6xxx series aluminum alloy material and preparation method and application thereof

Abstract

The present application relates to the technical field of aluminum alloy material processing, and particularly relates to a 6xxx series aluminum alloy material, a preparation method and application thereof. The present application can effectively promote alloy element dissolution, inhibit coarse phase precipitation, and optimize the morphology and distribution of precipitated phases by specific heat treatment combined with other steps, so as to ensure the strength of the 6xxx series aluminum alloy material while significantly improving its stress corrosion resistance, and make its comprehensive performance excellent. The 6xxx series aluminum alloy material provided by the present application can meet the performance requirements of high-end equipment manufacturing on structural materials, and is specifically applied to scenes such as photovoltaic equipment, intelligent robot skeleton frame, AR / VR glasses or folding screen mobile phone hinge, etc., and is controllable in cost, and has remarkable economic and social benefits.

Description

Technical Field

[0001] This invention relates to the field of aluminum alloy material processing technology, and in particular to a 6xxx series aluminum alloy material, its preparation method and application. Background Technology

[0002] 6xxx series aluminum alloys are commonly used heat-treatable Al-Mg-Si alloys, widely applied in various fields due to their excellent comprehensive properties. However, the manufacturing of cutting-edge equipment (such as CVD equipment, etching machines and other photovoltaic equipment, intelligent robot skeleton frames, AR / VR glasses, foldable screen phone hinges, etc.) places extremely stringent requirements on the performance of structural materials such as 6xxx series aluminum alloys. These advanced devices not only require 6xxx series aluminum alloys to possess the necessary mechanical strength and excellent machinability, but also require them to have extremely high corrosion resistance, long service life, and excellent batch-to-batch quality consistency and microstructure uniformity to adapt to complex and long-term working environments.

[0003] Traditional methods for preparing 6xxx series aluminum alloys often employ T6 heat treatment (solution treatment + single-stage artificial aging). While this can achieve high strength, it often leads to a decrease in corrosion resistance, particularly stress corrosion resistance. To balance the strength and corrosion resistance of 6xxx series aluminum alloys, multi-stage aging is an effective approach. However, precisely controlling the process parameters at each stage and achieving optimal matching with upstream preparation processes (such as casting and rolling) to obtain 6xxx series aluminum alloys with stable and excellent overall performance remains a challenge for those skilled in the art. Summary of the Invention

[0004] In view of this, the present invention provides a 6xxx series aluminum alloy material, its preparation method and application. The preparation method provided by the present invention can balance the strength and corrosion resistance of the 6xxx series aluminum alloy material, and the obtained 6xxx series aluminum alloy material has excellent comprehensive performance.

[0005] This invention provides a method for preparing 6xxx series aluminum alloy materials, comprising the following steps:

[0006] The aluminum alloy ingot is subjected to homogenization, milling, hot rolling, solution treatment and aging treatment in sequence to obtain the 6xxx series aluminum alloy material; the solution treatment temperature is 500~550 degrees Celsius; the aging treatment is a graded aging treatment; the graded aging treatment includes pre-aging, over-aging and stabilization aging performed in sequence.

[0007] Preferably, the pre-aging temperature is 100-150 degrees Celsius, and the holding time is 0.5-8 hours; the over-aging temperature is 200-250 degrees Celsius, and the holding time is 0.5-8 hours; the stabilization aging temperature is 150-200 degrees Celsius, and the holding time is 0.5-5 hours; the holding time of the pre-aging is not longer than the holding time of the over-aging; and the holding time of the stabilization aging is not longer than half of the holding time of the over-aging.

[0008] Preferably, the hot rolling includes a first hot rolling and a second hot rolling performed sequentially; the temperature of the first hot rolling is 440~470 degrees Celsius, and the holding time is 0.5~6 hours; the temperature of the second hot rolling is 250~320 degrees Celsius, and the holding time of the second hot rolling is determined by the conveying speed, which is 8~25m / s.

[0009] Preferably, the target thickness of the hot-rolled sheet is 5 to 50 millimeters.

[0010] Preferably, the heat preservation time of the solution treatment is determined according to the thickness of the hot-rolled plate: when the plate thickness is less than 25mm, the heat preservation time is 2.5 hours; when the plate thickness is greater than 25mm, the heat preservation time is extended by 0.1 hours for every 1mm increase in plate thickness, based on the standard of 2.5 hours.

[0011] Preferably, the solution treatment further includes quenching the resulting product; the quenching cooling rate is not less than 100°C / s.

[0012] Preferably, the temperature for heat equalization is 540-570 degrees Celsius, and the heat preservation time is 6-12 hours.

[0013] Preferably, the aluminum alloy ingot is a 6xxx series aluminum alloy.

[0014] The present invention also provides 6xxx series aluminum alloy materials obtained by the preparation method described above.

[0015] This invention also provides the application of the 6xxx series aluminum alloy material described above in the field of high-end equipment manufacturing.

[0016] This invention provides a method for preparing 6xxx series aluminum alloy materials. Through specific heat treatment combined with other steps, this invention effectively promotes the dissolution of alloying elements, inhibits the precipitation of coarse phases, and optimizes the morphology and distribution of precipitated phases. This significantly improves the stress corrosion resistance of the 6xxx series aluminum alloy material while maintaining its strength, resulting in excellent overall performance. The specific mechanism and beneficial effects of this invention are as follows:

[0017] 1) Solution quenching control: This invention ensures the full dissolution of the main strengthening phase Mg2Si by precisely controlling the solution temperature at 500~550℃ and combining it with a reasonable holding time, while avoiding overheating; and by using a high cooling rate of ≥100℃ / s, the precipitation of coarse and brittle phases such as β-AlFeSi during the quenching process is effectively suppressed, laying the foundation for subsequent aging treatment.

[0018] 2) Synergistic Staged Aging System: This invention employs a three-stage aging process: pre-aging, over-aging, and stabilization aging. Pre-aging forms a high-density atomic segregation structure (GP region), providing ample nucleation sites for subsequent precipitation. Over-aging promotes moderate coarsening and spheroidization of the precipitated phase, reducing grain boundary continuity, which is crucial for improving corrosion resistance. Stabilization aging further eliminates internal stress and reduces stress corrosion sensitivity. The synergistic effect of these three processes achieves a good balance between strength and stress corrosion resistance.

[0019] 3) Complete process chain matching: This invention systematically matches and controls the aluminum alloy composition, ingot homogenization, hot rolling to solution treatment and aging treatment. The parameters of each step are interrelated and mutually supportive, which together ensure the stability and superior performance of 6xxx series aluminum alloy materials.

[0020] This invention also provides 6xxx series aluminum alloy materials obtained by the preparation method described above. The 6xxx series aluminum alloy materials provided by this invention exhibit excellent overall performance in terms of strength and corrosion resistance, and have broad application prospects.

[0021] This invention also provides the application of the 6xxx series aluminum alloy material described above in the field of high-end equipment manufacturing. The 6xxx series aluminum alloy material provided by this invention can meet the performance requirements of structural materials in high-end equipment manufacturing. Specific applications include photovoltaic equipment, intelligent robot skeletal frames, AR / VR glasses, or hinges for foldable screen phones, etc., and the cost is controllable, resulting in significant economic and social benefits. Attached Figure Description

[0022] To more clearly illustrate the technical solutions of this invention, the accompanying drawings used in the embodiments of this invention or in the prior art are briefly described below. For those skilled in the art, other drawings can be derived from the following drawings without creative effort, and all such drawings are within the protection scope of this invention.

[0023] Figure 1 Nyquist plot and equivalent circuit diagram of the 6xxx series aluminum alloy materials prepared in Example 1 and Comparative Examples 1-2; wherein, (a) is the Nyquist plot and (b) is the equivalent circuit diagram;

[0024] Figure 2The images show the grain boundary distribution of the 6xxx series aluminum alloy materials prepared in Examples 1 and Comparative Examples 1-2; wherein, (a) is the grain boundary distribution of the 6xxx series aluminum alloy material prepared in Comparative Example 1, (b) is the grain boundary distribution of the 6xxx series aluminum alloy material prepared in Comparative Example 2, (c) is the grain boundary distribution of the 6xxx series aluminum alloy material prepared in Example 1, (d) is the transmission grain boundary diagram of the 6xxx series aluminum alloy material prepared in Example 1, (e) is the transmission grain boundary diagram of the 6xxx series aluminum alloy material prepared in Comparative Example 1, and (f) is the transmission grain boundary diagram of the 6xxx series aluminum alloy material prepared in Comparative Example 2.

[0025] Figure 3 A schematic diagram of the process flow for the preparation method of 6xxx series aluminum alloy materials provided by the present invention;

[0026] Figure 4 The microstructure diagrams are of the homogenized products obtained in Examples 1 and Comparative Examples 4-5, and the aluminum alloy ingot of Comparative Example 3; wherein, (a) is the microstructure diagram of the aluminum alloy ingot of Comparative Example 3, (b) is the microstructure diagram of the homogenized product of Comparative Example 4, (c) is the microstructure diagram of the homogenized product of Comparative Example 5, (d) is the microstructure diagram of the homogenized product obtained in Example 1 after homogenization for 5 hours, and (e) is the microstructure diagram of the homogenized product obtained in Example 1 after homogenization for 10 hours. Detailed Implementation

[0027] This invention provides a method for preparing 6xxx series aluminum alloy materials, comprising the following steps:

[0028] The aluminum alloy ingot is subjected to homogenization, milling, hot rolling, solution treatment and aging treatment in sequence to obtain the 6xxx series aluminum alloy material.

[0029] In this invention, the aluminum alloy ingot is preferably a 6xxx series aluminum alloy; the 6xxx series aluminum alloy preferably includes a 6061 aluminum alloy ingot.

[0030] In this invention, the temperature for heat equalization is preferably 540-570 degrees Celsius, more preferably 550-565 degrees Celsius, and even more preferably 560 degrees Celsius. The heat preservation time is preferably 6-12 hours, more preferably 8-11 hours, and even more preferably 10 hours.

[0031] In this invention, the process of homogenizing the product preferably includes cooling the product before milling; the cooling is preferably air cooling.

[0032] In this invention, there are no special requirements for the milling method; conventional methods in the art can be used. This invention removes the oxide layer and defects from the material surface through milling.

[0033] In this invention, the hot rolling preferably includes a first hot rolling and a second hot rolling performed sequentially; the temperature of the first hot rolling is preferably 440~470 degrees Celsius, more preferably 450~460 degrees Celsius, and even more preferably 455 degrees Celsius, and the holding time is preferably 0.5~6 hours, more preferably 1~5 hours, and even more preferably 2~4 hours.

[0034] In this invention, the temperature of the second hot rolling is preferably 250~320 degrees Celsius, more preferably 270~300 degrees Celsius, and even more preferably 280 degrees Celsius; the equipment for the second hot rolling preferably includes a rolling mill and a conveyor belt, the conveyor belt being used to transport the milled aluminum alloy ingot to the rolling mill, and by controlling the conveying speed of the conveyor belt, the dwell time of the milled aluminum alloy ingot in the rolling mill can be directly controlled; the holding time of the second hot rolling is determined by the conveying speed; the conveying speed is preferably 8~25 m / s, more preferably 10~20 m / s, and even more preferably 15~18 m / s.

[0035] In this invention, the target thickness of the hot-rolled sheet is preferably 5 to 50 mm, more preferably 10 to 40 mm, and even more preferably 20 to 30 mm.

[0036] In this invention, the solution treatment temperature is preferably 500-550 degrees Celsius, more preferably 510-540 degrees Celsius, and even more preferably 520-530 degrees Celsius. The holding time is preferably determined according to the thickness of the hot-rolled plate: when the plate thickness is less than 25 mm, the holding time is 2.5 hours; when the plate thickness is greater than 25 mm, the holding time is extended by 0.1 hours for every 1 mm increase in plate thickness, based on the standard of 2.5 hours (for example, when the plate thickness is 30 mm, the solution treatment holding time is 3 hours).

[0037] In this invention, the solution treatment preferably further includes quenching the resulting product; the quenching agent used for quenching is preferably water; the temperature of the water is preferably 20~40 degrees Celsius; the quenching is preferably carried out under stirring conditions; and the cooling rate of the quenching is preferably not less than 100°C / s.

[0038] In this invention, the aging process is preferably a graded aging process; the graded aging process preferably includes pre-aging, over-aging and stabilization aging performed sequentially.

[0039] In this invention, the pre-aging temperature is preferably 100-150 degrees Celsius, more preferably 120-130 degrees Celsius, and the heat preservation time is preferably 0.5-8 hours, more preferably 1-6 hours, and even more preferably 3-4 hours.

[0040] In this invention, the over-aging temperature is preferably 200-250 degrees Celsius, more preferably 220-240 degrees Celsius, and even more preferably 230 degrees Celsius. The heat preservation time is preferably 0.5-8 hours, more preferably 1-6 hours, and even more preferably 3-5 hours.

[0041] In this invention, the stabilization aging temperature is preferably 150-200 degrees Celsius, more preferably 160-190 degrees Celsius, and even more preferably 170-180 degrees Celsius, and the heat preservation time is preferably 0.5-5 hours, more preferably 1-4 hours, and even more preferably 2-3 hours.

[0042] In this invention, the pre-aging holding time is preferably no longer than the over-aging holding time; the stabilization aging holding time is preferably no longer than half of the over-aging holding time.

[0043] In this invention, the role of pre-aging is to form GP region nanoclusters, providing nucleation sites for subsequent precipitated phases; the role of over-aging is to coarsen and spheroidize the Mg2Si and Al2Cu phases; and the role of stabilizing aging is to eliminate residual stress.

[0044] The process flow of the preparation method of 6xxx series aluminum alloy materials provided by this invention is as follows: Figure 3 As shown, this invention involves sequentially subjecting an aluminum alloy ingot to homogenization, milling, hot rolling, solution treatment, and aging treatment. The aging treatment is a staged aging process, including sequential pre-aging, over-aging, and stabilization aging, to obtain 6xxx series aluminum alloy materials. This invention, through the aforementioned aging treatment, yields 6xxx series aluminum alloy materials with excellent performance. The preparation method provided by this invention is simple in steps, convenient to operate, and has good process stability, possessing the potential for industrial production.

[0045] The present invention also provides 6xxx series aluminum alloy materials obtained by the preparation method described above.

[0046] The 6xxx series aluminum alloy material provided by this invention has excellent strength and corrosion resistance, and its comprehensive performance is promising.

[0047] This invention also provides the application of the 6xxx series aluminum alloy material described above in the field of high-end equipment manufacturing.

[0048] The 6xxx series aluminum alloy material provided by this invention can meet the performance requirements of high-end equipment manufacturing for structural materials. Specific application scenarios include photovoltaic equipment, intelligent robot skeleton frames, AR / VR glasses or hinges for foldable screen mobile phones, etc., and the cost is controllable, with significant economic and social benefits.

[0049] To further illustrate the present invention, the technical solutions of the present invention will be clearly and completely described below with reference to the accompanying drawings and embodiments.

[0050] Example 1:

[0051] This embodiment prepares a 6xxx series aluminum alloy material, and the process flow is as follows: Figure 3 As shown, the specific steps are as follows:

[0052] 1) The 6061 aluminum alloy ingot produced by semi-continuous casting has a size of 520mm×1480mm×6000mm. After sawing off the head and tail, a 6061 aluminum alloy ingot with a size of 520mm×1480mm×5500mm is obtained.

[0053] 2) The obtained 6061 aluminum alloy ingot was placed in a soaking furnace and held at 560℃ for 10 hours before being removed from the furnace and cooled. Subsequently, the 6061 aluminum alloy ingot was milled to obtain an ingot billet with dimensions of 490mm×1460mm×5500mm.

[0054] 3) The obtained ingot billet is heated to 450°C in a vertical pusher furnace, held for 5 hours and then taken out of the furnace. It is immediately sent to a hot rolling mill for rolling, held at 455°C for 3 hours, and then rolled into a 15mm thick plate at 300°C to obtain an aluminum alloy slab.

[0055] 4) Cut samples from the obtained aluminum alloy slab and place them in an air-circulating furnace for solution treatment. Set the furnace temperature to 535℃. Once the sample temperature reaches 535℃, start calculating the holding time and hold for 2.5 hours. After the holding time is completed, quickly transfer the sample to a circulating water bath with the temperature controlled between 20~40℃ for quenching. Use a stirring device to agitate the water flow to ensure that the cooling rate of the sample exceeds 100℃ / s.

[0056] 5) Perform graded aging treatment on the quenched samples:

[0057] a. Place the sample in an aging furnace at 110℃ and hold for 7 hours to complete the pre-aging process;

[0058] b. Then, raise the furnace temperature to 210℃ and continue to hold it for 7 hours to complete the aging process;

[0059] c. Then, adjust the furnace temperature to 160℃ and hold for 2 hours to complete the stabilization aging.

[0060] 6) After the aging treatment is completed, the sample is cooled to room temperature in the furnace to obtain 6xxx series aluminum alloy material.

[0061] Comparative Example 1:

[0062] The preparation method of this comparative example is the same as that of Example 1, except that the aging treatment is carried out at 175°C for 3 hours.

[0063] Comparative Example 2:

[0064] The preparation method of this comparative example is the same as that of Example 1, except that the aging treatment is carried out at 175°C for 8 hours.

[0065] Comparative Example 3:

[0066] The 6061 aluminum alloy ingot produced by semi-continuous casting has a size of 520mm×1480mm×6000mm. After sawing off the head and tail, a 6061 aluminum alloy ingot with a size of 520mm×1480mm×5500mm is obtained.

[0067] Comparative Example 4:

[0068] 6061 aluminum alloy ingots with dimensions of 520mm × 1480mm × 6000mm were produced by semi-continuous casting. The ends were sawn off to obtain 6061 aluminum alloy ingots with dimensions of 520mm × 1480mm × 5500mm. The obtained 6061 aluminum alloy ingots were placed in a soaking furnace and held at 530℃ for 5 hours. After cooling, the soaked product was obtained.

[0069] Comparative Example 5:

[0070] 6061 aluminum alloy ingots with dimensions of 520mm × 1480mm × 6000mm were produced by semi-continuous casting. The ends were sawn off to obtain 6061 aluminum alloy ingots with dimensions of 520mm × 1480mm × 5500mm. The obtained 6061 aluminum alloy ingots were placed in a soaking furnace and held at 530℃ for 10 hours. After cooling, the soaked product was obtained.

[0071] Test Example 1:

[0072] The mechanical properties and corrosion resistance of the 6xxx series aluminum alloy materials prepared in Examples 1 and Comparative Examples 1-2 were tested. Examples 2-3 in Tables 1-2 and Examples 2-7 in Table 3 were prepared repeatedly according to Example 1 to test the repeatability and stability of the preparation method of the present invention. The results are shown in Tables 1-3 and 2-7. Figure 1 As shown.

[0073] Table 1. Corrosion resistance of 6xxx series aluminum alloys in Examples 1-3 and Comparative Examples 1-2

[0074]

[0075] Table 2. Corrosion resistance of 6xxx series aluminum alloys in Examples 1-3 and Comparative Examples 1-2

[0076]

[0077] Table 3 Mechanical properties of 6xxx series aluminum alloys in Examples 1-7

[0078]

[0079] Note: Resistors in Table 2 R s Constant phase angle element CPE ,resistance R 1 ,capacitance C and resistance R 2 represents the electronic component symbols in the equivalent circuit, such as... Figure 1 As shown in (b) of the diagram.

[0080] Thermodynamic tendency of corrosion: The more negative the potential, the more active the metal, and the greater the corrosion tendency; the more positive the potential, the smaller the corrosion tendency. Kinetic rate of corrosion: The lower the corrosion current density, the less material loss per unit time, and the better the corrosion resistance; the higher the polarization resistance, the better the corrosion resistance. (Based on Tables 1-3 and...) Figure 1 As can be seen from (a) in the present invention, the 6xxx series aluminum alloy material prepared in the present invention has the best corrosion performance. Its tensile strength and other mechanical properties are comparable to those of aluminum alloy plates treated with traditional T6 heat treatment, but its corrosion resistance is significantly better than that of traditional aluminum alloy plates, and its comprehensive performance is excellent. Furthermore, the preparation method provided by the present invention has good repeatability and stability.

[0081] Test Example 2:

[0082] The grain boundary distribution of the 6xxx series aluminum alloy materials prepared in Example 1 and Comparative Examples 1-2 of this invention was observed, and the results are as follows: Figure 2 As shown.

[0083] according to Figure 2 It can be seen that the grain size of Example 1 is mainly concentrated in the range of 50~200μm, the grain size of Comparative Example 1 is mainly concentrated in the range of 50~300μm, and the grain size of Comparative Example 2 is mainly concentrated in the range of 50~250μm. By controlling the heat treatment, the present invention makes the grain size of Example 1 smaller and more uniformly distributed, while suppressing the formation of coarse precipitates at the grain boundaries, and obtaining fine dispersed precipitates.

[0084] Test Example 3:

[0085] The microstructure of the homogenized products prepared in Example 1 and Comparative Examples 4-5 of this invention, as well as the aluminum alloy ingot of Comparative Example 3, was characterized, and the results are as follows: Figure 4 As shown, the SEM microstructure of 6xxx series aluminum alloys under different homogenization conditions is illustrated. Based on... Figure 4In (a), a typical cast dendritic structure can be clearly observed. Coarse, continuous, and even skeletal or network-like non-equilibrium second phases are distributed between dendrites and at grain boundaries. These phases are mainly Fe-rich AlFeSi phase (bright white), as well as Mg2Si and Cu-containing phases (grayish black). Significant compositional fluctuations exist within the grains. This severe non-equilibrium solidification structure severely disrupts the continuity of the matrix and is the main reason for the deterioration of the alloy's processing properties.

[0086] according to Figure 4 As shown in (b), after homogenization at 530℃ for 5 hours, the continuous network-like second phase at the grain boundaries began to exhibit localized melting and passivation, but the network framework remained clearly discernible. The low-melting-point non-equilibrium Mg₂Si phase partially dissolved, while the thermally stable Fe-rich phase showed less morphological change. Based on... Figure 4 As shown in (c), extending the holding time to 10 hours significantly improved the spheroidization of the grain boundary second phase. The originally continuous network structure was essentially broken, evolving into chain-like or discrete particles distributed along the grain boundaries, thus improving the uniformity of the intragranular composition. The results indicate that although the time factor helps promote diffusion at 530 °C, the fragmentation of the insoluble phase and the long-range diffusion of solute atoms are still insufficient due to the relatively low atomic diffusion driving force.

[0087] according to Figure 4 As shown in (d) and (e), the microstructure evolution of the Al-Mg-Si alloy accelerates significantly after the temperature is increased to 560℃. The coarse second-phase network at the grain boundaries essentially disappears after 5 hours of holding, transforming into fine, dispersed granular phases. This change is mainly due to the fracture and spheroidization effect of the refractory Fe-rich phase at high temperatures. Notably, the homogenization effect achieved by holding at 560℃ for 5 hours is better than that achieved by holding at 530℃ for 10 hours, indicating that the effect of temperature on the diffusion rate indeed increases exponentially, and its effect is far greater than simply extending the holding time. When the holding time is extended to 10 hours, the alloy becomes even more highly homogenized. At this point, only a very small amount of fine, rounded stable phase particles remain at the grain boundaries, and the original network structure is completely eliminated. The non-equilibrium eutectic phase is fully dissolved, and the matrix exhibits excellent homogeneity.

[0088] In summary, compared with comparative examples 3-5, the aluminum alloy ingot in Example 1 of this invention, after homogenization under specific conditions, significantly eliminated intragranular segregation (making the distribution of alloying elements more uniform), promoted the dissolution of non-equilibrium second phases (such as Mg2Si, Al2Cu) back into the matrix, and transformed the coarse, continuous network second phase into fine, dispersed granular phases. Example 1 significantly improved the plasticity of the aluminum alloy ingot, reduced the risk of cracking during subsequent hot rolling or extrusion, laid a good foundation for subsequent heat treatment (solution treatment), and made the final age-strengthening effect better.

[0089] The embodiments of the present invention have been described above; however, these embodiments are for illustrative purposes only and are not intended to limit the scope of the invention. All other embodiments obtained by those skilled in the art based on the above embodiments of the present invention without inventive effort are within the protection scope of the present invention.

Claims

1. A method for preparing 6xxx series aluminum alloy materials, characterized in that, Includes the following steps: The aluminum alloy ingot is subjected to homogenization, milling, hot rolling, solution treatment and aging treatment in sequence to obtain the 6xxx series aluminum alloy material. The solution treatment temperature is 500~550 degrees Celsius; The timeliness processing is a tiered timeliness processing; The graded aging process includes pre-aging, over-aging, and stabilization aging processes performed sequentially. The pre-aging temperature is 100~150 degrees Celsius, and the holding time is 0.5~8 hours; The aging temperature is 200-250 degrees Celsius, and the holding time is 0.5-8 hours; The stabilization aging temperature is 150~200 degrees Celsius, and the holding time is 0.5~5 hours; The pre-aging heat preservation time shall not be longer than the over-aging heat preservation time; The holding time for stabilization aging shall not exceed half the holding time for over-aging; The heat preservation time for the solution treatment is determined according to the thickness of the hot-rolled plate: when the plate thickness is less than 25mm, the heat preservation time is 2.5 hours; When the thickness of the board is 25mm or more, the standard extension of the insulation time is 0.1 hours for every 1mm increase in board thickness, based on the 2.5-hour insulation time. The temperature for heat equalization is 540-570 degrees Celsius, and the heat preservation time is 6-12 hours.

2. The preparation method according to claim 1, characterized in that, The hot rolling includes a first hot rolling and a second hot rolling performed sequentially. The temperature of the first hot rolling is 440~470 degrees Celsius, and the holding time is 0.5~6 hours; The temperature of the second hot rolling is 250~320 degrees Celsius, and the holding time of the second hot rolling is determined by the conveying speed, which is 8~25m / s.

3. The preparation method according to claim 1, characterized in that, The target thickness of the hot-rolled sheet is 5 to 50 millimeters.

4. The preparation method according to claim 1, characterized in that, The solution treatment further includes quenching the resulting product; the quenching cooling rate is not less than 100℃ / s.

5. The 6xxx series aluminum alloy material obtained by the preparation method according to any one of claims 1 to 4.

6. The application of the 6xxx series aluminum alloy material as described in claim 5 in the field of high-end equipment manufacturing.

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