High-strength corrosion-resistant aluminum alloy plate and method for manufacturing the same

Abstract

The application provides a high-strength corrosion-resistant aluminum alloy plate and a preparation method thereof, and belongs to the technical field of aluminum alloys.The preparation method comprises the following steps: S1, dosing, wherein the mass percentage of Si is 0.8-0.9%, the mass percentage of Mg is 1.8-2.0%, the mass percentage of Zn is 0.13-0.19%, the mass percentage of Mn is 0.4-0.6%, the mass percentage of Zr is 0.05-0.1%, the mass percentage of Ti is 0.05-0.15%, the mass percentage of Cu is 0.04-0.08%, the mass percentage of Fe is less than or equal to 0.4%, and the balance is Al and inevitable impurities; S2, smelting, and casting into a ingot with a thickness of 200-300 mm; S3, homogenizing treatment, hot rolling to a plate thickness of 6-8 mm, cold rolling to a plate thickness of 2-4 mm, and obtaining a final plate; S4, solid solution treatment, and composite quenching liquid quenching treatment; and S5, aging treatment, and the aluminum alloy plate obtained by the application has excellent mechanical properties and corrosion resistance.

Description

Technical Field

[0001] The present invention belongs to the technical field of aluminum alloys, and in particular relates to a high-strength, corrosion-resistant aluminum alloy plate and a preparation method thereof. Background Art

[0002] Aluminum alloy sheet is a lightweight metal material with aluminum as the matrix and formed by adding alloying elements such as Cu, Mn, Mg, Si, and Zn. It has both high strength and good processing properties and is widely used in construction, transportation, aerospace and other fields.

[0003] The addition of Mn helps refine grains and improve corrosion resistance. Cu can prevent a decrease in corrosion resistance. When Mg is dissolved in the aluminum matrix, it causes lattice distortion due to differences in atomic size, creating resistance to dislocation movement and directly increasing strength. After Mg combines with Si to form the Mg2Si phase, nanoparticles (such as β'' phase) precipitate during aging, significantly improving strength by more efficiently pinning dislocations and hindering slip, achieving an effect far superior to solid solution strengthening. Zn, when dissolved in the aluminum matrix, causes lattice distortion due to the difference in atomic radius from aluminum, increasing resistance to dislocation movement and thus improving alloy strength. Zn combines with Mg to form MgZn2 nanoscale precipitates (such as η phase). During aging, these fine, dispersed precipitates pin dislocations, hindering slip and increasing tensile strength.

[0004] The ratio of Mg to Si and the ratio of Zn to Mg need to be precisely controlled. If Mg is in excess, the Mg that does not participate in the reaction cannot form Mg2Si / MgZn2 precipitation phase, but remains in the matrix in the form of solid solution atoms. If its solid solution concentration exceeds the critical value, it will lead to excessive accumulation of lattice distortion, which will in turn cause microcracks and decreased interfacial bonding strength, resulting in a decrease in strength. Excess Mg will also interfere with the formation kinetics of the precipitation phase, resulting in coarsening or uneven distribution of the precipitate phase particles, weakening its efficiency in pinning dislocations and reducing the strengthening effect. Summary of the Invention

[0005] In order to solve the problems existing in the background technology, the present invention provides a high-strength and corrosion-resistant aluminum alloy plate and a preparation method thereof, which can ensure that the obtained aluminum alloy plate has both excellent mechanical properties (yield strength / tensile strength) and corrosion resistance.

[0006] In order to achieve the above objectives, in a first aspect, the present invention provides a method for preparing a high-strength, corrosion-resistant aluminum alloy plate, comprising the following steps:

[0007] S1. The ingredients are prepared based on the chemical composition of the high-strength and corrosion-resistant aluminum alloy plate, which is calculated by mass percentage as follows: Si: 0.8-0.9%, Mg: 1.8-2.0%, Zn: 0.13-0.19%, Mn: 0.4-0.6%, Zr: 0.05-0.1%, Ti: 0.05-0.15%, Cu: 0.04-0.08%, Fe≤0.4%, and the balance is Al and unavoidable impurities;

[0008] S2. Melting under argon protection and casting into ingots with a thickness of 200-300 mm;

[0009] S3, after homogenizing the ingot, hot rolling it to a plate thickness of 6-8 mm, and then cold rolling it to a plate thickness of 2-4 mm to obtain a final plate;

[0010] S4, performing a solution treatment on the final plate, and then performing a quenching treatment using a composite quenching liquid; the composite quenching liquid comprises, by mass percentage, 5-6% potassium nitrate and 14-17% PAG, with the balance being water;

[0011] S5. Aging treatment is performed to obtain the high-strength and corrosion-resistant aluminum alloy plate.

[0012] Furthermore, in S3, the specific operation of the homogenization treatment is: keeping warm at 540-560°C for 8-12 hours.

[0013] Furthermore, in S3, the specific operation of hot rolling is: the starting rolling temperature is 480-500°C, and the finishing rolling temperature is ≥350°C.

[0014] Furthermore, in S3, the specific operation of cold rolling is: two-stage rolling, with annealing at 300° C. for 2 hours in the middle.

[0015] Furthermore, in S4, the specific operation of the solution treatment is: placing the final plate in a roller hearth furnace, heating to 530-550° C., and keeping the temperature for 30-50 minutes.

[0016] Furthermore, in S4, the cooling rate of the quenching treatment includes: a cooling rate in a high temperature zone of >300°C>120°C / s, and a cooling rate in a low temperature zone of <200°C<50°C / s.

[0017] Furthermore, in S5, the specific operation of the aging treatment is: first, keep the temperature at 80-100°C for 7-8 hours to improve the formability; then keep the temperature at 160-180°C for 8-12 hours to obtain the target strength.

[0018] In a second aspect, the present invention provides a high-strength, corrosion-resistant aluminum alloy plate, which is prepared using the above-mentioned preparation method.

[0019] Furthermore, the yield strength of the high-strength and corrosion-resistant aluminum alloy plate is greater than 302 MPa, and the tensile strength is greater than 395 MPa.

[0020] This application has the following beneficial effects:

[0021] In the preparation of aluminum alloy sheet materials, the composite quenching fluid maintains a cooling rate of >120°C / s in the high-temperature range (>300°C) (significantly higher than the <100°C / s achieved with water quenching). This allows excess Mg to rapidly combine with Si and Zn to form high-density Mg2Si and MgZn2 nano-precipitates (15–30 nm in size). This high-speed cooling suppresses precipitate coarsening, increasing their volume fraction. The composite quenching fluid maintains a cooling rate of <50°C / s in the low-temperature range (<200°C), preventing localized stress concentration and grain boundary embrittlement caused by rapid cooling. Combined with the high-density nano-precipitates in the high-temperature range, this results in a uniform stress distribution and reduces the probability of crack initiation.

[0022] When Mg is excessive, potassium nitrate in the composite quenching liquid adsorbs free Mg atoms. On the one hand, it regulates the solid solution concentration, reduces the lattice distortion stress, and retains the coherent strain strengthening effect; on the other hand, it limits the grain boundary segregation, compresses the PFZ width, and improves the grain boundary strength.

[0023] Rapid cooling (>120°C / s) can also transform excess Mg into high-density nano-precipitates, breaking the limits of traditional solid solution strengthening, while slow cooling (<50°C / s) reduces residual stress. Combined with the nitrate adsorption effect, this achieves a synergistic enhancement effect of precipitation strengthening and stress optimization. BRIEF DESCRIPTION OF THE DRAWINGS

[0024] Figure 1 This is a comparative trend diagram of the yield strength and tensile strength data of the aluminum alloy specimens obtained from Examples 1 to 3 and Comparative Examples 1 to 3 in Test Example 1 of the present invention;

[0025] Figure 2 This is a comparison chart of salt spray test corrosion pictures of aluminum alloy specimens prepared in Example 1 to Example 3 and Comparative Example 4 in Test Example 2 of the present invention; wherein a is Example 1, b is Example 2, c is Example 3, and d is Comparative Example 4. DETAILED DESCRIPTION

[0026] The following will provide a clear and complete description of the technical solutions in the embodiments of the present invention in conjunction with the accompanying drawings. Obviously, the described embodiments are only part of the embodiments of the present invention, not all of the embodiments. All other embodiments obtained by ordinary technicians in this field based on the embodiments of the present invention without making any creative efforts shall fall within the scope of protection of the present invention.

[0027] Unless otherwise specified, the raw materials used in the examples and comparative examples of the present application are all commercially available.

[0028] Embodiment 1: A method for preparing a high-strength corrosion-resistant aluminum alloy plate, comprising the following steps:

[0029] S1, based on the chemical composition of the high-strength corrosion-resistant aluminum alloy plate, the ingredients are as follows: Si: 0.84%, Mg: 1.9%, Zn: 0.156%, Mn: 0.5%, Zr: 0.08%, Ti: 0.1%, Cu: 0.06%, Fe: 0.2%, and the balance is Al and unavoidable impurities.

[0030] S2, under the protection of argon (purity ≥ 99.99%), smelting (about 720°C) and casting into a ingot with a thickness of 240mm.

[0031] S3, homogenizing treatment is performed on the ingot, and the specific operation is 550°C for 10h. Then, hot rolling is performed, the opening rolling temperature is 490°C, the final rolling temperature is 360°C, and the hot rolling is performed to a plate thickness of 7mm; then cold rolling is performed, two-stage rolling, intermediate annealing at 300°C for 2h, cold rolling to a plate thickness of 3mm, and finally obtaining the final plate.

[0032] S4, solid solution treatment is performed on the final plate, and the specific operation is as follows: the final plate is placed in a roller hearth furnace, heated to 540°C, and held for 40min. Then, quenching treatment is performed using a composite quenching liquid. The composite quenching liquid comprises 5.5% potassium nitrate and 15% PAG by mass percent, and the balance is water. Among them, PAG is polyalkylene glycol. The cooling rate of the quenching treatment includes: the cooling rate in the high temperature zone >300°C is about 125°C / s, the cooling rate gradually decreases in the medium temperature zone 300-200°C, and the cooling rate in the low temperature zone <200°C is about 45°C / s.

[0033] S5, aging treatment, the specific operation is as follows: first, 90°C for 7.5h to improve formability; then, 170°C for 10h to obtain the target strength; thus obtaining the high-strength corrosion-resistant aluminum alloy plate.

[0034] Embodiment 2: The difference between this embodiment and embodiment 1 is that: a method for preparing a high-strength corrosion-resistant aluminum alloy plate, comprising the following steps:

[0035] S1, based on the chemical composition of the high-strength corrosion-resistant aluminum alloy plate, the ingredients are as follows: Si: 0.8%, Mg: 1.8%, Zn: 0.13%, Mn: 0.4%, Zr: 0.05%, Ti: 0.05%, Cu: 0.04%, Fe: 0.2%, and the balance is Al and unavoidable impurities.

[0036] S2, smelting under the protection of argon, and casting into a ingot with a thickness of 200mm.

[0037] S3. The ingot is homogenized by holding it at 540°C for 12 hours. It is then hot rolled with a starting temperature of 480°C and a final temperature of 350°C until the plate thickness reaches 6 mm. It is then cold rolled in two stages, with an intermediate annealing at 300°C for 2 hours, and then cold rolled to a plate thickness of 3 mm to obtain the final plate.

[0038] S4. Solution treatment of the final plate is performed by placing the final plate in a roller-hearth furnace, heating it to 530°C, and holding it there for 50 minutes. The final plate is then quenched using a composite quenching fluid consisting of 5% potassium nitrate and 14% PAG by weight, with the balance being water. The cooling rates for the quenching process are approximately 125°C / s in the high-temperature zone (>300°C) and 45°C / s in the low-temperature zone (<200°C).

[0039] S5. Aging treatment: The specific operation is: first keep it at 80℃ for 8 hours to improve the formability; then keep it at 160℃ for 12 hours to obtain the target strength; thus, a high-strength and corrosion-resistant aluminum alloy plate is obtained.

[0040] Example 3: This example differs from Example 1 in that: a method for preparing a high-strength, corrosion-resistant aluminum alloy plate comprises the following steps:

[0041] S1. The ingredients are prepared based on the chemical composition of high-strength and corrosion-resistant aluminum alloy plates, which are Si: 0.9%, Mg: 2.0%, Zn: 0.19%, Mn: 0.6%, Zr: 0.1%, Ti: 0.15%, Cu: 0.08%, Fe: 0.2%, and the balance is Al and unavoidable impurities.

[0042] S2. Melt under argon protection and cast into an ingot with a thickness of 300 mm.

[0043] S3. The ingot is homogenized by holding it at 560°C for 8 hours. It is then hot rolled with a starting temperature of 500°C and a final temperature of 370°C until the plate thickness reaches 8 mm. It is then cold rolled in two stages, with an intermediate annealing at 300°C for 2 hours, and then cold rolled to a plate thickness of 3 mm to obtain the final plate.

[0044] S4. Solution treatment of the final plate is performed by placing the final plate in a roller-hearth furnace, heating it to 550°C, and holding it there for 30 minutes. The final plate is then quenched using a composite quenching fluid. The composite quenching fluid consists of 6% potassium nitrate and 17% PAG by mass, with the balance being water. The cooling rate for the quenching treatment is approximately 125°C / s in the high-temperature zone above 300°C, and approximately 45°C / s in the low-temperature zone below 200°C.

[0045] S5. Aging treatment: The specific operation is: first keep it at 100℃ for 7 hours to improve the formability; then keep it at 180℃ for 8 hours to obtain the target strength; thus, a high-strength and corrosion-resistant aluminum alloy plate is obtained.

[0046] Comparative Example 1: The difference between this comparative example and Example 1 is that 1.9% Mg is changed to 1.47% Mg, and the quenching treatment with the composite quenching liquid is changed to water quenching.

[0047] The details are as follows: A method for preparing a high-strength and corrosion-resistant aluminum alloy plate comprises the following steps:

[0048] S1. The ingredients are prepared based on the chemical composition of high-strength and corrosion-resistant aluminum alloy plates, which are Si: 0.8%, Mg: 2%, Zn: 0.8%, Mn: 0.5%, Zr: 0.08%, Ti: 0.1%, Cu: 0.06%, Fe: 0.2%, and the balance is Al and unavoidable impurities.

[0049] S2. Melting under argon protection and casting into an ingot with a thickness of 240 mm.

[0050] S3. The ingot is homogenized by holding it at 550°C for 10 hours. It is then hot rolled with a starting temperature of 490°C and a final temperature of 360°C until the plate thickness reaches 7 mm. It is then cold rolled in two stages, with an intermediate annealing at 300°C for 2 hours, and then cold rolled to a plate thickness of 3 mm to obtain the final plate.

[0051] S4. Solution treatment of the final plate is performed by placing the final plate in a roller hearth furnace, heating it to 540°C, and holding it at that temperature for 40 minutes. The final plate is then water quenched, i.e., quenched with water. The cooling rate for the quenching treatment is as follows: the cooling rate in the high temperature zone >300°C is approximately 90°C / s, the cooling rate in the medium temperature zone of 300-200°C gradually decreases, and the cooling rate in the low temperature zone <200°C is approximately 45°C / s.

[0052] S5, aging treatment, the specific operation is: first keep it at 90℃ for 7.5h to improve the formability; then keep it at 170℃ for 10h to obtain the target strength; thus, a high-strength and corrosion-resistant aluminum alloy plate is obtained.

[0053] Comparative Example 2: This comparative example differs from Example 1 in that 1.9% Mg is changed to 1.47% Mg.

[0054] Comparative Example 3: This comparative example differs from Example 1 in that the quenching treatment using the composite quenching liquid is replaced by water quenching.

[0055] Comparative Example 4: The difference between this comparative example and Example 1 is that the chemical components Mn and Cu are deleted.

[0056] Test Example 1: Test items: ① Tensile test - yield strength; ② Tensile test - tensile strength; Reference: GB / T 228.1-2021 Metallic materials - Tensile testing - Part 1: Room temperature test methods. Test subjects: Aluminum alloy plate specimens prepared in Examples 1-3 and Comparative Examples 1-3. Test results: See Table 1.

[0057] Table 1. Test data of Test Example 1

[0058] Yield strength (MPa) Tensile strength (MPa) Example 1 306.7 398.8 Example 2 302.1 395.2 Example 3 305.5 396.3 Comparative Example 1 294.7 388.5 Comparative Example 2 280.1 369.9 Comparative Example 3 269.5 363.4

[0059] Result analysis: Combining the data in Table 1 and Figure 1 ,Analysis of Example 1-Example 3, it can be seen that the yield strength of the aluminum alloy plate obtained by the present invention (Example 1-Example 3) is as high as 302.1MPa or more, and the tensile strength is as high as 395.2MPa or more.

[0060] Combining the data in Table 1 and Figure 1 , analysis of Example 1 and Comparative Examples 1 to Comparative Examples 3, specifically by comparing Comparative Example 1 with Comparative Example 2, it can be seen that when Mg content is 1.47%, compared with water quenching (Comparative Example 1), quenching with the composite quenching liquid (Comparative Example 2) will cause the yield strength and tensile strength of the obtained aluminum alloy plate to decrease instead of increase.

[0061] This is because, on the one hand, at a Mg content of 1.47% by mass, the stoichiometric ratio of Mg to Si and Zn perfectly meets the requirements for precipitate formation. However, the excessively high cooling rate (>120°C / s) in the high-temperature region (>300°C) leads to an excessively high instantaneous nucleation density of precipitates. However, the subsequent low-temperature region cannot provide sufficient thermal activation energy to promote phase growth, ultimately forming a large number of metastable nanophases (<10nm). Precipitates that are too small are sheared rather than bypassed by dislocations, failing to effectively hinder dislocation motion, leading to a decrease in yield strength. Furthermore, while the composite quenching fluid reduces the cooling rate (<50°C / s) in the low-temperature region (<200°C), the rapid cooling in the high-temperature region (>300°C) induces stress concentration within the matrix. In the 1.47% Mg system, the residual stress is insufficiently released, inducing microcracks to propagate preferentially along grain boundaries, resulting in a decrease in tensile strength. On the other hand, potassium nitrate in the composite quenching liquid inhibits grain boundary segregation by adsorbing free Mg atoms. However, at 1.47% Mg, the total amount of dissolved Mg is close to equilibrium. The adsorption effect causes a sudden drop in the dissolved Mg concentration in local areas, destroying the coherent strain strengthening effect of the matrix.

[0062] Specifically, by comparing Comparative Example 1 and Comparative Example 3, it can be seen that during water quenching, compared with 1.47% Mg (Comparative Example 1), excessive 1.9% Mg (Comparative Example 3) will cause the yield strength and tensile strength of the obtained aluminum alloy plate to decrease instead of increase.

[0063] This is because the molar ratio of Mg to Si (2:1) and the molar ratio of Zn to Mg (2:1) require precise control. If Mg is excessive, the unreacted Mg cannot form the Mg2Si / MgZn2 precipitate phase and instead remains in the matrix as solid solution atoms. If its solid solution concentration exceeds the critical value, it will lead to excessive accumulation of lattice distortion, which in turn causes microcracks and a decrease in interfacial bonding, resulting in a decrease in strength. Excess Mg also interferes with the formation dynamics of the precipitate phase, causing the precipitate phase particles to coarsen or become unevenly distributed, weakening its efficiency in pinning dislocations and reducing the strengthening effect.

[0064] By comparison with Example 1, it can be seen that when the mass fraction of Mg is 1.9%, quenching with the composite quenching liquid of the present invention can produce a synergistic effect and synergistically improve the yield strength and tensile strength of the obtained aluminum alloy plate.

[0065] This is because the composite quenching liquid has a cooling rate of >120°C / s in the high-temperature zone (>300°C), allowing Mg to quickly combine with Si and Zn to form high-density Mg2Si and MgZn2 nano-precipitates (size 15–30nm). This high-speed cooling also suppresses the coarsening of the precipitates, increasing their volume fraction. The composite quenching liquid has a cooling rate of <50°C / s in the low-temperature zone (<200°C), avoiding local stress concentration and grain boundary embrittlement caused by rapid cooling. Combined with the high-density nano-precipitates in the high-temperature zone, this creates a uniform stress distribution and reduces the probability of crack initiation.

[0066] When Mg is excessive, potassium nitrate in the composite quenching liquid adsorbs free Mg atoms. On the one hand, it regulates the solid solution concentration, reduces the lattice distortion stress, and retains the coherent strain strengthening effect; on the other hand, it limits the grain boundary segregation, compresses the PFZ width, and improves the grain boundary strength.

[0067] Rapid cooling (>120℃ / s) can also convert excess Mg into high-density nano-precipitates, breaking through the limits of traditional solid solution strengthening; slow cooling (<50℃ / s) reduces residual stress; combined with the nitrate adsorption effect, a synergistic enhancement effect of precipitation phase strengthening and stress optimization is achieved, thereby synergistically improving the yield strength and tensile strength of the obtained aluminum alloy plate.

[0068] Test Example 2: Test Item: Salt spray test. Corrosion rate was measured according to ASTM (American Society for Testing and Materials) B117-09 salt spray test standard. Test Subject: Aluminum alloy plate specimens prepared in Examples 1-3 and Comparative Example 4. Test Results: See Table 2.

[0069] Table 2. Test data of Test Example 2

[0070] Corrosion rate (mm / year) Example 1 0.045 Example 2 0.047 Example 3 0.044 Comparative Example 4 0.069

[0071] Result analysis: According to the analysis of Examples 1 to 3 and the data in Table 2, it can be seen that the corrosion rate of the aluminum alloy plates prepared in the present invention (Examples 1 to 3) is tested with reference to the ASTM (American Society for Testing and Materials) B117-09 salt spray test standard, and the corrosion rate is as low as below 0.047 mm / year.

[0072] From the analysis of Example 1 and Comparative Example 4 and the data in Table 2, it can be seen that deleting the chemical components Mn and Cu from the ingredients will lead to an accelerated corrosion rate of the aluminum alloy plate.

[0073] Although the present invention has been described in detail with reference to the aforementioned embodiments, it is still possible for those skilled in the art to modify the technical solutions described in the aforementioned embodiments, or to make equivalent substitutions for some of the technical features therein. Any modifications, equivalent substitutions, improvements, etc. made within the spirit and principles of the present invention should be included in the scope of protection of the present invention.

Claims

1. A method for preparing a high-strength, corrosion-resistant aluminum alloy plate, characterized in that: The steps include: S1. The ingredients are prepared based on the chemical composition of the high-strength and corrosion-resistant aluminum alloy plate, which is calculated by mass percentage as follows: Si: 0.8-0.9%, Mg: 1.8-2.0%, Zn: 0.13-0.19%, Mn: 0.4-0.6%, Zr: 0.05-0.1%, Ti: 0.05-0.15%, Cu: 0.04-0.08%, Fe≤0.4%, and the balance is Al and unavoidable impurities; S2. Melting under argon protection and casting into ingots with a thickness of 200-300 mm; S3, after homogenizing the ingot, hot rolling it to a plate thickness of 6-8 mm, and then cold rolling it to a plate thickness of 2-4 mm to obtain a final plate; S4, performing a solution treatment on the final plate, and then performing a quenching treatment using a composite quenching liquid; the composite quenching liquid comprises, by mass percentage, 5-6% potassium nitrate and 14-17% PAG, with the balance being water; S5. Aging treatment is performed to obtain the high-strength and corrosion-resistant aluminum alloy plate.

2. The method for preparing a high-strength, corrosion-resistant aluminum alloy plate according to claim 1, wherein: In S3, the specific operation of the homogenization treatment is: keeping warm at 540-560°C for 8-12 hours.

3. The method for preparing a high-strength, corrosion-resistant aluminum alloy plate according to claim 1, wherein: In S3, the specific operation of hot rolling is: starting rolling temperature 480-500°C, and finishing rolling temperature ≥350°C.

4. The method for preparing a high-strength, corrosion-resistant aluminum alloy plate according to claim 1, wherein: In S3, the specific operation of cold rolling is: two-stage rolling, with annealing at 300°C for 2h in the middle.

5. The method for preparing a high-strength, corrosion-resistant aluminum alloy plate according to claim 1, wherein: In S4, the specific operation of the solution treatment is: placing the final plate in a roller hearth furnace, heating to 530-550° C., and keeping the temperature for 30-50 minutes.

6. The method for preparing a high-strength, corrosion-resistant aluminum alloy plate according to claim 1, wherein: In S4, the cooling rate of the quenching treatment includes: a cooling rate of >120°C / s in a high temperature zone of >300°C, and a cooling rate of <50°C / s in a low temperature zone of <200°C.

7. The method for preparing a high-strength, corrosion-resistant aluminum alloy plate according to claim 1, characterized in that: In S5, the specific operation of the aging treatment is: first, keep the temperature at 80-100°C for 7-8 hours, and then keep the temperature at 160-180°C for 8-12 hours.

8. A high-strength, corrosion-resistant aluminum alloy plate, characterized in that: The method is as described in any one of claims 1 to 7.

9. The high-strength, corrosion-resistant aluminum alloy plate according to claim 8, characterized in that: The yield strength of the high-strength and corrosion-resistant aluminum alloy plate is greater than 302 MPa, and the tensile strength is greater than 395 MPa.

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