Heat treatment method for deformation and phase change synergistic strengthening of high-strength aluminum alloy

Abstract

The invention provides a heat treatment method for deformation and phase change synergistic strengthening of a high-strength aluminum alloy, and relates to the technical field of aluminum base alloy heat treatment. The treatment method comprises the following steps: S10, at a solid solution temperature, carrying out solid solution treatment on an aluminum alloy, and carrying out quenching treatment after the solid solution treatment to obtain a W-state aluminum alloy; s20, at the pre-aging temperature, the W-state aluminum alloy is subjected to pre-aging treatment, and after cooling, the PA-state aluminum alloy is obtained; s30, 0-8% of pre-deformation is conducted on the PA-state aluminum alloy, and the pre-hardened aluminum alloy is obtained; s40, at the first aging temperature, the pre-hardened aluminum alloy is subjected to first-stage aging treatment for 1-60 min, and a first-stage aluminum alloy is obtained after cooling; wherein the first aging temperature is smaller than the pre-aging temperature; s50, at the second aging temperature, the first-stage aluminum alloy is subjected to second-stage aging treatment for 1-60 min, and a second-stage aluminum alloy is obtained after cooling; wherein the second aging temperature is lower than the first aging temperature.

Description

Technical Field

[0001] The invention relates to the technical field of heat treatment of aluminum-based alloys, and in particular to a heat treatment method for synergistic strengthening of deformation and phase transformation of high-strength aluminum alloys. Background Art

[0002] Aluminum alloys are widely used in the automotive and aerospace fields due to their advantages such as low density, high strength and good corrosion resistance. However, aluminum alloys need to undergo subsequent aging treatment after forming to improve strength, especially to achieve peak aging mechanical properties. Aging treatment refers to a heat treatment process in which an aluminum alloy workpiece is subjected to solid solution treatment, high temperature quenching or a certain degree of cold working deformation, and then placed at a higher temperature or room temperature to maintain its shape and size, and the performance changes over time. However, traditional artificial aging treatment takes a long time and is inefficient, which limits the industrial application of high-strength aluminum alloys. Publication No. CN116377353A provides an optimization method for a high-rate heating regression and re-aging process for 7xxx series aluminum alloys. The patent improves the performance of 7xxx series aluminum alloys by performing a low-temperature aging, regression aging and secondary low-temperature aging on 7xxx series aluminum alloys. However, in this patent, the overall failure time needs to be more than 40 hours, and the aging time treatment time is relatively long.

[0003] It should be noted that the information disclosed in the above background technology section is only used to enhance the understanding of the background of the present disclosure, and therefore may include information that does not constitute the prior art known to ordinary technicians in the field. Summary of the invention

[0004] In view of this, the present invention proposes a heat treatment method for synergistic strengthening of deformation and phase transformation of high-strength aluminum alloy. Through the heat treatment method combining deformation and phase transformation, an aluminum alloy with mechanical properties close to T6 state peak aging is obtained with a shorter artificial aging period.

[0005] The technical solution of the present invention is achieved by providing a heat treatment method for synergistic strengthening of deformation and phase transformation of high-strength aluminum alloy, comprising the following steps:

[0006] S10, performing a solution treatment on the aluminum alloy at a solution temperature, and performing a quenching treatment after the solution treatment to obtain a W-state aluminum alloy;

[0007] S20, performing pre-aging treatment on the W-state aluminum alloy at the pre-aging temperature, and obtaining the PA-state aluminum alloy after cooling;

[0008] S30, pre-deforming the PA state aluminum alloy by 0-8% to obtain a pre-hardened aluminum alloy;

[0009] S40, performing a first-level aging treatment on the pre-hardened aluminum alloy at a first aging temperature for 1 to 60 minutes, and obtaining a first-level aluminum alloy after cooling; wherein the first aging temperature is less than the pre-aging temperature;

[0010] S50, performing a second aging treatment on the first-grade aluminum alloy at a second aging temperature for 1 to 60 minutes, and obtaining a second-grade aluminum alloy after cooling; wherein the second aging temperature is lower than the first aging temperature.

[0011] Thus, in the solution provided by the present invention, through pre-aging, pre-deformation and secondary aging treatment, and the temperature of each aging treatment satisfies the pre-aging temperature ≥ the first aging temperature > the second aging temperature, the synergistic strengthening effect of the deformation and phase transformation of the aluminum alloy is achieved, and an aluminum alloy with mechanical properties of T6 state peak aging is obtained.

[0012] On the basis of the above technical solution, preferably, in step S10, the quenching treatment is water quenching treatment; the water temperature used in the water quenching treatment is 20-25°C;

[0013] Before and after water quenching, the water temperature change is less than or equal to 5°C, and the water quenching transfer time does not exceed 25 seconds.

[0014] In this way, by optimizing the initial water temperature in the water quenching treatment, the change in water temperature before and after water quenching, and the water quenching time, it is possible to avoid using a cold mold for quenching, which results in the mechanical properties after T6 artificial aging being lower than the mechanical properties after peak aging.

[0015] On the basis of the above technical solution, preferably, in step S20, step S40 and step S50, the cooling is medium cooling at a temperature of 15 to 25°C.

[0016] On the basis of the above technical solution, preferably, in step S20, a GP zone is formed in the pre-aging treated aluminum alloy;

[0017] In step S40, a first-level main strengthening phase is formed in the first-level aluminum alloy;

[0018] In step S50, a second-level main strengthening phase and a GPII zone are formed in the second-level aluminum alloy.

[0019] On the basis of the above technical solution, preferably, S10, adopting a solution temperature of 488-554° C. to perform a solution treatment on the 2XXX series aluminum alloy, and performing a water quenching treatment after the solution treatment for 5-100 minutes to obtain a W-state 2XXX series aluminum alloy;

[0020] S20, pre-aging the W-state 2XXX series aluminum alloy at a pre-aging temperature of 90 to 180° C. for a pre-aging time of 1 to 24 h, and obtaining a PA-state 2XXX series aluminum alloy after cooling;

[0021] S30, pre-deforming the PA state 2XXX series aluminum alloy by 0-8% to obtain a pre-hardened 2XXX series aluminum alloy;

[0022] S40, performing a first aging treatment on the pre-hardened 2XXX series aluminum alloy for 1 to 60 minutes at a first aging temperature of 85 to 170° C., and obtaining a first-grade 2XXX series aluminum alloy after cooling; wherein the first aging temperature is less than the pre-aging temperature;

[0023] S50, subjecting the first-grade 2XXX series aluminum alloy to a second aging treatment for 1 to 60 minutes at a second aging temperature of 80 to 170° C., and obtaining a second-grade 2XXX series aluminum alloy after cooling; wherein the second aging temperature is lower than the first aging temperature.

[0024] More preferably, in step S20, a GP zone is formed in the pre-aging 2XXX series aluminum alloy; the size of the GP zone is 1 to 10 nm;

[0025] In step S40, a first-level main strengthening phase is formed in the first-level 2XXX series aluminum alloy, and the first-level main strengthening phase is a θ' phase with a size of 5 to 10 nm;

[0026] In step S50, a second-level main strengthening phase and a GPII zone are formed in the second-level 2XXX series aluminum alloy; the second-level main strengthening phase is a θ' phase with a size of 10 to 25 nm, and the size of the GPII zone is 1 to 10 nm.

[0027] On the basis of the above technical solution, preferably, S10, adopting a solution temperature of 504-579° C. to perform a solution treatment on the 6XXX series aluminum alloy, and performing a water quenching treatment after the solution treatment for 5-100 minutes to obtain a W-state 6XXX series aluminum alloy;

[0028] S20, performing pre-aging treatment on the W-state 6XXX series aluminum alloy at a pre-aging temperature of 90 to 170° C. for a pre-aging time of 1 to 24 h, and obtaining a PA-state 6XXX series aluminum alloy after cooling;

[0029] S30, pre-deforming the PA state 6XXX series aluminum alloy by 0-8% to obtain a pre-hardened 6XXX series aluminum alloy;

[0030] S40, performing a first aging treatment on the pre-hardened 6XXX series aluminum alloy for 1 to 60 minutes at a first aging temperature of 85 to 160° C., and obtaining a first-grade 6XXX series aluminum alloy after cooling; wherein the first aging temperature is less than or equal to the pre-aging temperature;

[0031] S50, subjecting the first-grade 6XXX series aluminum alloy to a second aging treatment for 1 to 60 minutes at a second aging temperature of 80 to 160° C., and obtaining a second-grade 6XXX series aluminum alloy after cooling; wherein the second aging temperature is lower than the first aging temperature.

[0032] More preferably, in step S20, a GP zone is formed in the pre-aging 6XXX series aluminum alloy; the size of the GP zone is 1 to 10 nm;

[0033] In step S40, a first-level main strengthening phase is formed in the first-level 6XXX series aluminum alloy, and the first-level main strengthening phase is a β" phase with a size of 5 to 10 nm;

[0034] In step S50, a second-level main strengthening phase and a GPII zone are formed in the second-level 6XXX series aluminum alloy; the second-level main strengthening phase is a β" phase with a size of 10 to 25 nm, and the GPII zone has a size of 1 to 10 nm.

[0035] On the basis of the above technical solution, preferably, S10, adopting a solution temperature of 449-521° C. to perform a solution treatment on the 7XXX series aluminum alloy, and performing a water quenching treatment after the solution treatment for 5-100 minutes to obtain a W-state 7XXX series aluminum alloy;

[0036] S20, pre-aging the W-state 7XXX series aluminum alloy at a pre-aging temperature of 85 to 130° C. for a pre-aging time of 1 to 24 h, and obtaining the PA-state 7XXX series aluminum alloy after cooling;

[0037] S30, pre-deforming the PA state 7XXX series aluminum alloy by 0-8% to obtain a pre-hardened 7XXX series aluminum alloy;

[0038] S40, performing a first aging treatment on the pre-hardened 7XXX series aluminum alloy for 1 to 60 minutes at a first aging temperature of 80 to 120° C., and obtaining a first-grade 7XXX series aluminum alloy after cooling; wherein the first aging temperature is less than or equal to the pre-aging temperature;

[0039] S50, subjecting the first-grade 7XXX series aluminum alloy to a second aging treatment for 1 to 60 minutes at a second aging temperature of 70 to 110° C., and obtaining a second-grade 7XXX series aluminum alloy after cooling; wherein the second aging temperature is lower than the first aging temperature.

[0040] More preferably, in step S20, a GP zone is formed in the pre-aging 7XXX series aluminum alloy; the size of the GP zone is 1 to 10 nm;

[0041] In step S40, a first-level main strengthening phase is formed in the first-level 7XXX series aluminum alloy, and the first-level main strengthening phase is an η' phase with a size of 5 to 10 nm;

[0042] In step S50, a second-level main strengthening phase and a GPII zone are formed in the second-level 7XXX series aluminum alloy; the second-level main strengthening phase is an η' phase with a size of 5 to 20 nm, and the size of the GPII zone is 1 to 10 nm.

[0043] In the above scheme, the W-state alloy is subjected to pre-aging treatment, so that a GP zone with a size of 1 to 10 nm can be formed in the aluminum alloy; the pre-deformation treatment can introduce more vacancies into the interior of the aluminum alloy, provide more nucleation sites and deformation energy storage for the strengthening phase, reduce the precipitation threshold of the main strengthening phase, and make the strengthening phase precipitate fully and in small size during the subsequent aging process. In this way, while ensuring the subsequent elongation, the strength of the aluminum alloy is initially improved. During the first-level aging treatment, the GP zone dissolves and forms the corresponding first-level main strengthening phase. During the second-level aging treatment, the aluminum alloy can continue to precipitate to form a second-level main strengthening phase and a GPII zone. During the aging treatment, since the main strengthening phase is bypassed by dislocations, cross slip is generated to soften, and the nanoclusters are cut by dislocations, and plane slip is generated to harden. The combined action of cross slip and plane slip improves the strain hardening ability of the aluminum alloy, so that the strength of the aluminum alloy reaches the strength of the T6 state alloy.

[0044] The heat treatment method for synergistic strengthening of deformation and phase transformation of high-strength aluminum alloy provided by the present invention has the following beneficial effects compared with the prior art:

[0045] 1. The aluminum alloy is treated by pre-aging + pre-deformation + secondary aging, which greatly shortens the aging treatment time, reduces the thermal processing time of the aluminum alloy, and improves production efficiency. At the same time, the method provided by the present disclosure enables the aluminum alloy to be synergistically strengthened by deformation and phase transformation during the treatment process, thereby improving the strength of the aluminum alloy.

[0046] 2. In the present invention, the pre-aging temperature ≥ the first-stage aging temperature > the second-stage aging temperature, so that the aluminum alloy obtains mechanical properties close to the peak-aged aluminum alloy in a shorter aging time. Therefore, the present invention proposes a heat treatment method for synergistic strengthening of deformation and phase transformation of high-strength aluminum alloys, which reduces the duration of artificial aging through the heat treatment process of pre-aging, pre-deformation and secondary aging, and obtains an aluminum alloy that reaches the peak aging T6 state strength. DETAILED DESCRIPTION

[0047] The following will be combined with the embodiments of the present invention to clearly and completely describe the technical solutions in the embodiments of the present invention. Obviously, the described embodiments are only part of the embodiments of the present invention, not all of the embodiments. Based on the embodiments of the present invention, all other embodiments obtained by ordinary technicians in this field without creative work are within the scope of protection of the present invention.

[0048] Example 1

[0049] In this embodiment, 2219 aluminum alloy is subjected to aging treatment to obtain T6 state 2219 aluminum alloy.

[0050] S10. Place the 2219 aluminum alloy in a heat treatment furnace for solution treatment at a solution temperature of 488-554°C for 40 minutes. After the solution treatment is completed, water quenching is performed at a water temperature of 25°C. The water temperature change before and after cooling does not exceed 5°C. The quenching transfer time does not exceed 25 seconds to obtain W-state 2219 aluminum alloy.

[0051] Among them, the mass percentage composition of 2219 aluminum alloy includes 0.20% silicon, 0.3% iron, 5.8-6.8% copper, 0.20-0.40% manganese, 0.02% magnesium, 0.10% zinc, 0.02-0.10% titanium, 0.05-0.15% vanadium, 0.10-0.25% zirconium, 0.15% others, and the balance is aluminum.

[0052] S20. After quenching, the W-state 2219 aluminum alloy is immediately placed in a pre-aging furnace for pre-aging treatment; the pre-aging temperature is 160° C., the pre-aging time is 30 min, and then cooled at room temperature to obtain the PA-state 2219 aluminum alloy.

[0053] S30, subjecting the PA state 2219 aluminum alloy to 0% pre-deformation treatment.

[0054] S40, subjecting the 2219 aluminum alloy obtained in step S30 to a first-level aging treatment, wherein the first-level aging temperature is 75° C., the first-level aging time is 30 min, and then cooled at room temperature to obtain a first-level 2219 aluminum alloy.

[0055] S50. After the first-stage aging is completed, the first-stage 2219 aluminum alloy is subjected to a second-stage aging treatment. The second-stage aging temperature is 70° C., the second-stage aging time is 30 min, and then cooled to room temperature. The obtained second-stage 2219 aluminum alloy is defined as T6 state 2219 aluminum alloy 1.

[0056] Example 2

[0057] The difference between Example 2 and Example 1 is that the pre-aging temperature is 160°C and the pre-aging time is 30 minutes; the first-stage aging temperature is 75°C and the first-stage aging time is 30 minutes; the second-stage aging temperature is 140°C and the second-stage aging time is 30 minutes. The rest of the process is the same as that of Example 1, and the obtained second-stage 2219 aluminum alloy is defined as T6 state 2219 aluminum alloy 2.

[0058] The difference between Example 3 to Example 27 and Example 1 also lies in the different pre-aging temperatures, pre-deformation amounts, first-stage aging temperatures, and second-stage aging temperatures. The rest of the process is the same as that of Example 1, and the obtained second-stage 2219 aluminum alloy is defined as T6 state 2219 aluminum alloy 3 to T6 state 2219 aluminum alloy 27, respectively. Among them, in Example 10 to Example 27, the pre-deformation is 4% or 8%. By pre-hardening the PA-state 2219 aluminum alloy, more vacancies will be introduced into the aluminum alloy, providing more nucleation sites and deformation energy storage for the strengthening phase, lowering the precipitation threshold of the main strengthening phase, so that the strengthening phase is fully precipitated and small in size in the subsequent process. In this way, while ensuring the subsequent elongation, the strength of the aluminum alloy is preliminarily improved. The temperature and time parameters of the aging treatment of each embodiment are shown in Table 1.

[0059] As shown in Table 1, under the aging treatment parameters provided in Example 14, the tensile strength of the obtained T6 state 2219 aluminum alloy 14 can reach 455MPa, and the yield strength can reach 365MPa. Under the aging treatment parameters provided in Example 23, the tensile strength of the obtained T6 state 2219 aluminum alloy 23 can reach 454MPa, and the yield strength can reach 363MPa. In this way, when the pre-aging temperature > first-stage aging temperature > second-stage aging temperature are satisfied, the aluminum alloy completes the synergistic strengthening of deformation and phase transformation through pre-aging treatment, pre-deformation and secondary aging treatment, and the mechanical properties obtained are close to the peak-aged T6 state 2219 aluminum alloy under shorter artificial aging.

[0060] Embodiment 28

[0061] In this embodiment, 6061 aluminum alloy is subjected to aging treatment to obtain T6 state 6061 aluminum alloy.

[0062] S10, placing the 6061 aluminum alloy in a heat treatment furnace for solution treatment, the solution temperature is 504-579°C, the solution time is 30 minutes, and after the solution treatment is completed, water quenching treatment is performed, the water temperature is 25°C, the water temperature change before and after cooling does not exceed 5°C, and the quenching transfer time does not exceed 25 seconds to obtain W-state 6061 aluminum alloy.

[0063] Among them, the mass percentage composition of the 6061 aluminum alloy includes 0.40-0.8% silicon, 0.7% iron, 0.15-0.4% copper, 0.15% manganese, 0.8-1.2% magnesium, 0.04-0.35% chromium, 0.25% zinc, 0.15% titanium, 0.15% others, and the balance is aluminum.

[0064] S20. After quenching, the W-state 6061 aluminum alloy is immediately placed in a pre-aging furnace for pre-aging treatment; the pre-aging temperature is 150° C., the pre-aging time is 30 min, and then cooled at room temperature to obtain a PA-state 6061 aluminum alloy.

[0065] S30, subjecting the PA state 6061 aluminum alloy to 0% pre-deformation treatment.

[0066] S40, subjecting the 6061 aluminum alloy obtained in step S30 to a first-level aging treatment, wherein the first-level aging temperature is 75° C., the first-level aging time is 30 min, and then cooled at room temperature to obtain a first-level 6061 aluminum alloy.

[0067] S50. After the first-stage aging is completed, the first-stage 6061 aluminum alloy is subjected to a second-stage aging treatment. The second-stage aging temperature is 70° C., the second-stage aging time is 30 min, and then cooled to room temperature. The obtained second-stage 6061 aluminum alloy is defined as T6 state 6061 aluminum alloy 1.

[0068] Embodiment 29

[0069] The difference between Example 29 and Example 28 is that the pre-aging temperature is 150°C and the pre-aging time is 30 minutes; the first-stage aging temperature is 75°C and the first-stage aging time is 30 minutes; the second-stage aging temperature is 130°C and the second-stage aging time is 30 minutes. The rest of the process is the same as that of Example 28, and the obtained second-stage 6061 aluminum alloy is defined as T6 state 6061 aluminum alloy 2.

[0070] The difference between Examples 30 to 54 and Example 28 is also that the pre-aging temperature, pre-deformation, first-stage aging temperature and second-stage aging temperature are different. The rest is the same as the process of Example 28, and the obtained second-stage 6061 aluminum alloy is defined as T6 state 6061 aluminum alloy 3 to T6 state 6061 aluminum alloy 27. The temperature and time parameters of the aging treatment of each example are shown in Table 1.

[0071] As shown in Table 1, under the aging treatment parameters provided in Example 41, the tensile strength of the obtained T6 state 6061 aluminum alloy 14 can reach 430MPa, and the yield strength can reach 350MPa; under the aging treatment parameters provided in Example 50, the tensile strength of the obtained T6 state 6061 aluminum alloy 23 can reach 432MPa, and the yield strength can reach 345MPa. In this way, when the pre-aging temperature ≥ the first-stage aging temperature > the second-stage aging temperature is satisfied, the aluminum alloy completes the synergistic strengthening of deformation and phase transformation through pre-aging treatment, pre-deformation and secondary aging treatment, and the mechanical properties obtained under a shorter artificial aging are close to those of the T6 state 6061 aluminum alloy with peak aging.

[0072] Embodiment 55

[0073] In this embodiment, 7075 aluminum alloy is subjected to aging treatment to obtain T6 state 7075 aluminum alloy.

[0074] S10. Place the 7075 aluminum alloy in a heat treatment furnace for solution treatment at a solution temperature of 449-521°C for 30 minutes. After the solution treatment is completed, water quenching is performed at a water temperature of 25°C. The water temperature change before and after cooling does not exceed 5°C. The quenching transfer time does not exceed 25 seconds to obtain W-state 7075 aluminum alloy.

[0075] Among them, the mass percentage composition of 7075 aluminum alloy includes 0.4% silicon, 0.5% iron, 1.2-2.0% copper, 0.3% manganese, 2.1-2.9% magnesium, 0.18-0.28% chromium, 5.1-6.1% zinc, 0.2% titanium, 0.15% others, and the balance is aluminum.

[0076] S20. After quenching, the W-state 7075 aluminum alloy is immediately placed in a pre-aging furnace for pre-aging treatment; the pre-aging temperature is 110° C., the pre-aging time is 30 min, and then cooled at room temperature to obtain the PA-state 7075 aluminum alloy.

[0077] S30, subjecting the PA state 7075 aluminum alloy to 0% pre-deformation treatment.

[0078] S40, subjecting the 7075 aluminum alloy obtained in step S30 to a first-level aging treatment, wherein the first-level aging temperature is 75° C., the first-level aging time is 30 min, and then cooled at room temperature to obtain a first-level 7075 aluminum alloy.

[0079] S50. After the first-stage aging is completed, the first-stage 7075 aluminum alloy is subjected to a second-stage aging treatment. The second-stage aging temperature is 70°C, the second-stage aging time is 30 minutes, and then cooled to room temperature. The obtained second-stage 7075 aluminum alloy is defined as T6 state 7075 aluminum alloy 1.

[0080] Embodiment 56

[0081] The difference between Example 56 and Example 55 is that the pre-aging temperature is 110°C and the pre-aging time is 30 minutes; the first-stage aging temperature is 75°C and the first-stage aging time is 30 minutes; the second-stage aging temperature is 90°C and the second-stage aging time is 30 minutes. The rest of the process is the same as that of Example 55, and the obtained second-stage 7075 aluminum alloy is defined as T6 state 7075 aluminum alloy 2.

[0082] The difference between Example 57 to Example 81 and Example 55 also lies in the different pre-aging temperatures, pre-deformation amounts, first-stage aging temperatures, and second-stage aging temperatures. The rest of the process is the same as that of Example 55, and the second-stage 7075 aluminum alloy obtained is defined as T6 state 7075 aluminum alloy 3 to T6 state 7075 aluminum alloy 27, respectively. Among them, in Example 64 to Example 81, the pre-deformation is 4% or 8%. By pre-deformation treatment of the PA-state grade 7075 aluminum alloy, more vacancies will be introduced into the aluminum alloy, providing more nucleation sites and deformation energy storage for the strengthening phase, reducing the precipitation threshold of the main strengthening phase, so that the strengthening phase is fully precipitated and small in size during the subsequent aging process. The temperature and time parameters of the aging treatment of each embodiment are shown in Table 1.

[0083] As shown in Table 1, under the aging treatment parameters provided in Example 68, the tensile strength of the obtained T6 state 7075 aluminum alloy 14 can reach 615MPa, and the yield strength can reach 510MPa; under the aging treatment parameters provided in Example 77, the tensile strength of the obtained T6 state 7075 aluminum alloy 23 can reach 611MPa, and the yield strength can reach 505MPa. In this way, when the pre-aging temperature ≥ the first-level aging temperature > the second-level aging temperature is satisfied, the aluminum alloy completes the synergistic strengthening of deformation and phase transformation through pre-aging treatment, pre-deformation and secondary aging treatment, and the mechanical properties of the T6 state 7075 aluminum alloy close to the peak aging can be obtained under a shorter artificial aging.

[0084] Table 1. Summary of different aging treatments for aluminum alloys of different materials

[0085]

[0086]

[0087]

[0088] It should be noted that, although the various steps of the heat treatment method for synergistic strengthening of high-strength aluminum alloy by deformation and phase transformation in the present disclosure are described in a specific order in the specification, this does not require or imply that these steps must be performed in this specific order, or that all the steps shown must be performed to achieve the desired results. Additionally or alternatively, some steps may be omitted, multiple steps may be combined into one step, and / or one step may be decomposed into multiple steps, etc.

[0089] The above description is only a preferred embodiment of the present invention and is not intended to limit the present invention. Any modifications, equivalent substitutions, improvements, etc. made within the spirit and principles of the present invention should be included in the protection scope of the present invention.

Claims

1. A heat treatment method for synergistic strengthening of deformation and phase transformation of high-strength aluminum alloy, characterized in that: The following steps are involved: S10, performing a solution treatment on the aluminum alloy at a solution temperature, and performing a quenching treatment after the solution treatment to obtain a W-state aluminum alloy; S20, performing pre-aging treatment on the W-state aluminum alloy at the pre-aging temperature, and obtaining the PA-state aluminum alloy after cooling; S30, pre-deforming the PA state aluminum alloy by 0-8% to obtain a pre-hardened aluminum alloy; S40, performing a first-level aging treatment on the pre-hardened aluminum alloy at a first aging temperature for 1 to 60 minutes, and obtaining a first-level aluminum alloy after cooling; wherein the first aging temperature is less than the pre-aging temperature; S50, performing a second aging treatment on the first-grade aluminum alloy at a second aging temperature for 1 to 60 minutes, and obtaining a second-grade aluminum alloy after cooling; wherein the second aging temperature is lower than the first aging temperature.

2. The heat treatment method for synergistic strengthening of deformation and phase transformation of high-strength aluminum alloy according to claim 1, characterized in that: In step S10, the quenching treatment is water quenching treatment; The water temperature used in the water quenching treatment is 20-25°C; Before and after water quenching, the water temperature change is less than or equal to 5°C, and the water quenching transfer time does not exceed 25 seconds.

3. The heat treatment method for synergistic strengthening of deformation and phase transformation of high-strength aluminum alloy according to claim 1, characterized in that: In step S20, step S40 and step S50, the cooling is performed at a temperature of 15 to 25°C.

4. The heat treatment method for synergistic strengthening of deformation and phase transformation of high-strength aluminum alloy according to claim 1, characterized in that: In step S20, a GP zone is formed in the pre-aging treated aluminum alloy; In step S40, a first-level main strengthening phase is formed in the first-level aluminum alloy; In step S50, a second-level main strengthening phase and a GPII zone are formed in the second-level aluminum alloy.

5. The heat treatment method for synergistic strengthening of deformation and phase transformation of high-strength aluminum alloy according to any one of claims 1 to 4, characterized in that: S10, performing a solution treatment on the 2XXX series aluminum alloy at a solution temperature of 488 to 554° C., and performing a water quenching treatment after the solution treatment for 5 to 100 minutes to obtain a W-state 2XXX series aluminum alloy; S20, pre-aging the W-state 2XXX series aluminum alloy at a pre-aging temperature of 90 to 180° C. for a pre-aging time of 1 to 24 h, and obtaining a PA-state 2XXX series aluminum alloy after cooling; S30, pre-deforming the PA state 2XXX series aluminum alloy by 0-8% to obtain a pre-hardened 2XXX series aluminum alloy; S40, performing a first aging treatment on the pre-hardened 2XXX series aluminum alloy for 1 to 60 minutes at a first aging temperature of 85 to 170° C., and obtaining a first-grade 2XXX series aluminum alloy after cooling; wherein the first aging temperature is less than the pre-aging temperature; S50, subjecting the first-grade 2XXX series aluminum alloy to a second aging treatment for 1 to 60 minutes at a second aging temperature of 80 to 170° C., and obtaining a second-grade 2XXX series aluminum alloy after cooling; wherein the second aging temperature is lower than the first aging temperature.

6. The heat treatment method for synergistic strengthening of deformation and phase transformation of high-strength aluminum alloy according to claim 5, characterized in that: In step S20, a GP zone is formed in the pre-aging 2XXX aluminum alloy; the size of the GP zone is 1 to 10 nm; In step S40, a first-level main strengthening phase is formed in the first-level 2XXX series aluminum alloy, and the first-level main strengthening phase is a θ' phase with a size of 5 to 10 nm; In step S50, a second-level main strengthening phase and a GPII zone are formed in the second-level 2XXX series aluminum alloy; the second-level main strengthening phase is a θ' phase with a size of 10 to 25 nm, and the size of the GPII zone is 1 to 10 nm.

7. The heat treatment method for synergistic strengthening of deformation and phase transformation of high-strength aluminum alloy according to any one of claims 1 to 4, characterized in that: S10, performing a solution treatment on the 6XXX series aluminum alloy at a solution temperature of 504 to 579° C., and performing a water quenching treatment after the solution treatment for 5 to 100 minutes to obtain a W-state 6XXX series aluminum alloy; S20, performing pre-aging treatment on the W-state 6XXX series aluminum alloy at a pre-aging temperature of 90 to 170° C. for a pre-aging time of 1 to 24 h, and obtaining a PA-state 6XXX series aluminum alloy after cooling; S30, pre-deforming the PA state 6XXX series aluminum alloy by 0-8% to obtain a pre-hardened 6XXX series aluminum alloy; S40, performing a first aging treatment on the pre-hardened 6XXX series aluminum alloy for 1 to 60 minutes at a first aging temperature of 85 to 160° C., and obtaining a first-grade 6XXX series aluminum alloy after cooling; wherein the first aging temperature is less than or equal to the pre-aging temperature; S50, subjecting the first-grade 6XXX series aluminum alloy to a second aging treatment for 1 to 60 minutes at a second aging temperature of 80 to 160° C., and obtaining a second-grade 6XXX series aluminum alloy after cooling; wherein the second aging temperature is lower than the first aging temperature.

8. The heat treatment method for synergistic strengthening of deformation and phase transformation of high-strength aluminum alloy according to claim 7, characterized in that: In step S20, a GP zone is formed in the pre-aging 6XXX aluminum alloy; the size of the GP zone is 1 to 10 nm; In step S40, a first-level main strengthening phase is formed in the first-level 6XXX series aluminum alloy, and the first-level main strengthening phase is a β" phase with a size of 5 to 10 nm; In step S50, a second-level main strengthening phase and a GPII zone are formed in the second-level 6XXX series aluminum alloy; the second-level main strengthening phase is a β" phase with a size of 10 to 25 nm, and the GPII zone has a size of 1 to 10 nm.

9. The heat treatment method for synergistic strengthening of deformation and phase transformation of high-strength aluminum alloy according to any one of claims 1 to 4, characterized in that: S10, performing a solution treatment on the 7XXX series aluminum alloy at a solution temperature of 449 to 521° C., and performing a water quenching treatment after the solution treatment for 5 to 100 minutes to obtain a W-state 7XXX series aluminum alloy; S20, pre-aging the W-state 7XXX series aluminum alloy at a pre-aging temperature of 85 to 130° C. for a pre-aging time of 1 to 24 h, and obtaining the PA-state 7XXX series aluminum alloy after cooling; S30, pre-deforming the PA state 7XXX series aluminum alloy by 0-8% to obtain a pre-hardened 7XXX series aluminum alloy; S40, performing a first aging treatment on the pre-hardened 7XXX series aluminum alloy for 1 to 60 minutes at a first aging temperature of 80 to 120° C., and obtaining a first-grade 7XXX series aluminum alloy after cooling; wherein the first aging temperature is less than or equal to the pre-aging temperature; S50, subjecting the first-grade 7XXX series aluminum alloy to a second aging treatment for 1 to 60 minutes at a second aging temperature of 70 to 110° C., and obtaining a second-grade 7XXX series aluminum alloy after cooling; wherein the second aging temperature is lower than the first aging temperature.

10. The heat treatment method for synergistic strengthening of deformation and phase transformation of high-strength aluminum alloy according to claim 9, characterized in that: In step S20, a GP zone is formed in the pre-aging 7XXX aluminum alloy; the size of the GP zone is 1 to 10 nm; In step S40, a first-level main strengthening phase is formed in the first-level 7XXX series aluminum alloy, and the first-level main strengthening phase is an η' phase with a size of 5 to 10 nm; In step S50, a second-level main strengthening phase and a GPII zone are formed in the second-level 7XXX series aluminum alloy; the second-level main strengthening phase is an η' phase with a size of 5 to 20 nm, and the size of the GPII zone is 1 to 10 nm.

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