Asynchronous rolling process method for high-strength and high-toughness Al-Cu-Mg-Ag alloy plate

Abstract

The invention discloses an asynchronous rolling process method of a high-strength and high-toughness Al-Cu-Mg-Ag alloy plate, which comprises the following steps: carrying out multi-pass asynchronous hot rolling on an Al-Cu-Mg-Ag alloy ingot to obtain a hot-rolled plate, carrying out annealing treatment on the hot-rolled plate to obtain an annealed part, and carrying out multi-pass asynchronous cold rolling on the annealed part to obtain a cold-rolled plate, and finally, the cold-rolled plate is sequentially subjected to solution treatment and aging treatment, and the high-strength and high-toughness Al-Cu-Mg-Ag alloy plate is obtained. According to the method, the initial cast ingot is directly subjected to asynchronous rolling forming, the morphology of a primary phase is remarkably improved, the content of Cu atoms in an aluminum solid solution is increased, the microstructure is regulated and controlled through plastic deformation and heat treatment process adjustment, and then the strength of the alloy plate is remarkably improved.

Description

Technical Field

[0001] The invention belongs to the technical field of Al-Cu-Mg-Ag alloy plate preparation, and specifically relates to an asynchronous rolling process method for a high-strength and high-toughness Al-Cu-Mg-Ag alloy plate. Background Art

[0002] With the continuous development of aerospace vehicles, higher requirements are placed on the performance and manufacturing technology of alloy parts. First, as the speed of the aircraft increases, the temperature of the fuselage skin after friction in the air during flight increases, even exceeding 200°C, so aluminum alloy materials need to meet the requirements of long-term use at a certain high temperature. Second, as aerospace engineering parts are developing towards high comprehensive performance, lightweight, integration, and structural and functional integration, the structure of parts is becoming more and more complex. Traditional casting, plastic processing, machining, and welding are obviously difficult to meet the requirements of manufacturing technology. Therefore, it is necessary to seek innovation in manufacturing technology.

[0003] By controlling the Fe and Si impurity content in the alloy and adjusting the solute element content, the United States has developed alloys such as 2124, 2048 and 2524. However, the operating temperature of these alloys is generally below 150°C, which still cannot meet the thermal stability requirements of high-speed aircraft materials. The industry is eager to obtain a new high-strength and heat-resistant aluminum alloy for casting.

[0004] In order to improve the heat resistance of aluminum alloys, people have developed a series of high-strength heat-resistant aluminum alloys that can be prepared by traditional metallurgical casting methods by trying alloying design, spray deposition, mechanical alloying and powder metallurgy. In terms of alloying, the mechanical properties and corrosion resistance of the alloy are improved mainly by adding trace transition elements and rare earth elements such as Ag, Ti, and Zr to the Al-Cu-Mg alloy.

[0005] During the alloying research, it was found that adding trace amounts of Ag can promote the aging strengthening of all Mg-containing aluminum alloys. Al-Cu-Mg-Ag alloy is a new type of material developed based on Al-Cu-Mg alloys. It precipitates a Phase, when aged below 250°C, the thickness of the precipitated phase changes very little and has excellent thermal stability.

[0006] Al-Cu-Mg-Ag alloy is a heat-resistant aluminum alloy obtained by adding trace Ag to Al-Cu-Mg alloy. It was first discovered by Polmear and Vietz in the 1960s. After adding trace Ag elements, the aging precipitation behavior of Al-Cu-Mg alloy changes. After artificial aging, the alloy changes in {111} A new type of strengthening phase Ω phase is precipitated on the surface. This strengthening phase has good thermal stability and can effectively improve the high temperature performance of the alloy, so that the alloy still has high strength even at 200°C. Therefore, Al-Cu-Mg Ag alloy can meet the heat resistance requirements of high-speed aircraft components, and the era of large-scale application of this alloy has also begun.

[0007] Al-Cu-Mg-Ag alloy is developed by adding appropriate amount of Mg (0.4-0.5%) and trace amount of Ag (0.4%) to 2219 alloy (Al-Cu-Mn). Its yield strength in T6 state (close to 500MPa) is nearly 200MPa and 100MPa higher than that of T6 state and T87 state 2219 alloy, respectively. Summary of the invention

[0008] In view of the shortcomings of the prior art in improving the strength of Al-Cu-Mg-Ag alloy, the purpose of the present invention is to provide an asynchronous rolling process method for high-strength and high-toughness Al-Cu-Mg-Ag alloy plates. The process method provided by the present invention, through a method combining an adaptive asynchronous rolling process and a heat treatment process, regulates the primary AlCu phase in the Al-Cu-Mg-Ag alloy ingot to dissolve as fully as possible in the aluminum matrix to inhibit the formation of a large amount of second phases, promotes the solid solubility of the Cu element in the aluminum matrix, and obtains a higher volume fraction of the aging precipitation phase during the aging process, significantly increases its contribution to strength, and achieves a significant improvement in the strength and toughness of the Al-Cu-Mg-Ag alloy.

[0009] In order to achieve the above object, the present invention adopts the following technical solution:

[0010] The invention provides an asynchronous rolling process method for a high-strength and high-toughness Al-Cu-Mg-Ag alloy plate, comprising the steps of performing multiple asynchronous hot rolling on an Al-Cu-Mg-Ag alloy ingot to obtain a hot-rolled plate, performing annealing on the hot-rolled plate to obtain an annealed piece, performing multiple asynchronous cold rolling on the annealed piece to obtain a cold-rolled plate, and finally performing solution treatment and aging treatment on the cold-rolled plate in sequence to obtain the high-strength and high-toughness Al-Cu-Mg-Ag alloy plate.

[0011] The process method of the present invention directly performs multiple asynchronous hot rolling on the Al-Cu-Mg-Ag alloy ingot. Since the elastic constant and deformation behavior of the coarse phase and the Al matrix in the ingot are not coordinated, stress concentration occurs during the deformation process. When the stress concentration is greater than a critical value, the coarse phase cracks and breaks into fine particles. The fine phase with a larger curvature radius (i.e., higher surface energy) is more easily dissolved than the coarse phase, and forms dynamic dissolution during the multiple hot rolling processes, which plays a role in dissolving the coarse phase and inhibiting the formation of the Ag-rich second phase. After the asynchronous hot rolling, annealing treatment is performed to promote the partial residual low-melting point primary phase during the hot rolling process. The phase is further dissolved, which promotes the uniform distribution of solute atoms and improves the plastic deformation ability during asynchronous cold rolling. Subsequently, multiple asynchronous cold rolling is carried out to further effectively break the Cu-rich second phase through the rapid accumulation of deformation energy storage, forming high-density dislocations, etc., providing a favorable channel for rapid atomic diffusion and improving the effect of Cu atoms dissolving back into the Al matrix during the solid solution insulation process. Then, the solid solution heat treatment is used to fully dissolve the second phase in the cold-rolled plate into the aluminum matrix to obtain a supersaturated solid solution. Finally, through aging treatment, a fine strengthening phase with uniform distribution and high volume fraction is obtained during the aging process, which significantly improves the strength of the alloy.

[0012] In the present invention, the Al-Cu-Mg-Ag alloy ingot does not need to be subjected to homogenization annealing treatment, but is directly hot rolled. The inventors have found that if homogenization annealing treatment is performed before hot rolling, the coarse Cu-rich second phase will further agglomerate to the grain boundary at high temperature, forming a coarse second phase that is difficult to fully break during the subsequent hot rolling process. On the one hand, these coarse second phases are prone to cracking during the rolling process, resulting in a decrease in toughness; on the other hand, the Cu solute atoms required for the precipitation of the strengthening phase during the subsequent solution aging heat treatment will be insufficient, resulting in insufficient strength.

[0013] The process of the present invention is applicable to all Al-Cu alloys, and therefore is not limited to the composition of the Al-Cu-Mg-Ag alloy. However, the inventors have found that the process of the present invention can make greater improvements to the Al-Cu-Mg-Ag alloys with the following compositions, ultimately obtaining better performance.

[0014] In a preferred embodiment, the Al-Cu-Mg-Ag alloy ingot is composed of the following by mass percentage: Cu: 2.50-5.5%, Mg: 0.3-1.2%, Ag: 0.20-0.8%, Mn: 0.30-0.50%, Zn: 0.20-0.5%, Sc: 0.05-0.20%, Zr: 0.1-0.30%, and the balance is Al. The preferred alloy composition is based on forming a minimum amount of Ag-containing Cu-rich second phase, whose Ag content is less than 1.0wt.%; while forming as many Ω-strengthening precipitation phases as possible (whose main component is Al2Cu), and the designed Cu content is higher than 2.0wt.%. For this type of alloy, the effect of improving strength and toughness by directly performing asynchronous hot rolling on the ingot can be better reflected: on the one hand, the smaller proportion of the Ag-containing Cu-rich second phase will weaken the tendency of hot-rolled thin plates to crack, and the toughness of the prepared thin plates will be higher; on the other hand, more Cu solute atoms will promote the formation of more Ω-strengthening precipitation phases, significantly improving the strength of the Al-Cu-Mg-Ag alloy thin plates after solid solution aging.

[0015] When the linear speeds of the upper and lower rollers are not equal during asynchronous rolling, the neutral point positions of the upper and lower rollers will move in opposite directions, and the neutral point of the faster roller will move toward the plate discharge port, while the neutral point of the slower roller will move toward the plate feed port. In this way, a "rubbing zone" with opposite surface friction will be formed between the upper and lower rollers, causing the stress state of the initial alloy material to change during the rolling deformation process. In addition to the compressive stress in the vertical direction, it is subjected to shear stress in the horizontal direction parallel to the plate surface. In this way, the rolled plate will produce compressive strain and shear strain at the same time. By setting process parameters such as the deformation temperature of the roller, the pass reduction, the speed ratio and the roller offset, a certain shear strain tensor can be introduced to regulate the evolution of the texture and grain boundary characteristics in the deformation area.

[0016] In a preferred embodiment, the process of the multi-pass asynchronous hot rolling is as follows: first, the Al-Cu-Mg-Ag alloy ingot is preheated at 460°C-500°C, preferably 480-490°C for 1h-10h, preferably 3h-4h, and then multi-pass asynchronous hot rolling is performed, the rolling reduction of a single pass is controlled to be 12%-15%, and the total reduction is 85%-90%; and the temperature is kept at 460°C-500°C for 10min-30min between passes.

[0017] The inventors found that controlling the reduction of each pass between 12% and 15% and keeping warm for 10-30 minutes after each pass can avoid dislocation accumulation and cause local microcracks in the ingot, ensuring the quality of the rolled plate. In addition, hot rolling deformation can break up the primary phase to a certain extent and introduce a certain amount of deformation energy storage.

[0018] According to a preferred solution, during the multi-pass asynchronous hot rolling, the speed ratio of the upper and lower rollers is 1.2-1.6, preferably 1.4; and the offset of the upper and lower rollers is 2mm-6mm, preferably 4mm.

[0019] Compared with the conventional asynchronous rolling process method with upper and lower rollers at different speeds, the present invention introduces the offset of the upper and lower rollers. The main purposes are twofold: on the one hand, the thin plate prepared in the rolling process with upper and lower rollers at different speeds will have obvious warping, and the degree of warping is related to the speed ratio of the upper and lower rollers. Setting a certain range of upper and lower roller horizontal offset can introduce lateral shear stress from a mechanical point of view to balance the warping of the thin plate during the rolling process; on the other hand, the shear stress introduced by the offset of the upper and lower rollers can significantly improve the grain orientation of the thin plate, forming a grain orientation biased towards {111} Al The texture orientation of the dislocation slip plane, this type of crystal oriented aluminum alloy material has higher strength and toughness effects.

[0020] However, the offset of the upper and lower rollers needs to be controlled within the scope of the present invention. If the offset of the upper and lower rollers is too small, the warping of the plate cannot be balanced and the prepared thin plate is uneven; if the offset of the upper and lower rollers is too large, the plate will form a significant wavy shape and cannot be corrected.

[0021] In a preferred embodiment, the annealing temperature is 480° C.-530° C., and the annealing time is 1 h-10 h.

[0022] In the present invention, by performing annealing treatment after multiple asynchronous hot rolling, the dissolution of some residual low-melting primary phases during the hot rolling process can be further promoted, which is beneficial to the uniform distribution of solute atoms, improves the plastic deformation ability during cold rolling, and prevents overburning during high-temperature solution process.

[0023] Preferably, the reduction per pass of the multi-pass asynchronous cold rolling is 6-9%, and the total reduction is 50%-90%.

[0024] According to a preferred solution, during the multi-pass asynchronous cold rolling, the speed ratio of the upper and lower rollers is 1.8-2.0, and the offset of the upper and lower rollers is 6mm-8mm.

[0025] In the present invention, further through multiple asynchronous cold rolling, deformation energy storage is rapidly accumulated and the Cu-rich second phase is effectively broken, forming high-density dislocations, etc., providing a favorable channel for rapid atomic diffusion, and improving the effect of Cu atoms dissolving back into the Al matrix during the solid solution insulation process. However, in the present invention, during multiple asynchronous cold rolling, the offset of the upper and lower rollers is controlled within the scope of the present invention, and the final alloy sheet has the best performance. If the offset of the upper and lower rollers is too small during asynchronous cold rolling, the warping of the sheet cannot be balanced, and the prepared thin sheet is uneven; and if the offset of the upper and lower rollers is too large, the sheet will form a significant wave shape and cannot be corrected.

[0026] In a preferred embodiment, the temperature of the solution treatment is 520° C.-555° C., the time of the solution treatment is 1 h-3 h, and after the solution treatment is completed, the solution is immediately cooled to room temperature.

[0027] In the present invention, the solution heat treatment allows the second phase in the cold-rolled sheet to be fully dissolved in the aluminum matrix to obtain a supersaturated solid solution, which is beneficial to subsequent aging precipitation.

[0028] In actual operation, the plate after solution treatment is immediately placed in room temperature water for quenching. By rapidly cooling to room temperature, the cooling rate is too low to avoid the formation of coarse second phases, which in turn affects aging precipitation.

[0029] In a preferred solution, pre-deformation is performed before the aging treatment, and the pre-deformation amount is 1-5%, preferably 3-5%.

[0030] Further preferably, the pre-deformation is pre-stretching deformation.

[0031] Pre-deformation can effectively release the residual stress in the quenching process. In addition, the present invention effectively promotes the nucleation of precipitates by introducing dislocations through pre-stretching deformation, further improving the mechanical properties of the material. However, the pre-deformation amount needs to be effectively controlled. If the pre-deformation amount is too small, the dislocation density cannot be effectively introduced, and if the pre-deformation amount is too large, the plasticity of the alloy will be significantly reduced.

[0032] In a preferred embodiment, the aging treatment temperature is 155°C-165°C, and the aging treatment time is 15 h-20 h.

[0033] After the solution treatment, the peak aging treatment is carried out, and the aging treatment temperature is controlled within the above range. The final Al-Cu-Mg-Ag alloy has the highest strength. If the aging temperature is too low, it is not conducive to the precipitation of the main strengthening phase. If the aging temperature is too high, it will accelerate the coarsening of the strengthening phase and reduce the peak hardness.

[0034] Principles and advantages

[0035] The process method of the present invention directly performs multiple hot rolling on the Al-Cu-Mg-Ag alloy ingot. Since the elastic constant and deformation behavior of the coarse phase in the ingot are not coordinated with the Al matrix, stress concentration occurs during the deformation process. When the stress concentration is greater than a critical value, the coarse phase generates cracks and breaks into fine particles. The fine particles with a larger curvature radius (i.e., higher surface energy) are more easily dissolved than the coarse phase, and form dynamic dissolution during the multiple hot rolling processes, which plays a role in dissolving the coarse phase and inhibiting the formation of the coarse secondary phase. After the hot rolling, annealing treatment is performed to promote the residual low-melting-point primary phase in the hot rolling process. Further dissolution promotes uniform distribution of solute atoms and improves plastic deformation capacity during cold rolling. Subsequently, multiple cold rolling passes are carried out to further effectively break up the Cu-rich second phase through rapid accumulation of deformation energy storage, forming high-density dislocations, etc., providing favorable channels for rapid atomic diffusion and improving the effect of Cu atoms dissolving back into the Al matrix during the solution heat preservation process. Solution heat treatment is then used to fully dissolve the second phase in the cold-rolled sheet in the aluminum matrix to obtain a supersaturated solid solution. Finally, aging treatment is performed during the aging process to obtain a uniformly distributed and high-volume-fraction fine strengthening phase, which significantly improves the strength of the alloy.

[0036] The present invention directly performs plastic deformation on the initial ingot, significantly improves the morphology of the primary phase, and increases the content of Cu atoms in the aluminum solid solution. The microstructure is regulated by adjusting the plastic deformation and heat treatment process, thereby significantly improving the strength of the Al-Cu-Mg-Ag alloy. The present invention adjusts the thermomechanical treatment process to eliminate the residual crystalline phase in the alloy ingot to the greatest extent, and significantly improves the toughness of the Al-Cu-Mg-Ag alloy plate. DETAILED DESCRIPTION

[0037] The embodiment of the present invention provides an asynchronous rolling process method for high-strength and high-toughness Al-Cu-Mg-Ag alloy plate. Obviously, the described embodiment is only a part of the embodiment of the present invention, not all of the embodiments. Based on the embodiment 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.

[0038] Example 1

[0039] This embodiment provides an asynchronous rolling process method for high-strength and high-toughness Al-Cu-Mg-Ag alloy plates. The process method comprises the following steps:

[0040] Insulation: The Al-Cu-Mg-Ag alloy ingot (Cu: 3.5%, Mg: 0.75%, Ag: 0.75%, Mn: 0.35%, Zn: 0.30%, Sc: 0.15%, Zr: 0.20%, the balance is Al) was machined on the outer surface and then kept warm in a heat treatment furnace at 490 °C / 2 h.

[0041] Multi-pass asynchronous hot rolling: The ingot after insulation is directly and immediately subjected to multi-pass asynchronous hot rolling to obtain the initial alloy rolled plate. The rolling reduction of a single pass is 13%, the total reduction is 87%, and the insulation between passes is 10 minutes. During asynchronous rolling, the upper and lower roller speed ratio is 1.4, and the upper and lower roller offset is 4mm.

[0042] Annealing: anneal the alloy hot-rolled plate obtained in step ② above at 520℃ / 1h;

[0043] Multi-pass asynchronous cold rolling: The annealed plate is directly subjected to multi-pass asynchronous cold rolling, with a total rolling reduction of 90%. During asynchronous cold rolling, the upper and lower roller speed ratio is 1.8, and the upper and lower roller offset is 8mm.

[0044] Solution aging: The alloy cold-rolled sheet was solution treated at 540 °C for 1 h, immediately quenched in room temperature water, and then artificially aged at 165 °C for 15 h to reach the peak value. The final mechanical properties of the obtained material are shown in Table 1.

[0045] Example 2

[0046] This embodiment provides an asynchronous rolling process method for high-strength and high-toughness Al-Cu-Mg-Ag alloy plates. The process method comprises the following steps:

[0047] Insulation: The Al-Cu-Mg-Ag alloy ingot (Cu: 4%, Mg: 0.9%, Ag: 0.45%, Mn: 0.40%, Zn: 0.30%, Sc: 0.15%, Zr: 0.20%, the balance is Al) was machined on the outer surface and then kept warm in a heat treatment furnace at 490 °C / 2 h.

[0048] Multi-pass asynchronous hot rolling: The ingot after insulation is directly and immediately subjected to multi-pass hot rolling to obtain the initial alloy rolled plate. The rolling reduction of a single pass is 15%, and the total reduction is 87%. The insulation between passes is 10 minutes. During asynchronous rolling, the upper and lower roller speed ratio is 1.2, and the upper and lower roller offset is 6mm.

[0049] Annealing: anneal the alloy hot-rolled plate obtained in step ② above at 520℃ / 1h;

[0050] Multi-pass asynchronous cold rolling: The annealed plate is directly subjected to multi-pass cold rolling, with a total rolling reduction of 90%. During asynchronous rolling, the upper and lower roller speed ratio is 2.0, and the upper and lower roller offset is 6mm.

[0051] Solution aging: The alloy cold-rolled sheet was solution treated at 540 °C for 1 h, immediately quenched in room temperature water, and subjected to 3% pre-stretching deformation, and then artificially aged at 165 °C for 15 h to reach the peak value. The final mechanical properties of the obtained material are shown in Table 1.

[0052] Example 3

[0053] This embodiment provides an asynchronous rolling process method for high-strength and high-toughness Al-Cu-Mg-Ag alloy plates. The process method comprises the following steps:

[0054] Insulation: The outer surface of the Al-Cu-Mg-Ag alloy ingot (Cu: 5%, Mg: 0.8%, Ag: 0.6%, Mn: 0.40%, Zn: 0.30%, Sc: 0.15%, Zr: 0.20%, the balance is Al) was machined and then kept warm in a heat treatment furnace at 490°C / 2 h.

[0055] Multi-pass asynchronous hot rolling: The ingot after insulation is directly and immediately subjected to multi-pass hot rolling to obtain the initial alloy rolled plate. The rolling reduction of a single pass is 12%, and the total reduction is 85%. The insulation between passes is 10 minutes. During asynchronous rolling, the upper and lower roller speed ratio is 1.2, and the upper and lower roller offset is 2mm.

[0056] Annealing: anneal the alloy hot-rolled plate obtained in step ② above at 520℃ / 1h;

[0057] Multi-pass asynchronous cold rolling: The annealed plate is directly subjected to multi-pass cold rolling, with a total rolling reduction of 90%; during asynchronous rolling, the upper and lower roller speed ratio is 1.8, and the upper and lower roller offset is 8mm. ;

[0058] Solution aging: The alloy cold-rolled sheet was solution treated at 540 °C for 1 h, immediately quenched in room temperature water, and subjected to 5% pre-stretching deformation, and then artificially aged at 165 °C for 15 h to reach the peak value. The final mechanical properties of the obtained material are shown in Table 1.

[0059] Comparative Example 1

[0060] The other conditions were the same as those in Example 1, except that a homogenization heat treatment at 510° C. for 48 h was performed before hot rolling.

[0061] Comparative Example 2

[0062] The other conditions are the same as those in Example 1, except that the upper and lower roll speed ratio during asynchronous hot rolling is 2, and the upper and lower roll offset is 8 mm.

[0063] Comparative Example 3

[0064] The other conditions are the same as those in Example 2, except that the upper and lower roller speed ratio during asynchronous cold rolling is 1.5, and the upper and lower roller offset is 10 mm.

[0065] Comparative Example 4

[0066] The other conditions are the same as those in Example 3, except that the rolling reduction in a single pass during asynchronous hot rolling is 20%.

[0067] Performance Tests of Examples and Comparative Examples

[0068] Room temperature mechanical properties test

[0069] The Al-Cu-Mg-Ag alloy plates prepared in Examples 1-3 of the present invention and the Al-Cu-Mg-Ag alloy plates prepared in Comparative Examples 1-4 were tested for mechanical properties on a DDL100 electronic universal testing machine. The mechanical properties of the Al-Cu-Mg-Ag alloy plates obtained in Examples 1-3 and Comparative Examples 1-2 are listed in Table 1. It can be clearly seen from Table 1 that the strength and elongation of the Al-Cu-Mg-Ag alloy plates prepared in this embodiment are higher than those in the comparative example, indicating that the rolling system and heat treatment process adopted in the present invention can significantly improve the mechanical properties of the Al-Cu-Mg-Ag alloy. The strength and toughness of Comparative Example 1 are the worst, indicating that the homogenization heat treatment before hot rolling will cause the segregation of the Cu-rich phase at the grain boundary, which is not conducive to the improvement of strength and toughness; the strength and toughness of Comparative Examples 2 and 3 are lower than those of Examples 2 and 3, indicating that the speed ratio and offset of the hot rolling and cold rolling rolls in asynchronous rolling are improperly set, and the compressive strain and shear strain in the core of the rolled plate are uneven, which is not conducive to performance improvement; the strength of Comparative Example 4 is not much different from that of Example 3, but the toughness (elongation) is significantly lower than that of Example 3, indicating that inappropriate asynchronous hot rolling reduction will cause the plate to have a tendency to crack and a significant decrease in toughness.

[0070]

Claims

1. An asynchronous rolling process for high-strength and high-toughness Al-Cu-Mg-Ag alloy sheet, characterized in that: The Al-Cu-Mg-Ag alloy ingot is subjected to multiple passes of asynchronous hot rolling to obtain a hot-rolled plate, the hot-rolled plate is annealed to obtain an annealed piece, the annealed piece is subjected to multiple passes of asynchronous cold rolling to obtain a cold-rolled plate, and finally the cold-rolled plate is sequentially subjected to solution treatment and aging treatment to obtain a high-strength and high-toughness Al-Cu-Mg-Ag alloy plate.

2. The process for producing a high-strength and high-toughness Al-Cu-Mg-Ag alloy sheet according to claim 1, characterized in that: The Al-Cu-Mg-Ag alloy ingot has the following composition by mass percentage: Cu: 2.50-5.5%, Mg: 0.3-1.2%, Ag: 0.20-0.8%, Mn: 0.30-0.50%, Zn: 0.20-0.5%, Sc: 0.05-0.20%, Zr: 0.1-0.30%, and the balance is Al.

3. The asynchronous rolling process of a high-strength and high-toughness Al-Cu-Mg-Ag alloy sheet according to claim 1 or 2, characterized in that: The process of the multi-pass asynchronous hot rolling is: first preheating the Al-Cu-Mg-Ag alloy ingot at 460°C-500°C for 1h-10h, and then performing multi-pass asynchronous hot rolling, controlling the rolling reduction of a single pass to be 12%-15%, and the total reduction to be 85%-90%; keeping the temperature at 460°C-500°C for 10min-30min between passes.

4. The asynchronous rolling process of a high-strength and high-toughness Al-Cu-Mg-Ag alloy sheet according to claim 1 or 2, characterized in that: During the multi-pass asynchronous hot rolling, the speed ratio of the upper and lower rollers is 1.2-1.6, and the offset of the upper and lower rollers is 2mm-6mm.

5. The asynchronous rolling process of a high-strength and high-toughness Al-Cu-Mg-Ag alloy sheet according to claim 1 or 2, characterized in that: The annealing temperature is 480° C.-530° C., and the annealing time is 1 h-10 h.

6. The asynchronous rolling process of a high-strength and high-toughness Al-Cu-Mg-Ag alloy sheet according to claim 1 or 2, characterized in that: The reduction per pass of the multi-pass asynchronous cold rolling is 6-9%, and the total reduction is 50%-90%; during the multi-pass asynchronous cold rolling, the speed ratio of the upper and lower rollers is 1.8-2.0, and the offset of the upper and lower rollers is 6mm-8mm.

7. The asynchronous rolling process of a high-strength and high-toughness Al-Cu-Mg-Ag alloy sheet according to claim 1 or 2, characterized in that: The temperature of the solution treatment is 520° C.-555° C., the time of the solution treatment is 1 h-3 h, and after the solution treatment is completed, it is immediately water-cooled to room temperature.

8. The asynchronous rolling process of a high-strength and high-toughness Al-Cu-Mg-Ag alloy sheet according to claim 1 or 2, characterized in that: Before the aging treatment, pre-deformation is performed, and the pre-deformation amount is 1-5%.

9. The asynchronous rolling process of a high-strength and high-toughness Al-Cu-Mg-Ag alloy sheet according to claim 8, characterized in that: The pre-deformation is pre-stretching deformation.

10. The asynchronous rolling process of a high-strength and high-toughness Al-Cu-Mg-Ag alloy sheet according to claim 1 or 2, characterized in that: The temperature of the aging treatment is 155°C-165°C, and the time of the aging treatment is 15 h-20 h.

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