appeared after quenching, and the size of the AlZnMg precipitates in the alloy matrix was approximately 470nm. The average residual stress of the surface after quenching was 104.9MPa.

[0047] Comparative Example 2 The difference between this comparative example and Example 1 is that in step (2), the solution treatment is carried out by the method of "warming up to the sample", that is, the temperature is first raised to 520°C, and the hot-rolled thick plate is directly put into the heat treatment equipment for solution treatment. The other steps are the same as those in Example 1.

[0048] Tests and analyses were conducted on the hot-rolled plates after graded quenching. Overheating was observed in the alloy plates, but no quenching cracks were found. The size of the AlZnMg desolventized precipitates in the alloy matrix was approximately 155 nm, and the average value of the residual stress after surface quenching was 141.1 MPa.

[0049] Comparative Example 3 The difference between this comparative example and Example 1 is that in step (2), the solution heating temperature is reduced to 455°C, while the other steps are the same as in Example 1.

[0050] Tests and analyses were conducted on the hot-rolled plates after graded quenching. No quenching cracks were observed. The size of the AlZnMg desolventized precipitates in the alloy matrix was approximately 150 nm, and the average value of the residual stress after surface quenching was 179.2 MPa.

[0051] Comparative Example 4 The difference between this comparative example and Example 1 is that the method of solution treatment and heat preservation followed by direct spray quenching is used instead of the staged quenching in steps (3), (4), and (5). The other steps are the same as those in Example 1.

[0052] Tests and analyses were conducted on the hot-rolled plates after graded quenching. No quenching cracks were observed. The size of the AlZnMg desolventized precipitates in the alloy matrix was approximately 95 nm, and the average value of the residual stress after surface quenching was 253.6 MPa.

[0053] Comparative Example 5 The difference between this comparative example and Example 1 is that in step (4), the hot-rolled sheet after the first-stage quenching in step (3) is cooled to 120°C, while the other steps are the same as in Example 1. The hot-rolled sheet after staged quenching was tested and analyzed, and no quenching cracks were observed. The size of the AlZnMg desolventized precipitate in the alloy matrix was about 95 nm, and the average value of the surface quenching residual stress was 233.1 MPa.

[0054] Comparative Example 6 The difference between this comparative example and Example 1 is that in step (4), the hot-rolled plate after the first-stage quenching in step (3) is cooled to 270°C, while the other steps are the same as in Example 1.

[0055] Tests and analyses were conducted on the hot-rolled plates after graded quenching. No quenching cracks were observed. The size of the AlZnMg desolventized precipitates in the alloy matrix was approximately 280 nm, and the average value of the residual stress after surface quenching was 175.7 MPa.

[0056] Comparative Example 7 The difference between this comparative example and Example 1 is that in step (4), deionized water is used instead of quenching medium for quenching, while the other steps are the same as in Example 1.

[0057] Tests and analyses were conducted on the hot-rolled plates after graded quenching. No quenching cracks were observed. The size of the AlZnMg desolventized precipitates in the alloy matrix was approximately 140 nm, and the average value of the residual stress after surface quenching was 184.3 MPa.

[0058] Comparative Example 8 The difference between this comparative example and Example 1 is that in step (4), the pressure is controlled to reduce the second-stage quenching cooling rate to the range of 30~35℃ / s, while the other steps are the same as in Example 1.

[0059] Tests and analyses were conducted on the hot-rolled plates after graded quenching. No quenching cracks were observed. The size of the AlZnMg desolventized precipitates in the alloy matrix was approximately 510 nm, and the average value of the residual stress after surface quenching was 135.9 MPa.

[0060] The above description is merely a preferred embodiment of the present invention and is not intended to limit the invention in any other way. Any person skilled in the art may make changes or modifications to the above-disclosed technical content to create equivalent embodiments. However, any simple modifications, equivalent changes, and modifications made to the above embodiments based on the technical essence of the present invention without departing from the scope of the present invention shall still fall within the protection scope of the present invention.

Claims

1. A novel solution heating-stage quenching process for high-magnesium-content aluminum alloys, characterized in that, The aluminum alloy is composed of the following components: Mg 6.0~9.9wt%, Zn 1.1~3.01wt%, Si 0.1~1.15wt%, and at least one of Mn, Cu, Zr, Sc, and Ti elements with a total content not exceeding 0.8wt%, the remainder being Al and unavoidable impurities; the process includes the following steps: (1) The novel high-magnesium aluminum alloy hot-deformed material is prepared by rolling or extrusion and subjected to solution heating and heat preservation treatment at 460~545℃ / 30~150min; (2) The heat-deformed material heated by solution cooling is subjected to first-stage quenching by air cooling, and the temperature is cooled to 420~450℃. The cooling rate is 2~8℃ / s, and the transfer time from solution cooling to first-stage quenching does not exceed 15s. (3) Perform a second quenching on the hot-deformed material after the first quenching, and cool it to 180~230℃ at a rate of 40~75℃ / s; (4) After the second-stage quenching, the hot-deformed material is subjected to a third-stage quenching and cooled to 30~50℃ at a rate of 2~8℃ / s. (5) The processed material after graded quenching is subjected to pre-deformation and aging treatment.

2. The solution heating-stage quenching process for the novel high-magnesium content aluminum alloy according to claim 1, characterized in that, The aluminum alloy is composed of the following components: Mg 6.3~9.9wt%, Zn 1.1~2.9wt%, Si 0.15~1.0wt%, and at least one of Mn, Cu, Zr, Sc and Ti elements with a total content not exceeding 0.6wt%, with the remainder being Al and unavoidable impurities.

3. The solution heating-stage quenching process for the novel high-magnesium content aluminum alloy according to claim 1 or 2, characterized in that, In step (1), the heat preservation temperature of the solution heating is 485~535℃, the heat preservation time is 60~120min, and the heating rate of the heat-deformed material from room temperature to solution temperature is 15~20℃ / h.

4. The solution heating-stage quenching process for novel high-magnesium content aluminum alloys according to claim 1 or 2, characterized in that, In step (2), during the first-stage quenching process, the final cooling temperature of the hot-deformed material is 430~440℃, the wind speed is 40~60m / s, the nozzle height is 50~80mm, and the angle between the nozzle and the horizontal plane of the hot-deformed material is 30~45°.

5. The solution heating-stage quenching process for novel high-magnesium content aluminum alloys according to claim 1 or 2, characterized in that, In step (3), during the second-stage quenching process, the final cooling temperature of the hot-deformed material is 190~210℃, the quenching medium pressure is 4~7 bar both above and below, the quenching medium temperature is 20~30℃, the nozzle height is 50~80mm, and the angle between the nozzle and the horizontal plane of the hot-deformed material is 30~40°.

6. The solution heating-stage quenching process for novel high-magnesium content aluminum alloys according to claim 1 or 2, characterized in that, In step (4), during the third-stage quenching process, the final cooling temperature of the hot-deformed material is 30~40℃, the wind speed is 40~60m / s, the nozzle height is 50~80mm, and the angle between the nozzle and the horizontal plane of the hot-deformed material is 30~45°.

7. The solution heating-stage quenching process for novel high-magnesium content aluminum alloys according to claim 1 or 2, characterized in that, In step (3), during the second-stage quenching process, the quenching medium is a water-based quenching liquid, which, by mass, includes: 10% polyethylene glycol, 10% butyl acrylate, 2% styrene, 3% acrylic acid, 5% isododecyl alcohol, 0.3% preservative, 0.1% defoamer, 0.5% antioxidant, and the remainder is water; the preservative is nitrite, the defoamer is polyether-modified silicone, and the antioxidant is tert-butylhydroquinone.

8. The solution heating-stage quenching process for the novel high-magnesium content aluminum alloy according to claim 1 or 2, characterized in that, In step (5), the pre-deformation amount of the hot-deformed material is 2~4.5%, the deformation rate is 0.5~1.0 mm / min, the pressure holding time is 50~100s, and the time interval between graded quenching and pre-deformation is no more than 5h.

9. The solution heating-stage quenching process for novel high-magnesium content aluminum alloys according to claim 1 or 2, characterized in that, In step (5), the aging treatment of the heat-deformed material is a two-stage artificial aging process. The first stage is an aging treatment of 12 to 48 hours at 60 to 105°C, and the second stage is an aging treatment of 1 to 24 hours at 135 to 190°C. The time interval between the pre-deformation and the two-stage artificial aging treatment is 5 to 60 days.

10. The solution heating-stage quenching process for novel high-magnesium content aluminum alloys according to claim 1 or 2, characterized in that, In step (4), after the third-stage quenching is completed, the hot-deformed material does not experience quenching cracking, and the size of the AlZnMg desolventized precipitate phase in the alloy matrix does not exceed 350nm.

11. A novel high-magnesium-content aluminum alloy processed material, characterized in that, The quenching residual stress of the processed material obtained by any one of claims 1 to 10 is reduced by more than 50 MPa compared with that obtained by direct single-stage spray quenching.

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