A solution treatment-free al-zn-mg-cu-c alloy and a preparation method and application thereof

Abstract

The application provides a solid solution treatment-free Al-Zn-Mg-Cu-C alloy and a preparation method and application thereof, the petroleum coke content is 0.1% to 5%, and the rest is an aluminum alloy matrix, the Al-Zn-Mg-Cu matrix material comprises the following components in percentage by weight: Zn 4.0% to 8.4%, Mg 0.5% to 3.3%, and Cu 0.3% to 2.6%. The solid solution treatment-free Al-Zn-Mg-Cu-C alloy is obtained by mechanical ball milling, pressing and subsequent processing. By adding the petroleum coke, the number of C / Al phase interfaces with metallurgical bonding is increased, the atomic diffusion efficiency is improved, the supersaturation solid solution of Zn in the aluminum matrix in the mechanical alloying process is finally realized, the solid solution heat treatment process is reduced, the growth of the ultrafine aluminum grains is avoided, and the mechanical properties of the material are improved. The process flow of the application is simple, the requirement for equipment is low, and the application has an industrialization popularization prospect.

Description

Technical Field

[0001] This invention belongs to the field of aluminum alloy preparation technology, specifically relating to a solution-free Al-Zn-Mg-Cu-C alloy, its preparation method, and its application. Background Technology

[0002] High-performance 7xxx (Al-Zn-Mg-Cu) aluminum alloys are widely used in transportation, aerospace, and defense technology due to their excellent specific strength, specific modulus, fatigue performance, weldability, and corrosion resistance. With the rapid development of aerospace equipment, the requirements for lightweight and integrated key components are constantly increasing, placing higher demands on material properties, especially strength. Aluminum alloys have high stacking fault energy, and the main plastic deformation mechanism is dislocation slip; therefore, their mechanical properties are closely related to the ease of dislocation slip. 7xxx series aluminum alloys contain a large number of second-phase particles and solid solution atoms, which hinder dislocation slip during plastic deformation. Grain boundaries with atomic distortion also hinder dislocation slip. Therefore, their main strengthening mechanisms include dispersion strengthening, solid solution strengthening, grain refinement strengthening, and dislocation strengthening caused by plastic deformation.

[0003] Powder metallurgy is a manufacturing process that solidifies material particles into bulk materials. Its main processes include powder preparation, powder treatment, and solidification. In the preparation of 7xxx series aluminum alloys, foreign countries started earlier, with Europe having already achieved the preparation of 840MPa powder metallurgy 7xxx series aluminum alloys. Research has found that mechanical alloying processes can refine the aluminum matrix grains, improve the fine-grain strengthening ability of the material, and further enhance the strength of the aluminum alloy. Elemental powders, as initial raw materials for mechanical alloying, have advantages such as material composition stability, reduced material costs, and fewer impurity elements in the alloy. However, the dispersion strengthening of 7xxx series aluminum alloys requires the formation of nanoscale GP zones, η, and η' through solution treatment and aging treatment. The eutectic temperature of Al and Zn is 277℃, and the mutual diffusion time between pure Al powder and pure Zn powder is relatively long. During solution treatment, the ultrafine aluminum grains inevitably grow, affecting the fine-grain strengthening effect of the aluminum alloy. Therefore, achieving supersaturated solid solution of Zn atoms in the aluminum matrix during mechanical alloying, reducing the solid solution heat treatment process, and avoiding the growth of ultrafine aluminum grains are crucial for further improving the performance of 7xxx series aluminum alloys. Summary of the Invention

[0004] This invention addresses the problem of grain growth during solution heat treatment in the mechanical alloying preparation of ultrafine-grained 7xxx series aluminum alloys. To this end, this invention provides a solution-free Al-Zn-Mg-Cu-C alloy, its preparation method, and its applications. This invention incorporates petroleum coke during the mechanical alloying process of 7xxx series aluminum alloys, which promotes the supersaturated solid solution of Zn in the aluminum matrix, reduces the need for solution treatment steps in the mechanical alloying preparation of 7xxx series aluminum alloys, avoids the growth of ultrafine aluminum grains, and achieves the preparation of ultrafine-grained, high-strength 7xxx series aluminum alloys.

[0005] The petroleum coke used in this invention is a byproduct obtained from the coking process of heavy oil during petroleum refining. It is inexpensive and abundant. This invention shortens the process flow for preparing 7xxx series aluminum alloys using powder metallurgy while improving the mechanical properties of these alloys. The process is simple, requires minimal equipment, and has promising prospects for industrial application. The technical solution of this invention is as follows:

[0006] The first aspect of the present invention is to provide a solution-free Al-Zn-Mg-Cu-C alloy, comprising petroleum coke and an Al-Zn-Mg-Cu matrix material in the following mass fractions: petroleum coke 0.1% to 5%, and the Al-Zn-Mg-Cu matrix material comprising the following components by weight percentage: Zn 4.0% to 8.4%, Mg 0.5% to 3.3%, Cu 0.3% to 2.6%, and Al as the balance.

[0007] This invention provides a solution-free Al-Zn-Mg-Cu-C alloy. The main elemental composition of petroleum coke is carbon, accounting for more than 85 wt%. In addition, the constituent elements include a small amount of metallic elements and non-metallic elements that can react with metal powders, including O, S, etc. This can significantly improve the wettability of C particles with metal powders such as Al and Zn. According to Fick's law, the atomic diffusion rate at the phase boundary of this C / Al phase interface with metallurgical bonding is much greater than that within the grain, which increases the high-speed diffusion channels of elements. Ultimately, it achieves supersaturated solid solution of Zn in the aluminum matrix during the mechanical alloying process, reduces the solid solution heat treatment process of Al-Zn-Mg-Cu alloy prepared by mechanical alloying, avoids the growth of ultrafine aluminum grains, and improves the performance of Al-Zn-Mg-Cu alloy.

[0008] In a preferred embodiment, the petroleum coke mass fraction is 2% to 5%, more preferably 2% or 5%.

[0009] A second aspect of the present invention is to provide a method for preparing the above-mentioned solution-free Al-Zn-Mg-Cu-C alloy, comprising the steps of:

[0010] (1) Petroleum coke was uniformly mixed with Al, Zn, Mg and Cu element powders by low-speed ball milling to obtain Al-Zn-Mg-Cu-C alloy powder.

[0011] (2) Press the Al-Zn-Mg-Cu-C alloy powder.

[0012] (3) The product obtained in step (2) is further processed to obtain carbon-reinforced aluminum-based composite material products.

[0013] Furthermore, in step (1), the Al, Zn, Mg, and Cu elemental powders are gas-atomized powders with an average particle size between 1 and 200 μm.

[0014] Furthermore, the Al, Zn, Mg, and Cu elemental powders are gas-atomized powders, with Zn, Mg, and Cu contents of 8.4%, 2.3%, and 2.5%, respectively, and an average particle size of 1 μm.

[0015] Furthermore, in step (1), the ball mill is performed at a low speed, with a rotation speed of 100-250 rpm and a milling time of 10-40 h.

[0016] Furthermore, in step (2), the pressing pressure is higher than 100 MPa to solidify the powder.

[0017] Furthermore, in step (3), the subsequent processing methods include one or a combination of processing methods such as sintering, extrusion, forging, and rolling.

[0018] The third aspect of this invention provides the application of the above-mentioned solution-free Al-Zn-Mg-Cu-C alloy in the preparation of vehicle structures and national defense weapon equipment. Specifically, it includes the preparation of structures such as vehicle body panels, bases, bumpers, aircraft wheel hubs, sight brackets, and armor-piercing projectile sabots for transportation and national defense weapon equipment.

[0019] Compared with the prior art, the beneficial effects of the present invention are:

[0020] (1) Significant grain refinement strengthening effect: The nanoscale GP region, η and η' generated by solution treatment and aging treatment can effectively improve the strength of aluminum alloy. However, for ultrafine-grained aluminum alloy, the solution treatment process inevitably causes grain growth. This invention increases the C / Al phase interface with metallurgical bonding by introducing petroleum coke, improves the atomic diffusion efficiency, realizes the supersaturated solid solution of Zn element in Al-Zn-Mg-Cu alloy in aluminum matrix during mechanical alloying, reduces the solution heat treatment process, gives full play to the grain refinement strengthening effect of the material, and thus prepares high-strength Al-Zn-Mg-Cu alloy.

[0021] (2) Coupling strengthening and toughening effect: Through mechanical alloying, elements such as O and S are introduced into the aluminum matrix using petroleum coke as a carrier. During the hot forming process, nanoscale dispersed phases are formed, resulting in a dispersion strengthening effect, which improves the strength of the aluminum alloy. The C phase in petroleum coke is well bonded to the aluminum matrix interface, playing a load-bearing strengthening role and improving the plasticity of the aluminum alloy.

[0022] (3) Low material and processing costs: This invention uses petroleum coke as a reinforcing material, which is suitable for industrial production compared to nano-carbon materials, including carbon nanotubes and graphene. Compared to traditional mechanical alloying for Al-Zn-Mg-Cu alloy preparation, it reduces the solid solution treatment process, shortens the process flow, saves energy and reduces consumption, and is environmentally friendly, with broad application prospects.

[0023] (4) Strong technical applicability: The preparation process provided by this invention can be carried out by conventional sintering, extrusion, forging, rolling and other processing after powder pressing, so it is compatible with other processing technologies. Attached Figure Description

[0024] The accompanying drawings, which form part of this invention, are used to provide a further understanding of the invention. The illustrative embodiments of the invention and their descriptions are used to explain the invention and do not constitute an improper limitation of the invention.

[0025] Figure 1 This is a scanning electron microscope image of the pressed, solution-free Al-Zn-Mg-Cu-C alloy prepared in the first embodiment of the present invention.

[0026] Figure 2 This is a scanning electron microscope image of the aged, solution-free Al-Zn-Mg-Cu-C alloy prepared in the first embodiment of the present invention.

[0027] Figure 3 This is a scanning electron microscope image of the tensile fracture surface of the aged, solution-free Al-Zn-Mg-Cu-C alloy prepared in the first embodiment of the present invention. Detailed Implementation

[0028] It should be noted that the following detailed descriptions are exemplary and intended to provide further illustration of the invention. Unless otherwise specified, all technical and scientific terms used herein have the same meaning as commonly understood by one of ordinary skill in the art to which this invention pertains.

[0029] The technical solution of the present invention is not limited to the specific embodiments listed below, but also includes any reasonable combination of the specific embodiments.

[0030] Specific Implementation Method 1: This implementation method provides a solution-free Al-Zn-Mg-Cu-C alloy, comprising the following mass fractions of petroleum coke and Al-Zn-Mg-Cu matrix material: petroleum coke is 0.1% to 5%, and aluminum matrix material is the balance.

[0031] The Al-Zn-Mg-Cu matrix material comprises the following components by weight percentage: Zn 4.0%–8.4%, Mg 0.5%–3.3%, and Cu 0.3%–2.6%.

[0032] Specific Implementation Method Two: This implementation method provides a method for preparing the above-mentioned solution-free Al-Zn-Mg-Cu-C alloy, including the following steps:

[0033] (1) Petroleum coke was uniformly mixed with Al, Zn, Mg and Cu element powders by low-speed ball milling to obtain Al-Zn-Mg-Cu-C alloy powder.

[0034] (2) Press the Al-Zn-Mg-Cu-C alloy powder.

[0035] (3) The product obtained in step (2) is further processed to obtain carbon-reinforced aluminum-based composite material products.

[0036] Furthermore, in step (1), the Al, Zn, Mg, and Cu elemental powders are gas-atomized powders with an average particle size between 1 and 200 μm.

[0037] Furthermore, in step (1), the ball mill is performed at a low speed, with a rotation speed of 100-250 rpm and a milling time of 10-40 h.

[0038] Furthermore, in step (2), the pressing pressure is higher than 100 MPa.

[0039] Furthermore, in step (3), the subsequent processing methods include one or more combined processing methods such as sintering, extrusion, forging, and rolling.

[0040] Specific Implementation Method 3: In one embodiment of the present invention, the solution-free Al-Zn-Mg-Cu-C alloy, due to its high specific strength, is provided for applications in transportation and defense weapon equipment, including: vehicle body panels, bases, bumpers, aircraft wheel hubs, sight brackets, armor-piercing projectile sabots, etc.

[0041] Example 1,

[0042] A solution-free Al-Zn-Mg-Cu-C alloy comprises petroleum coke and Al-Zn-Mg-Cu matrix material in the following mass fractions: 2% petroleum coke and the balance being aluminum matrix material.

[0043] The Al-Zn-Mg-Cu matrix material comprises the following components by weight percentage: Zn 4.0%–8.4%, Mg 0.5%–3.3%, and Cu 0.3%–2.6%.

[0044] A method for preparing Al-Zn-Mg-Cu-C alloys without solution treatment includes the following steps:

[0045] (1) Petroleum coke was uniformly mixed with Al, Zn, Mg and Cu element powders by low-speed ball milling to obtain Al-Zn-Mg-Cu-C alloy powder.

[0046] The Al, Zn, Mg, and Cu elemental powders are gas-atomized powders, with Zn, Mg, and Cu contents of 8.4 wt.%, 2.3 wt.%, and 2.5 wt.%, respectively, and an average particle size of 1 μm.

[0047] The ball mill rotates at 200 rpm and the milling time is 30 hours.

[0048] (2) Press the Al-Zn-Mg-Cu-C alloy powder.

[0049] The pressing pressure is 1300 MPa.

[0050] (3) The product obtained in step (2) is extruded at an extrusion temperature of 500℃ and an extrusion ratio of 10 to obtain Al-Zn-Mg-Cu-C alloy products without solution treatment. The yield strength, tensile strength and elongation of the material are 454MPa, 487MPa and 11.8%, respectively.

[0051] Furthermore, the extruded Al-Zn-Mg-Cu-C alloy without solution treatment was subjected to aging heat treatment at a temperature of 120℃ for 24 hours to obtain a heat-treated Al-Zn-Mg-Cu-C alloy without solution treatment. The yield strength, tensile strength and elongation of the material were 789MPa, 827MPa and 11.3%, respectively.

[0052] Furthermore, the pressed-state solution-free Al-Zn-Mg-Cu-C alloy of the first embodiment was observed using a scanning electron microscope, and the results are as follows: Figure 1 As shown in the figure, mechanical ball milling achieves supersaturated solid solution of Zn in the aluminum matrix.

[0053] Furthermore, the aged, solution-free Al-Zn-Mg-Cu-C alloy of the first embodiment was observed using a scanning electron microscope, and the results are as follows: Figure 2 As shown in the figure, a large number of precipitated phases are dispersed in the aluminum matrix.

[0054] Furthermore, the tensile fracture surface of the solution-free Al-Zn-Mg-Cu-C alloy prepared in the first embodiment was observed using a scanning electron microscope, and the results are as follows: Figure 3 As shown in the figure, large dimples can be observed, which is typical of ductile fracture surfaces.

[0055] Comparative Example 1

[0056] This comparative example is basically the same as the process in Example 1, except that petroleum coke is not added in the comparative example. The specific steps are as follows:

[0057] (1) Al, Zn, Mg and Cu element powders were uniformly mixed by low-speed ball milling to obtain Al-Zn-Mg-Cu composite material powder.

[0058] The Al, Zn, Mg, and Cu elemental powders are gas-atomized powders, with Zn, Mg, and Cu contents of 8.4 wt.%, 2.3 wt.%, and 2.5 wt.%, respectively, and an average particle size of 1 μm.

[0059] The ball mill rotates at 200 rpm and the milling time is 30 hours.

[0060] (3) Press the Al-Zn-Mg-Cu material powder.

[0061] The pressing pressure is 1300 MPa.

[0062] (4) The Al-Zn-Mg-Cu material was extruded at a temperature of 500℃ and an extrusion ratio of 10 to obtain Al-Zn-Mg-Cu material products. The yield strength, tensile strength and elongation of the material were 385MPa, 421MPa and 11.2%, respectively.

[0063] Furthermore, the extruded Al-Zn-Mg-Cu material was subjected to aging heat treatment at 120℃ for 24 hours to obtain heat-treated Al-Zn-Mg-Cu material. The yield strength, tensile strength, and elongation of the material were 534 MPa, 612 MPa, and 10.3%, respectively. It can be seen that compared with Example 1, the increase in strength of the composite material before and after aging heat treatment was relatively small, mainly due to the significant precipitation strengthening effect in Example 1. The addition of petroleum coke achieved complete solid solution of Zn element in the aluminum matrix, such as... Figure 1 As shown, after aging heat treatment, supersaturated Zn solution formed a large number of dispersed precipitates with an average particle size of approximately 260 nm. Figure 2 As shown, it has a precipitation and strengthening effect.

[0064] Comparative Example 2

[0065] This comparative example is basically the same as the process in Example 1, except that petroleum coke is not added and a solution heat treatment step is added. The specific steps are as follows:

[0066] (1) Al, Zn, Mg and Cu element powders were uniformly mixed by low-speed ball milling to obtain Al-Zn-Mg-Cu composite material powder.

[0067] The Al, Zn, Mg, and Cu elemental powders are gas-atomized powders, with Zn, Mg, and Cu contents of 8.4 wt.%, 2.3 wt.%, and 2.5 wt.%, respectively, and an average particle size of 1 μm.

[0068] The ball mill rotates at 200 rpm and the milling time is 30 hours.

[0069] (3) Press the Al-Zn-Mg-Cu material powder.

[0070] The pressing pressure is 1300 MPa.

[0071] (4) The Al-Zn-Mg-Cu material was extruded at a temperature of 500℃ and an extrusion ratio of 10 to obtain Al-Zn-Mg-Cu material products. The yield strength, tensile strength and elongation of the material were 385MPa, 421MPa and 11.2%, respectively.

[0072] Furthermore, the extruded Al-Zn-Mg-Cu material was subjected to solution treatment and aging heat treatment. The solution treatment temperature was 480℃ and the solution treatment time was 2h. The aging heat treatment temperature was 120℃ and the aging time was 24h to obtain the heat-treated Al-Zn-Mg-Cu material. The yield strength, tensile strength and elongation of the material were 620MPa, 685MPa and 11.5%, respectively.

[0073] Comparative Example 3

[0074] This comparative example is basically the same as the process in Example 1, except that a solution heat treatment step is added. The specific steps are as follows:

[0075] (1) Petroleum coke was uniformly mixed with Al, Zn, Mg and Cu element powders by low-speed ball milling to obtain Al-Zn-Mg-Cu-C alloy powder.

[0076] The Al, Zn, Mg, and Cu elemental powders are gas-atomized powders, with Zn, Mg, and Cu contents of 8.4 wt.%, 2.3 wt.%, and 2.5 wt.%, respectively, and an average particle size of 1 μm.

[0077] The ball mill rotates at 200 rpm and the milling time is 30 hours.

[0078] (3) Press the Al-Zn-Mg-Cu-C alloy powder.

[0079] The pressing pressure is 1300 MPa.

[0080] (4) The Al-Zn-Mg-Cu-C alloy powder was extruded at a temperature of 500℃ and an extrusion ratio of 10 to obtain Al-Zn-Mg-Cu-C alloy products. The yield strength, tensile strength and elongation of the material were 454MPa, 487MPa and 11.8%, respectively.

[0081] Furthermore, the Al-Zn-Mg-Cu-C alloy was subjected to solution treatment and aging heat treatment. The solution treatment temperature was 480℃ and the solution treatment time was 2h. The aging heat treatment temperature was 120℃ and the aging time was 24h, resulting in a heat-treated Al-Zn-Mg-Cu material. The yield strength, tensile strength and elongation of the material were 714MPa, 746MPa and 11.4%, respectively. It can be seen that the strength of the material is reduced compared to that of Example 1. This is mainly because the aluminum matrix grains coarsen during the solution heat treatment. This coarsening behavior is irreversible and weakens the grain-refining strengthening effect of the prepared composite material.

[0082] Example 2

[0083] This embodiment provides an Al-Zn-Mg-Cu-C alloy, and the specific steps are basically the same as those in Example 1, except that the Al-Zn-Mg-Cu-C alloy is sintered. The specific steps are as follows:

[0084] (1) Petroleum coke was uniformly mixed with Al, Zn, Mg and Cu element powders by low-speed ball milling to obtain Al-Zn-Mg-Cu-C alloy powder.

[0085] The Al, Zn, Mg, and Cu elemental powders are gas-atomized powders, with Zn, Mg, and Cu contents of 8.4 wt.%, 2.3 wt.%, and 2.5 wt.%, respectively, and an average particle size of 1 μm.

[0086] The ball mill rotates at 200 rpm and the milling time is 30 hours.

[0087] (3) Press the Al-Zn-Mg-Cu-C alloy powder.

[0088] The pressing pressure is 1300 MPa.

[0089] (4) The Al-Zn-Mg-Cu-C alloy is sintered at a temperature of 500℃ for 1 hour to obtain Al-Zn-Mg-Cu-C alloy products.

[0090] Furthermore, the sintered Al-Zn-Mg-Cu-C alloy was subjected to aging heat treatment at a temperature of 120℃ for 24 hours to obtain a heat-treated Al-Zn-Mg-Cu-C alloy with yield strength, compressive strength and compressive fracture strain of 672MPa, 827MPa and 26.4%, respectively.

[0091] Example 3

[0092] This embodiment describes a solution-free Al-Zn-Mg-Cu-C alloy. The specific steps are basically the same as in Embodiment 1, except that the petroleum coke content is 5 wt.%.

[0093] A heat-treated Al-Zn-Mg-Cu-C alloy product without solution treatment was obtained, with a yield strength, tensile strength, and elongation of 852 MPa, 915 MPa, and 8.1%, respectively.

[0094] Example 4,

[0095] This embodiment describes a solution-free Al-Zn-Mg-Cu-C alloy. The specific steps are basically the same as in Embodiment 1, except that the petroleum coke content is 0.1 wt.%.

[0096] A heat-treated Al-Zn-Mg-Cu-C alloy product without solution treatment was obtained, with a yield strength, tensile strength, and elongation of 596 MPa, 685 MPa, and 12.5%, respectively.

[0097] Example 5,

[0098] This embodiment describes a solution-free Al-Zn-Mg-Cu-C alloy. The specific steps are basically the same as in Embodiment 1, except that the average particle size of the powder is 200 μm.

[0099] A heat-treated Al-Zn-Mg-Cu-C alloy product without solution treatment was obtained, with a yield strength, tensile strength, and elongation of 776 MPa, 819 MPa, and 12.1%, respectively.

[0100] The above description is merely a preferred embodiment of the present invention and is not intended to limit the present invention. Although the present invention has been described in detail with reference to the foregoing embodiments, those skilled in the art can still modify the technical solutions described in the foregoing embodiments or make equivalent substitutions for some of the technical features. Any modifications, equivalent substitutions, improvements, etc., made within the spirit and principles of the present invention should be included within the protection scope of the present invention.

Claims

1. A method for preparing an Al-Zn-Mg-Cu-C alloy without solution treatment, characterized in that, The mixture comprises petroleum coke and Al-Zn-Mg-Cu matrix material in the following mass fractions: petroleum coke 0.1%~5%, and the Al-Zn-Mg-Cu matrix material comprising the following components by weight percentage: Zn 4.0%~8.4%, Mg 0.5%~3.3%, Cu 0.3%~2.6%, with Al as the balance; The preparation method of solution-free Al-Zn-Mg-Cu-C alloy includes the following steps: (1) Petroleum coke was uniformly mixed with Al, Zn, Mg and Cu element powders by low-speed ball milling to obtain Al-Zn-Mg-Cu-C alloy powder; (2) Pressing Al-Zn-Mg-Cu-C alloy powder; (3) The product obtained in step (2) is further processed to obtain carbon-reinforced aluminum-based composite material products; In step (1), the ball mill rotation speed is 100~200 rpm and the ball milling time is 10~30 h.

2. The method for preparing a solution-free Al-Zn-Mg-Cu-C alloy according to claim 1, characterized in that, The mass fraction of petroleum coke is 2% to 5%.

3. The method for preparing a solution-free Al-Zn-Mg-Cu-C alloy according to claim 1, characterized in that, The mass fraction of petroleum coke is 5%.

4. The method for preparing the solution-free Al-Zn-Mg-Cu-C alloy according to claim 1, characterized in that, In step (1), the Al, Zn, Mg and Cu element powders are gas atomized powders with an average particle size between 1 and 200 μm.

5. The method for preparing the solution-free Al-Zn-Mg-Cu-C alloy according to claim 1, characterized in that, In step (1), the contents of Zn, Mg and Cu are 8.4%, 2.3% and 2.5% respectively, and the average particle size is 1 μm.

6. The method for preparing the solution-free Al-Zn-Mg-Cu-C alloy according to claim 1, characterized in that, In step (2), the pressing pressure is higher than 100 MPa.

7. The method for preparing the solution-free Al-Zn-Mg-Cu-C alloy according to claim 1, characterized in that, In step (3), the subsequent processing methods include one or a combination of sintering, extrusion, forging and rolling.

8. The application of the solution-free Al-Zn-Mg-Cu-C alloy prepared by the method described in claim 1 in the preparation of vehicle structures and national defense weapons and equipment.

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