Anodizable ultra-high-strength aluminum alloy and method for producing the same

Abstract

The application discloses anode-oxidizable super-high-strength aluminum alloy and a preparation method thereof. Al 83.85~90.46wt%, Mg 6.0~9.5wt%, Zn 3.51~5.0wt%, Si 0.025~0.45wt%, and at least one of Mn, Cu, Ti, Be, Sb elements with a total content of not more than 0.70wt%, wherein the content of Mg, Zn and Si satisfies the relationship formula: -3.3≤[(2.31×Si)+(1.76×Zn)-Mg]×100≤3.6, and the grain length-diameter ratio is ≤3. The preparation method of the aluminum alloy deformed material comprises the following steps: (1) manufacturing an aluminum alloy ingot; (2) homogenizing heat treatment; (3) processing into a processing material; (4) solid solution heat treatment on the processing material; (5) cooling to room temperature; and (6) aging treatment. The aluminum alloy has low density, high strength and excellent surface treatment adaptability.

Description

Technical Field

[0001] This invention belongs to the field of aluminum alloys and their preparation and processing technology, and particularly relates to Al-Mg-Zn series aluminum alloys. More specifically, this invention relates to an anodizable ultra-high strength, high magnesium content Al-Mg-Zn alloy and its preparation method. Background Technology

[0002] In aerospace, high-end electronic equipment, precision instruments, and transportation, increasingly stringent requirements are being placed on the mechanical properties and surface treatment adaptability of structural materials. Aluminum alloys are widely used due to their high specific strength. To achieve decorative properties, wear resistance, and corrosion resistance, anodizing is one of the most critical surface treatment technologies for aluminum alloys, which improves performance by forming a dense alumina ceramic film on the material surface.

[0003] In the 3C consumer electronics sector, components such as smartphone frames and laptop casings are evolving towards greater robustness and durability. This requires materials to provide extremely high rigidity and impact resistance even with sub-millimeter-thin wall designs, protecting internal precision components. Meanwhile, anodizing is the soul of creating a high-end product feel and brand recognition; the market demands absolutely uniform, delicate, and flawless oxide film color. In the new energy vehicle sector, large components such as battery pack casings and integrated die-cast body parts must meet performance requirements while ensuring safety. Furthermore, with the high integration of components, many previously hidden structural parts have become "visible" or "perceptible," requiring surfaces with excellent corrosion resistance, wear resistance, and aesthetics, or providing a high-quality substrate for subsequent connection processes.

[0004] However, existing aluminum alloy systems face significant technical contradictions and limitations in simultaneously meeting the requirements of "anodizability" and "high strength": While widely used anodizable 6xxx series aluminum alloys can achieve uniform and bright oxide films, their strength (especially in the cast or die-cast state without sufficient plastic deformation and heat treatment) is usually limited, making it difficult to meet the requirements of high-load components. High-strength 2xxx and 7xxx series aluminum alloys, due to their high copper content or the presence of specific alloy phases, often result in uneven anodized films, dark colors, reduced corrosion resistance, or extreme sensitivity to oxidation processes, limiting their application in scenarios requiring surface beautification, protection, or functionalization. Current technology lacks an aluminum alloy that can simultaneously achieve high mechanical properties (especially high yield strength) and excellent, stable, and widely adaptable anodizing performance.

[0005] The present invention aims to provide a low-cost aluminum alloy composition and its preparation method. Its core objective is to achieve ultra-high strength and excellent anodizing performance, thereby providing a material solution for components with comprehensive requirements for structural strength and surface quality. Summary of the Invention

[0006] This invention, through extensive research and industrial practice, reveals that by synergistically designing magnesium, zinc, and silicon, a multi-scale nano-synergistic precipitation strengthening system composed of T phase, Mg2Si phase, and MgZn2 phase is constructed in the alloy. This fundamentally eliminates the grain boundary precipitation-free zones formed by the depletion of solute atoms in traditional alloys, effectively avoiding stress concentration and reducing potential difference. Furthermore, by intentionally avoiding the addition of elements such as Sc and Zr to eliminate their inhibitory effect on the recrystallization process, combined with a matched deformation-heat treatment integrated process, the material achieves a uniform, fine equiaxed grain structure with an average grain size ≤700μm, a grain aspect ratio ≤3, and a recrystallization ratio ≥80%. This dual regulation of composition and structure ensures that the alloy possesses both excellent mechanical properties and outstanding anodizing adaptability, meeting a wide range of needs from ordinary to hard and functional anodizing.

[0007] The purpose of this invention is to address the difficulty in balancing the strength and surface treatment of existing commercial aluminum alloys by providing a low-cost, ultra-high-strength anodizable aluminum alloy and its preparation method, thus offering an ideal material solution for consumer electronics, new energy vehicles and high-end transportation equipment, precision machinery and optical instruments, and other high-value-added fields.

[0008] The primary technical problem to be solved by this invention is to provide an ultra-high strength anodizable aluminum alloy material; the second technical problem to be solved by this invention is to provide a method for preparing the aluminum alloy material; the third technical problem to be solved by this invention is to provide a method for connecting the aluminum alloy material with itself or other alloys to form a new product; the fourth technical problem to be solved by this invention is to provide a new product formed by deformation of the alloy; and the fifth technical problem to be solved by this invention is to provide a method for processing the aluminum alloy material into a final component.

[0009] This invention relates to an anodizable ultra-high strength aluminum alloy, wherein the aluminum alloy contains: Al 83.85~90.46wt%, Mg 6.0~9.5wt%, Zn 3.51~5.0wt%, Si 0.025~0.45wt%, and at least one of Mn, Cu, Ti, Be, and Sb elements with a total content not exceeding 0.70wt%, wherein the contents of Mg, Zn, and Si satisfy the following relationship: -3.3≤[(2.31×Si)+(1.76×Zn)-Mg]×100≤3.6, and the grain aspect ratio ≤3.

[0010] The alloy of the present invention may also contain other elements that have the same refining and modifying effects as Mn, Cu, Ti, Be, Sb, etc.

[0011] The first preferred embodiment of the present invention is that the aluminum alloy contains: Al 84.20~90.17wt%, Mg 6.2~9.3wt%, Zn 3.6~5.0wt%, Si 0.025~0.40wt%, and at least one of Mn, Cu, Ti, Be, and Sb elements with a total content not exceeding 0.60wt%.

[0012] As a second preferred embodiment of the present invention, the aluminum alloy contains: Al 84.65~89.87wt%, Mg 6.4~9.0wt%, Zn 3.7~5.0wt%, Si 0.025~0.30wt%, and at least one of Cu, Mn, Ti, Be, and Sb elements with a total content not exceeding 0.55wt%.

[0013] As a third preferred embodiment of the present invention, the aluminum alloy contains: Mn 0.10~0.30wt%.

[0014] As a fourth preferred embodiment of the present invention, the aluminum alloy contains: Cu 0.15~0.55wt%.

[0015] As a fifth preferred embodiment of the present invention, the aluminum alloy contains: Ti 0.001~0.15wt%.

[0016] As a sixth preferred embodiment of the present invention, the aluminum alloy contains: Be 0.0002~0.01wt%.

[0017] As a seventh preferred embodiment of the present invention, the aluminum alloy contains: Sb 0.005~0.03wt%.

[0018] As an eighth preferred embodiment of the present invention, the aluminum alloy contains elements unintentionally introduced as impurities during the manufacturing process of the alloy ingot, wherein Fe ≤ 0.40 wt%, each of the other impurity elements ≤ 0.20 wt%, and the total ≤ 0.50 wt%. Preferably, the following conditions are met: Fe ≤ 0.20 wt%, each of the other impurity elements ≤ 0.10 wt%, and the total ≤ 0.25 wt%. Further, the following condition is met: Fe ≤ 0.10 wt%.

[0019] This invention also relates to a method for producing the aforementioned aluminum alloy. The process of producing the aluminum alloy deformed material can be described as "alloy preparation and smelting - semi-continuous casting to prepare ingots - homogenization heat treatment of ingots - hot deformation processing - (intermediate annealing) - (cold deformation processing) - solution treatment - (pre-deformation or straightening) - aging treatment - product supply"; the basic preparation process of the aluminum alloy casting can be described as "alloy preparation and smelting - casting and forming of castings - solution treatment - aging treatment - product supply".

[0020] The method for producing this wrought aluminum alloy material includes the following steps:

[0021] (1) Manufacturing semi-continuous casting ingots of the aluminum alloy material;

[0022] (2) The resulting ingot is subjected to homogenization heat treatment and / or preheating;

[0023] (3) The ingot is hot-deformed into the required form of the material by one or more hot deformation processing methods selected from extrusion, rolling and forging, or hot-deformed into a pre-processed material;

[0024] (4) Optionally, the pre-processed material can be reheated and then cold-deformed into the required material form;

[0025] (5) Perform solution heat treatment on the processed material;

[0026] (6) Rapidly cool the solution-treated material to room temperature; and

[0027] (7) The cooled processed material is subjected to natural aging or artificial aging treatment to obtain alloy aged processed material.

[0028] In step (1), the ingot is manufactured using smelting, degassing, inclusion removal, and semi-continuous casting. During smelting, Mg and Zn are used as the core elements to precisely control the content of the elements. Through online composition analysis, the ratio between alloying elements is quickly adjusted to complete the entire ingot manufacturing process. In one preferred aspect, 0.001~0.15wt% Ti is added in the form of an Al-Ti master alloy during smelting to refine the grains. In another preferred aspect, 0.0002~0.01wt% Be is added in the form of an Al-Be master alloy during smelting to change the oxide film properties and reduce oxidation loss and inclusions. In a third preferred aspect, 0.005~0.03% Sb is added in the form of an Al-Sb master alloy to neutralize alkali metal impurities such as Na in the alloy, improve the surface quality of the ingot, and enhance the hot working plasticity of the alloy. In another preferred aspect, step (1) further includes applying an electromagnetic field, an ultrasonic field, or mechanical stirring at or near the crystallizer.

[0029] In step (2), the homogenization heat treatment is performed by means of the group selected from: (1) a single-stage homogenization heat treatment for a total time of 6 to 60 h in the range of 380 to 490 °C; and (2) a two-stage or multi-stage homogenization heat treatment for a total time of 6 to 60 h in the range of 380 to 500 °C.

[0030] In step (3), the heat distortion temperature is 340~480℃; preferably, the distortion temperature is 360~460℃; more preferably, the distortion temperature is 380~440℃.

[0031] In steps (3) and (4), the preheating temperature and reheating temperature before each hot deformation process are 380~460℃, and the processing time is 1~8h; in a preferred aspect, the deformation amount is not less than 40%; more preferably, the deformation amount is not less than 60%. In another preferred aspect, an intermediate annealing process of 350~450℃ / 0.5~6h is added between cold deformation passes.

[0032] In step (5), the solution heat treatment needs to further adjust the recrystallization ratio in the material according to performance requirements, and is carried out by means of the group selected from: (1) single-stage, double-stage or multi-stage solution heat treatment with a total time of ≥1h in the range of 430~485℃; and (2) continuous heating solution heat treatment with a total time of 0.5~5h in the range of 430~485℃. In a preferred aspect, the continuous heating solution heat treatment is used, and the heating rate is ≤40℃ / min.

[0033] In step (6), the workpiece is rapidly cooled to room temperature using a method selected from cooling medium spray quenching, immersion quenching, forced air cooling, and combinations thereof.

[0034] In step (7), the artificial aging treatment is carried out by means of the following group: (1) natural aging at room temperature after quenching and cooling for ≥24h; (2) artificial aging treatment within 2h after quenching and cooling in the range of 50~240℃ for a total time of 6~60h; and (3) after quenching and cooling, a combination of natural aging and artificial aging is used, with artificial aging temperature of 50~240℃ and time of 6~70h.

[0035] Between steps (6) and (7), the following steps may also be included: straightening and / or pre-deformation of the cooled processed material, using roller straightening, tension straightening, tension bending straightening and combinations thereof to improve the flatness of the processed material, and using tension, compression and combinations thereof to pre-deform to reduce the residual stress formed by quenching and cooling, so as to facilitate subsequent processing and application.

[0036] The processing material described in the preparation method of this invention is an extruded material, a sheet material, or a forging product.

[0037] The density of the anodizable ultra-high strength alloy of the present invention is ≤2.70 g / cm³. 3 The yield strength is ≥400MPa, meeting the requirements for anodizing. Preferably, the yield strength of the aluminum alloy is ≥450MPa. Preferably, the density of the aluminum alloy is ≤2.69g / cm³. 3 The yield strength is ≥500MPa. Preferably, the density of the aluminum alloy is ≤2.68g / cm³. 3The yield strength is ≥550MPa. Preferably, the density of the alloy is ≤2.67g / cm³. 3 Yield strength ≥ 600 MPa.

[0038] This invention also relates to a method for preparing the aluminum alloy casting, comprising the following steps:

[0039] (1) Aluminum alloy castings are prepared by smelting, degassing, removing inclusions and sand casting, metal casting, or die casting. During the smelting process, the content of elements is precisely controlled with Mg and Zn as the core. The ratio between alloy elements is quickly adjusted by online composition detection and analysis, and the entire casting preparation process is completed.

[0040] (2) Solution heat treatment of the obtained aluminum alloy casting: including single-stage, double-stage or multi-stage solution heat treatment of aluminum alloy casting for a total time of ≥1h in the range of 440~480℃, or continuous heating solution heat treatment of aluminum alloy casting for a total time of 0.5~5h in the range of 440~480℃. In a preferred aspect, continuous heating solution treatment is adopted, and the heating rate is ≤40℃ / h.

[0041] (3) Perform natural aging or artificial aging heat treatment on aluminum alloy castings; natural aging is carried out at room temperature for ≥24h; artificial aging is carried out in the range of 50~240℃ for a total time of 6~60h; or a combination of natural aging and artificial aging is used, with artificial aging temperature of 50~240℃ and time of 6~70h.

[0042] As described in this invention, the aluminum alloy can be connected with itself or other alloys to form a new product; it can be a new product formed by deformation of the alloy; it can also be processed into a final component; the final component is a load-bearing structural component.

[0043] The beneficial effects of this invention are as follows:

[0044] (1) By synergistically regulating the main alloying elements Mg, Zn, and Si, a multi-scale nano-synergistic precipitation strengthening system was constructed, which suppressed or even eliminated the grain boundary precipitation band. This achieved a comprehensive improvement in the alloy's ultra-high yield strength and anodizing performance, meeting the material selection requirements of lightweight and high aesthetics for high-end equipment.

[0045] (2) The material described in this invention has both excellent mechanical properties and excellent surface treatment properties. Moreover, the preparation process involved is simple, efficient, controllable, and highly operable. It is easy to transfer and scale up in existing industrial production lines, and has a solid industrialization foundation and broad market application prospects. Attached Figure Description

[0046] Figure 1This is a photograph of the grain morphology of alloy #9 in the aged state in Example 1 of the present invention. Detailed Implementation

[0047] The present invention will be further described below with reference to the accompanying drawings and embodiments. It should be emphasized that the following description is merely exemplary and is not intended to limit the scope of the invention or its application.

[0048] Example 1

[0049] Alloy extruded sheets and strips were prepared on a laboratory scale to demonstrate the principles of the invention. The composition of the experimental alloys is shown in Table 1.

[0050] Φ200mm round ingots were prepared using well-known alloy smelting, degassing, inclusion removal, and simulated semi-continuous casting conditions. The homogenization heat treatment regime for the ingots was selected as (400±5℃ / 10h) + (475±5℃ / 24h), followed by air cooling. After peeling, milling, and sawing, extruded billets with a specification of Φ151mm were obtained. The billets were preheated at 410±10℃ for 4h, and then extruded to obtain 18×100mm strips, with the extrusion temperature controlled at around 400℃. The extruded strips were placed in an air furnace at 430℃ and subjected to continuous heating solution heat treatment at 450~485℃ for a total time of 120~300min. After water quenching, they were immediately subjected to 2.0~2.5% tensile straightening treatment, followed by two-stage aging treatment at 90±5℃ / 24h + 145±5℃ / 10~24h, depending on the alloy characteristics.

[0051] Samples were cut according to relevant methods. Referring to the intercept method for grain size determination in GB / T3246.1, the transverse grain size / longitudinal grain size value was used as the grain length-to-diameter ratio. The alloy was tested for density (GB / T1423), tensile properties (GB / T 16865), and anodizing (GB / T 8013) according to relevant testing standards to evaluate the alloy's performance. The results are shown in Table 2.

[0052] Table 1. Experimental alloy composition

[0053]

[0054] Table 2 Performance test results of the experimental alloys

[0055]

[0056] As can be seen from Table 2, alloys #1 to #12 all exhibit a good match between density, strength, and anodizing performance: density not exceeding 2.69 g / cm³. 3The yield strength remained above 460 MPa, and the elongation after fracture was above 10.0%. All anodizing treatments were passed. However, alloys 13# to 16# failed to meet the anodizing requirements, exhibiting problems such as material marks, black spots, and localized peeling: alloy 13# had a high Si content, alloy 14# contained Zr, alloy 15# had a Cu+Mn content exceeding 0.70 wt%, alloy 16# had a low Mg content and a high Zn content, and alloy 17# did not meet the required relationship between Mg, Zn, and Si elements. Figure 1 The photograph shows the grain morphology of alloy #9 in this embodiment under aging conditions. It can be seen that the grains in the alloy are basically equiaxed.

[0057] Example 2

[0058] Aluminum alloy rolled sheets were prepared in the laboratory, and the composition of the experimental alloy is shown in Table 3.

[0059] Flat ingots with a thickness of 120 mm were prepared using well-known alloy smelting, degassing, inclusion removal, and simulated semi-continuous casting conditions. All ingots underwent a three-stage homogenization heat treatment (400±5℃ / 10h) + (460±5℃ / 20h + (480±5℃ / 12h)) followed by air cooling. After peeling, milling, and sawing, 90 mm thick rolled billets were obtained. The billets were preheated at 430±10℃ for 2 hours, and the initial rolling temperature was 420℃. First, along... The flat ingot is subjected to 3-4 passes of intermediate annealing at 415±5℃ for 3 hours along its width. Then, it is rolled in reverse direction along its length to a thickness of approximately 40mm. The sheet is then placed in an air furnace at 445℃ for solution heat treatment at 450℃ for 60 minutes followed by 470℃ for 90 minutes. After water quenching, it undergoes a 2.2% pre-stretch deformation treatment immediately, followed by a two-stage aging treatment at 90±5℃ for 24 hours and 145±5℃ for 24 hours.

[0060] Samples were cut according to relevant methods. Referring to the intercept method for grain size determination in GB / T3246.1, the transverse grain size / longitudinal grain size value was used as the grain length-to-diameter ratio. The alloy was tested for density (GB / T1423), tensile properties (GB / T 16865), and anodizing (GB / T 8013) according to relevant testing standards to evaluate the alloy's performance. The results are shown in Table 4.

[0061] Table 3 Experimental alloy composition

[0062]

[0063] Table 4 Performance test results of the experimental alloys

[0064]

[0065] As can be seen from Table 4, the 18# alloy of the present invention exhibits good strength and anodizing effect, which is significantly better than the 19# alloy of the non-present invention.

[0066] Example 3

[0067] Small-sized aluminum alloy forgings were prepared on a pilot-scale platform. The alloy composition is shown in Table 5.

[0068] Using well-known industry procedures such as alloy smelting, degassing, and inclusion removal, Φ500mm round ingots were prepared by semi-continuous casting. The homogenization heat treatment regime for the ingots was selected as (390±5℃ / 10h)+(470±5℃ / 24h)+(485±5℃ / 12h), followed by air cooling. After peeling, milling, and sawing, Φ450mm extrusion billets were obtained. The billets were preheated at 450±10℃ for 6h, and then extruded to obtain Φ320mm extrusion bar billets. These billets were then subjected to multi-faceted forging to obtain small-diameter forgings of 50×600×900mm. The extrusion and forging deformation temperatures were controlled between 390 and 440℃. The forgings were placed in an air furnace at 450℃ and subjected to solution heat treatment at 450℃ / 60min + 480℃ / 150min. After water quenching, they were immediately subjected to pre-compression deformation treatment of 2.0~2.5%, followed by two-stage aging treatment at 70±5℃ / 24h + 135±5℃ / 26h.

[0069] Samples were cut according to relevant methods. Referring to the intercept method for grain size determination in GB / T3246.1, the transverse grain size / longitudinal grain size value was used as the grain length-diameter ratio. The alloy was tested for density (GB / T1423), tensile properties (GB / T 16865), and anodizing (GB / T 8013) according to relevant testing standards to evaluate the alloy's performance. The results are shown in Table 6.

[0070] Table 5 Experimental Alloy Composition

[0071]

[0072] Table 6 Performance test results of the experimental alloys

[0073]

[0074] As can be seen from Table 6, the 20# alloy of the present invention exhibits good strength and anodizing effect.

[0075] Example 4

[0076] Aluminum alloy castings were prepared in the laboratory, and the alloy composition is shown in Table 7.

[0077] The process involves preparing raw materials (high-purity aluminum, pure magnesium, pure zinc, pure Cu, Al-Si master alloy, Al-Mn master alloy, Al-Ti master alloy, Al-Be master alloy, Al-Sb master alloy, and Al-Ti-B master alloy refiner), baking the molds, melting the high-purity aluminum at 735℃, and then adding pure zinc, Al-Si master alloy, Al-Ti master alloy, Al-Be master alloy, and Al-Sb master alloy in the conventional order, stirring until completely melted; cooling to 715℃ and adding the Al-Ti-B master alloy, stirring and letting it stand for 4-6 minutes; continuing to cool to 710℃ and then using... The pure magnesium wrapped in aluminum foil is pressed into the molten aluminum alloy using a bell jar and stirred until fully melted. The mixture is then degassed and refined at 720℃, followed by a pre-furnace inspection. After standing for 30 minutes at a casting temperature of 695℃, the molten aluminum alloy is poured into a preheated metal mold at a temperature of approximately 180-210℃. The resulting aluminum alloy casting is placed in an air furnace at 465℃ for solution heat treatment at 465±5℃ / 14h + 480±5℃ / 16h. After water cooling, it undergoes natural aging for 48h, followed by a two-stage aging treatment at 80±5℃ / 12h + 130±5℃ / 22h.

[0078] Samples were cut according to relevant methods. Referring to the intercept method for grain size determination in GB / T3246.1, the transverse grain size / longitudinal grain size value was used as the grain length-to-diameter ratio. The alloy was tested for density (GB / T1423), tensile properties (GB / T 16865), and anodizing (GB / T 8013) according to relevant testing standards to evaluate the alloy's performance. The results are shown in Table 8.

[0079] Table 7 Experimental Alloy Composition

[0080]

[0081] Table 8 Performance test results of the experimental alloys

[0082]

[0083] As can be seen from Table 8, compared with the 22# alloy (Al-Mg-Si cast aluminum alloy) casting, the 21# alloy of the present invention exhibits a higher strength level and anodizing effect.

Claims

1. An anodizable ultra-high strength aluminum alloy, characterized in that, The aluminum alloy contains: Al 83.85~90.46wt%, Mg 6.0~9.5wt%, Zn 4.06~5.0wt%, Si 0.025~0.45wt%, and at least one of Mn, Cu, Ti, Be, and Sb with a total content not exceeding 0.70wt%. The contents of Mg, Zn, and Si satisfy the following relationship: -3.3≤[(2.31×Si)+(1.76×Zn)-Mg]×100≤3.6, and the grain aspect ratio ≤3. The density of the aluminum alloy material is ≤2.68g / cm³. 3 With a yield strength ≥550MPa, it meets a wide range of needs from ordinary to hard and functional anodizing.

2. The anodizable ultra-high strength aluminum alloy according to claim 1, characterized in that, The aluminum alloy contains: Al 84.20~90.17wt%, Mg 6.2~9.3wt%, Zn 4.06~5.0wt%, Si 0.025~0.40wt%, and at least one of Mn, Cu, Ti, Be, and Sb in total content not exceeding 0.60wt%.

3. The anodizable ultra-high strength aluminum alloy according to claim 2, characterized in that, The aluminum alloy contains: Al 84.65~89.87wt%, Mg 6.4~9.0wt%, Zn 4.06~5.0wt%, Si 0.025~0.30wt%, and at least one of Cu, Mn, Ti, Be, and Sb in total content not exceeding 0.55wt%.

4. The anodizable ultra-high strength aluminum alloy according to claim 3, characterized in that, The aluminum alloy contains: Mn 0.10~0.30wt%.

5. The anodizable ultra-high strength aluminum alloy according to claim 3, characterized in that, The aluminum alloy contains: Cu 0.15~0.55wt%.

6. The anodizable ultra-high strength aluminum alloy according to claim 3, characterized in that, The aluminum alloy contains: Ti 0.001~0.15wt%.

7. The anodizable ultra-high strength aluminum alloy according to claim 3, characterized in that, The aluminum alloy contains: Be 0.0002~0.01wt%.

8. The anodizable ultra-high strength aluminum alloy according to claim 3, characterized in that, The aluminum alloy contains: Sb 0.005~0.03wt%.

9. The anodizable ultra-high strength aluminum alloy according to claim 3, characterized in that, The aluminum alloy contains elements that were unintentionally introduced as impurities during the manufacturing process of the alloy ingot, wherein Fe ≤ 0.40 wt%, each of the other impurity elements ≤ 0.20 wt%, and the total ≤ 0.50 wt%.

10. The anodizable ultra-high strength aluminum alloy according to claim 9, characterized in that, The aluminum alloy contains elements that were unintentionally introduced as impurities during the manufacturing process of the alloy ingot, wherein Fe ≤ 0.20 wt%, each of the other impurity elements ≤ 0.10 wt%, and the total ≤ 0.25 wt%.

11. The anodizable ultra-high strength aluminum alloy according to claim 10, characterized in that, In the aluminum alloy, Fe ≤ 0.10 wt%.

12. A method for producing wrought aluminum alloy materials, characterized in that, Includes the following steps: (1) Manufacturing an ingot of the aluminum alloy material according to any one of claims 1 to 11; (2) The resulting ingot is subjected to homogenization heat treatment and / or preheating; (3) The ingot is hot-deformed into the required form of the material by one or more hot deformation processing methods selected from extrusion, rolling and forging, or hot-deformed into a pre-processed material; (4) Optionally, the pre-processed material can be reheated and then cold-deformed into the required material form; (5) Perform solution heat treatment on the processed material; (6) Rapidly cool the solution-treated material to room temperature; and (7) The cooled processed material is subjected to natural aging or artificial aging treatment to obtain alloy aged processed material.

13. The method according to claim 12, characterized in that, In step (1), the ingot is manufactured by smelting, degassing, removing inclusions and semi-continuous casting. During the smelting process, the content of elements is precisely controlled with Mg and Zn as the core. Through online component detection and analysis, the ratio between alloying elements is quickly supplemented and adjusted, and the entire ingot manufacturing process is completed.

14. The method according to claim 13, characterized in that, In step (1), 0.001 to 0.15 wt% Ti is added in the form of an Al-Ti master alloy during smelting to refine the grain size.

15. The method according to claim 13, characterized in that, In step (1), 0.0002~0.01wt% of Be is added in the form of an Al-Be master alloy during smelting to change the properties of the oxide film and reduce oxidation loss and inclusions.

16. The method according to claim 13, characterized in that, In step (1), 0.005-0.03% Sb is added in the form of an Al-Sb master alloy during smelting to neutralize alkali metal impurities such as Na in the alloy, improve the surface quality of the ingot, and enhance the hot working plasticity of the alloy.

17. The method according to claim 13, characterized in that, Step (1) also includes applying an electromagnetic field, an ultrasonic field or mechanical stirring to or near the crystallizer.

18. The method according to claim 12, characterized in that, In step (2), the homogenization heat treatment is performed by means selected from the group consisting of: (1) A single-stage homogenization heat treatment with a total time of 6 to 60 hours was carried out in the range of 380 to 490℃; and (2) Perform a two-stage or multi-stage homogenization heat treatment with a total time of 6 to 60 hours in the range of 380 to 500℃.

19. The method according to claim 12, characterized in that, In step (3), the heat distortion temperature is 340~480℃.

20. The method according to claim 19, characterized in that, In step (3), the heat distortion temperature is 360~460℃.

21. The method according to claim 20, characterized in that, In step (3), the heat distortion temperature is 380~440℃.

22. The method according to claim 12, characterized in that, In steps (3) and (4), the preheating temperature and reheating temperature before each hot deformation process are 380~460℃, and the processing time is 1~8h.

23. The method according to claim 12, characterized in that, In steps (3) and (4), the deformation is more than 40%.

24. The method according to claim 12, characterized in that, In steps (3) and (4), the deformation is more than 60%.

25. The method according to claim 12, characterized in that, In step (4), an intermediate annealing treatment of 350~450℃ / 0.5~6h is also added between cold deformation passes.

26. The method according to claim 12, characterized in that, In step (5), the solution heat treatment needs to further adjust the recrystallization structure ratio and grain size in the material according to performance requirements, and is carried out by means selected from the following group: (1) Single-stage, double-stage, or multi-stage solution heat treatment with a total time ≥1h, performed within the temperature range of 430~485℃; and (2) A continuous heating solution heat treatment with a total time of 0.5 to 5 hours is carried out in the range of 430 to 485℃.

27. The method according to claim 26, characterized in that, Continuous solution heat treatment with a heating rate ≤40℃ / min is adopted.

28. The method according to claim 12, characterized in that, In step (6), the workpiece is rapidly cooled to room temperature using a method selected from cooling medium spray quenching, immersion quenching, forced air cooling, and combinations thereof.

29. The method according to claim 12, characterized in that, In step (7), the artificial aging process is performed by means selected from the group consisting of: (1) After quenching and cooling, allow the material to age naturally at room temperature for ≥24 hours; (2) Within 2 hours after quenching and cooling, perform artificial aging treatment within the range of 50~240℃, for a total time of 6~60 hours; and (3) After quenching and cooling, natural aging and artificial aging are combined. The artificial aging temperature is 50~240℃ and the time is 6~70h.

30. The method according to claim 12, characterized in that, Between steps (6) and (7), the following steps are also included: straightening and / or pre-deformation of the cooled processed material, using roller straightening, tension straightening, tension bending straightening and combinations thereof to improve the flatness of the processed material, and using tension, compression and combinations thereof to pre-deform to reduce the residual stress formed by quenching and cooling, so as to facilitate subsequent processing and application.

31. The method according to claim 12, characterized in that, The processed materials are extruded materials, plates, and forgings.

32. The anodizable ultra-high strength aluminum alloy according to any one of claims 1 to 11, or the anodizable ultra-high strength aluminum alloy manufactured by the method according to any one of claims 12 to 31, characterized in that, The density of the aluminum alloy material is ≤2.67 g / cm³. 3 Yield strength ≥ 600 MPa.

33. A method for producing cast aluminum alloy materials, characterized in that, Includes the following steps: (1) Aluminum alloy castings of any one of the aluminum alloy materials described in claims 1 to 11 are prepared by smelting, degassing, removing inclusions and casting with sand molds, metal molds or die casting; during the smelting process, the element content is precisely controlled with Mg and Zn as the core, and the ratio between alloy elements is quickly supplemented and adjusted through online component detection and analysis, and the entire casting preparation process is completed. (2) Solution heat treatment of the obtained aluminum alloy castings: including single-stage, double-stage or multi-stage solution heat treatment of aluminum alloy castings with a total time of ≥1h in the range of 440~480℃, or continuous heating solution heat treatment of aluminum alloy castings with a total time of 0.5~5h in the range of 440~480℃, with a heating rate ≤40℃ / h; (3) Perform natural aging or artificial aging heat treatment on aluminum alloy castings; natural aging is carried out at room temperature for ≥24h; artificial aging is carried out in the range of 50~240℃ for a total time of 6~60h; or a combination of natural aging and artificial aging is used, with artificial aging temperature of 50~240℃ and time of 6~70h.

34. An aluminum alloy product, characterized in that, It is a product formed by bonding together with the anodizable ultra-high strength aluminum alloy according to any one of claims 1 to 11, 32 or the anodizable ultra-high strength aluminum alloy manufactured by the method according to any one of claims 12 to 31, 33, and other alloys.

35. An aluminum alloy product, characterized in that, It is a product obtained by deformation of an anodizable ultra-high strength aluminum alloy according to any one of claims 1 to 11, 32 or an anodizable ultra-high strength aluminum alloy manufactured by the method according to any one of claims 12 to 31, 33.

36. A final component, characterized in that, The anodizable ultra-high strength aluminum alloy according to any one of claims 1 to 11, 32 or the anodizable ultra-high strength aluminum alloy manufactured by the method according to any one of claims 12 to 31, 33 is processed into a final component.

37. The final component according to claim 36, characterized in that, The final component is a load-bearing structural member.

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