Aluminum base alloy, aluminum base alloy forge piece and preparation method of aluminum base alloy forge piece

Abstract

The invention relates to the technical field of alloys, and discloses an aluminum-based alloy, an aluminum-based alloy forge piece and a preparation method of the aluminum-based alloy forge piece. Wherein the aluminum-based alloy comprises Al, Zn, Mg and Cu. Wherein the content of each component is as follows in atomic mole percent: 70 mol%-85 mol% of Al, 5 mol%-10 mol% of Zn, 5 mol%-10 mol% of Mg and 5 mol%-10 mol% of Cu. By adopting the aluminum-based alloy provided by the invention, the lightweight requirement can be met, the aluminum-based alloy has higher yield strength and tensile strength, the cost is reduced, and the aluminum-based alloy has better plasticity and is easy to produce and process.

Description

Technical Field

[0001] The present application relates to the field of alloy technology, for example, to an aluminum-based alloy, an aluminum-based alloy forging and a preparation method thereof. Background Art

[0002] Lightweight high-entropy alloys have broad application prospects. For example, in the field of automobile manufacturing, they can be used in the manufacture of automobile engines, braking systems and other components to improve the safety and durability of automobiles. In the field of electronics, they can be used to manufacture laptop computer cases, folding screen mobile phone hinges, etc.

[0003] However, the currently developed lightweight high-entropy alloy systems usually include relatively expensive metals, such as lithium, titanium, nickel, etc., resulting in high costs for the prepared lightweight high-entropy alloys. In addition, the existing alloy systems also exhibit greater brittleness and processing difficulties, further limiting the practical application of lightweight high-entropy alloys. Summary of the invention

[0004] In order to provide a basic understanding of some aspects of the disclosed embodiments, a brief summary is given below. The summary is not an extensive review, nor is it intended to identify key / critical components or delineate the scope of protection of these embodiments, but rather serves as a prelude to the detailed description that follows.

[0005] The embodiments of the present disclosure provide an aluminum-based alloy, an aluminum-based alloy forging, and a method for preparing the same, thereby reducing the production cost of the aluminum-based alloy.

[0006] In some embodiments, an aluminum-based alloy is provided, comprising: Al, Zn, Mg and Cu; wherein, in terms of atomic molar percentage, the content of each component is as follows: 70 mol% to 85 mol% of Al, 5 mol% to 10 mol% of Zn, 5 mol% to 10 mol% of Mg, and 5 mol% to 10 mol% of Cu.

[0007] In some embodiments, a method for preparing an aluminum-based alloy forging is provided, comprising: melting an aluminum ingot, a zinc ingot, an aluminum-copper alloy, and a magnesium ingot to obtain a melt; pouring the melt into a mold, and ultrasonically treating the melt to obtain an ingot; homogenizing the ingot; forging the homogenized ingot for a first time to obtain a primary forging blank; quenching the primary forging blank, and then forging it for a second time to obtain an aluminum-based alloy forging; wherein, in terms of atomic molar percentage, the content of each component in the aluminum-based alloy forging is as follows: 70 mol% to 85 mol% of Al, 5 mol% to 10 mol% of Zn, 5 mol% to 10 mol% of Mg, and 5 mol% to 10 mol% of Cu.

[0008] In some embodiments, an aluminum-based alloy forging is provided, comprising: an aluminum-based alloy forging prepared by the method for preparing the aluminum-based alloy forging described in any of the above embodiments.

[0009] The aluminum-based alloy, aluminum-based alloy forging and preparation method thereof provided by the embodiments of the present disclosure can achieve the following technical effects:

[0010] The aluminum-based alloy provided by the present disclosure includes Al, Zn, Mg and Cu. The content of each component is, in terms of atomic mole percentage, 70 mol% to 85 mol% of Al, 5 mol% to 10 mol% of Zn, 5 mol% to 10 mol% of Mg, and 5 mol% to 10 mol% of Cu.

[0011] Compared with the components of lightweight high entropy alloys in the related art, the components of the aluminum-based alloy disclosed in the present invention use relatively low-priced Al, Zn, Mg and Cu, which can greatly reduce the cost of the aluminum-based alloy.

[0012] Furthermore, the atomic molar percentage of aluminum in the aluminum-based alloy is 70 mol% to 85 mol%, which, as the matrix of the multi-principal alloy, helps to improve the lightweight of the alloy. In addition, the atomic molar percentages of zinc, magnesium, and copper each account for 5 mol% to 10 mol%. Through the interaction of multiple elements, multiple strengthening phases can be formed to improve the yield strength and tensile strength of the multi-principal alloy. In this way, the aluminum-based alloy provided by the present disclosure can meet the lightweight requirements, have high yield strength and tensile strength, reduce costs, have good plasticity, and be easy to produce and process.

[0013] The above general description and the following description are exemplary and explanatory only and are not intended to limit the present application. BRIEF DESCRIPTION OF THE DRAWINGS

[0014] One or more embodiments are exemplarily described by corresponding drawings, which do not limit the embodiments. Elements with the same reference numerals in the drawings are shown as similar elements, and the drawings do not constitute a scale limitation, and wherein:

[0015] Figure 1 is a flow chart of a method for preparing an aluminum-based alloy forging provided by one embodiment of the present disclosure;

[0016] Figure 2 is a flow chart of a method for preparing an aluminum-based alloy forging provided by another embodiment of the present disclosure;

[0017] Figure 3 is a SEM image of the as-cast structure of the ingot after ultrasonic treatment during the preparation of the aluminum-based multi-principal alloy in Example 1 of the present disclosure;

[0018] Figure 4 is a SEM image of an ingot after homogenization treatment during the preparation of an aluminum-based multi-principal alloy in Example 1 of the present disclosure;

[0019] Figure 5 is a SEM image of the as-cast structure of the ingot after ultrasonic treatment during the preparation of the aluminum-based multi-principal alloy in Example 5 of the present disclosure;

[0020] Figure 6 is a SEM image of an ingot after homogenization treatment during the preparation of an aluminum-based multi-principal alloy in Example 5 of the present disclosure;

[0021] Figure 7 is a SEM image of the as-cast structure of the ingot after ultrasonic treatment during the alloy preparation process of Comparative Example 2;

[0022] Figure 8 This is a SEM image of the ingot after homogenization treatment during the alloy preparation process of Comparative Example 2. DETAILED DESCRIPTION

[0023] In order to be able to understand the features and technical contents of the embodiments of the present disclosure in more detail, the implementation of the embodiments of the present disclosure is described in detail below in conjunction with the accompanying drawings. The attached drawings are for reference only and are not used to limit the embodiments of the present disclosure. In the following technical description, for the convenience of explanation, a full understanding of the disclosed embodiments is provided through multiple details. However, one or more embodiments can still be implemented without these details. In other cases, to simplify the drawings, well-known structures, steps and devices can be simplified for display.

[0024] The terms "first", "second", etc. in the specification and claims of the embodiments of the present disclosure and the above-mentioned drawings are used to distinguish similar objects, and are not necessarily used to describe a specific order or sequence. It should be understood that the terms used in this way can be interchanged where appropriate, so that the embodiments of the embodiments of the present disclosure described herein. In addition, the terms "including" and "having" and any variations thereof are intended to cover non-exclusive inclusions.

[0025] Unless otherwise defined, all technical and scientific terms used in this document have the same meaning as commonly understood by technicians in the technical field to which this application belongs. The term "plurality" means two or more. In the disclosed embodiment, the character " / " indicates that the objects before and after are in an "or" relationship. For example, A / B means: A or B. The term "and / or" is a description of the association relationship between objects, indicating that three relationships can exist. For example, A and / or B means: A or B, or, three relationships of A and B.

[0026] It should be noted that, in the absence of conflict, the embodiments and features in the embodiments of the present disclosure may be combined with each other.

[0027] Those skilled in the art will appreciate that, in the methods of various embodiments or examples, the order in which the steps are written does not mean a strict order of execution and does not constitute any limitation on the implementation process, and the detailed order of execution of each step should be determined by its function and possible internal logic. Unless otherwise specified, all steps of the present application may be performed sequentially or randomly, preferably sequentially. For example, the method includes steps A and B, indicating that the method may include steps A and B performed sequentially, or steps B and A performed sequentially. For example, the method may further include step C, indicating that step C may be added to the method in any order, for example, the method may include steps A, B and C, or steps A, C and B, or steps C, A and B, etc.

[0028] In this application, in the open technical features or technical solutions described by the words "contain", "include", "include", etc., if there is no other explanation, additional members other than the listed members are not excluded, and it can be regarded as providing both closed features or solutions consisting of the listed members and open features or solutions including additional members in addition to the listed members. For example, A includes a1, a2 and a3. If there is no other explanation, it may also include other members or may not include additional members. It can be regarded as providing both the feature or solution of "A consists of a1, a2 and a3" and the feature or solution of "A includes not only a1, a2 and a3, but also other members".

[0029] The "range" disclosed in the present application can be defined in the form of a lower limit and an upper limit, and a given range is defined by selecting a lower limit and an upper limit, and the selected lower limit and upper limit define the boundaries of a particular range. The range defined in this way can be inclusive or exclusive of the end values, and any end value can be included or excluded independently, and can be arbitrarily combined, that is, any lower limit can be combined with any upper limit to form a range. For example, if a range of 60 to 120 and 80 to 110 is listed for a specific parameter, it is understood that the range of 60 to 110 and 80 to 120 is also expected. In addition, if the minimum range values ​​1 and 2 are listed, and if the maximum range values ​​3, 4 and 5 are also listed, the following ranges can all be expected: 1 to 3, 1 to 4, 1 to 5, 2 to 3, 2 to 4 and 2 to 5. In the present application, unless otherwise specified, the numerical range "a to b" represents an abbreviation of any real number combination between a and b, where a and b are both real numbers. For example, the numerical range "0-5" means that all real numbers between "0-5" are listed in this document, and "0-5" is just an abbreviation of these numerical combinations. In addition, when a parameter is expressed as an integer ≥ 2, it is equivalent to listing the parameter as, for example, integers 2, 3, 4, 5, 6, 7, 8, 9, 10, 11, 12, etc. For example, when a parameter is expressed as an integer selected from "2-10", it is equivalent to listing the integers 2, 3, 4, 5, 6, 7, 8, 9 and 10.

[0030] In this application, unless otherwise specified, A (such as B) means that B is a non-limiting example of A, and it can be understood that A is not limited to B.

[0031] In some embodiments, an aluminum-based alloy is provided, comprising: Al, Zn, Mg, and Cu. In terms of atomic molar percentage, the content of each component is as follows: 70 mol% to 85 mol% of Al, 5 mol% to 10 mol% of Zn, 5 mol% to 10 mol% of Mg, and 5 mol% to 10 mol% of Cu.

[0032] The aluminum-based alloy provided by the present disclosure adopts the Al-Zn-Mg-Cu quaternary system, forms a matrix-dominated high-entropy structure through a high proportion of Al (70 mol% to 85 mol%), and combines the solid solution and precipitation synergy of Zn, Mg, and Cu (5 mol% to 10 mol% each), while ensuring lightweight and realizing a multi-principal high mixed entropy effect. The Al matrix is ​​used to reduce the density, and Zn / Mg / Cu is strengthened by solid solution strengthening and subsequent precipitation phases, avoiding the problem of excessive density caused by equal molar ratios in traditional high-entropy alloys.

[0033] Compared with the components of lightweight high entropy alloys in the related art, the components of the aluminum-based alloy disclosed in the present invention use relatively low-priced Al, Zn, Mg and Cu, which can greatly reduce the cost of the aluminum-based alloy.

[0034] Furthermore, the atomic molar percentage of aluminum in the aluminum-based alloy is 70 mol% to 85 mol%, which, as the matrix of the high entropy alloy, helps to improve the lightweight of the alloy. In addition, the atomic molar percentages of zinc, magnesium and copper each account for 5 mol% to 10 mol%. Through the interaction of multiple elements, multiple strengthening phases can be formed to improve the yield strength and tensile strength of the alloy. In this way, the aluminum-based alloy provided by the present disclosure can meet the lightweight requirements, have high yield strength and tensile strength, reduce costs, have good plasticity, and be easy to produce and process.

[0035] Optionally, in terms of atomic mole percentage, specific values ​​of the Al content include but are not limited to: 70 mol%, 71 mol%, 72 mol%, 73 mol%, 74 mol%, 75 mol%, 76 mol%, 77 mol%, 78 mol%, 79 mol%, 80 mol%, 81 mol%, 82 mol%, 83 mol%, 84 mol% or 85 mol%.

[0036] Optionally, in terms of atomic mole percentage, specific values ​​of the Zn content include but are not limited to: 5 mol%, 6 mol%, 7 mol%, 8 mol%, 9 mol% or 10 mol%.

[0037] Optionally, in terms of atomic mole percentage, specific values ​​of the Mg content include but are not limited to: 5 mol%, 6 mol%, 7 mol%, 8 mol%, 9 mol% or 10 mol%.

[0038] Optionally, in terms of atomic mole percentage, specific values ​​of the Cu content include but are not limited to: 5 mol %, 6 mol %, 7 mol %, 8 mol %, 9 mol % or 10 mol %.

[0039] Optionally, the density of the aluminum-based alloy is less than or equal to 3.5 g / cm 3 , making aluminum-based alloys lighter and able to be used in aerospace, automobiles, high-speed trains and other fields.

[0040] Optionally, the tensile strength of the aluminum-based alloy is greater than or equal to 800 MPa, that is, the aluminum-based alloy has a higher load-bearing capacity.

[0041] Optionally, the yield strength of the aluminum-based alloy is greater than or equal to 680 MPa, that is, the aluminum-based alloy has good deformation resistance.

[0042] Optionally, the elongation of the aluminum-based alloy is greater than or equal to 5%, that is, the aluminum-based alloy has a certain plasticity and is easy to be formed and processed.

[0043] In this embodiment, the contents of Al, Zn, Mg and Cu are reasonably set to achieve high strength, high yield strength and appropriate plasticity while maintaining the lightness of the alloy. In this way, compared with the aluminum-based alloy in the related art, the production cost is reduced and the application range of the alloy is increased.

[0044] In some embodiments, in combination Figure 1 As shown, a method for preparing an aluminum-based alloy forging is provided, comprising:

[0045] S102, melting the aluminum ingot, the zinc ingot, the aluminum-copper alloy and the magnesium ingot to obtain a melt.

[0046] S104, pouring the melt into a mold, and subjecting the melt to ultrasonic treatment to obtain an ingot.

[0047] S106, homogenizing the ingot.

[0048] S108, performing the first forging on the homogenized ingot to obtain a primary forging blank.

[0049] S110, after quenching the primary forging blank, performing a second forging to obtain an aluminum-based alloy forging.

[0050] Among them, in terms of atomic molar percentage, the content of each component in the aluminum-based alloy forging is as follows: 70 mol% to 85 mol% of Al, 5 mol% to 10 mol% of Zn, 5 mol% to 10 mol% of Mg, and 5 mol% to 10 mol% of Cu.

[0051] In the preparation method of aluminum-based alloy forgings provided in the present disclosure, aluminum ingots, zinc ingots, aluminum-copper alloys and magnesium ingots are melted to obtain a uniform melt. The melting process enables the elements to be fully mixed to form a solid solution with uniform composition and no segregation, thereby increasing the entropy value of the alloy.

[0052] The melt is poured into the mold and ultrasonically treated. The mechanical vibration of ultrasound is used to continuously break up the dendrites to form new crystal nuclei, and finally a fine casting structure is obtained, laying a good foundation for subsequent plastic processing.

[0053] The ingot is homogenized so that a large amount of eutectic precipitated phases in the cast structure gradually dissolve and diffuse and dissolve back into the matrix to form an alloy structure of α solid solution + part of excess phase, eliminate component segregation and improve the uniformity of the alloy.

[0054] After homogenization, the first forging is performed, which will cause the lightweight high-entropy alloy to be fully broken from the cast structure to the deformed structure through forging, thereby improving the plasticity of the alloy. That is, after homogenization and the first forging, the grains of the ingot are refined, the internal stress is released, the dynamic recrystallization eliminates the casting porosity, and the elongation is increased, laying the foundation for subsequent heat treatment and final forging.

[0055] The primary forging blank after the first high-temperature forging is quenched to form a state with a supersaturated solid solution deformation structure. The primary forging blank with a supersaturated solid solution structure is forged for the second time, that is, medium-temperature forging, until the final forging size is obtained. A large number of deformation dislocations are generated in the lightweight high-entropy alloy through medium-temperature forging, which promotes the precipitation of fine precipitate phases in the matrix dislocations, so that the alloy produces obvious precipitation strengthening and work hardening effects. In this way, medium-temperature forging combined with homogenization treatment realizes "dislocation + precipitation + fine grain" multi-scale strengthening, improves the grain size and distribution of the alloy, and thus improves the tensile strength, yield strength and elongation of the forging.

[0056] The preparation method disclosed in the present invention combines ultrasonic casting with step homogenization to combine ultrasonic grain refinement with step homogenization to eliminate component segregation, thus overcoming the problem of coarse structure in traditional casting. Furthermore, through the composite strengthening path of high temperature forging → quenching → medium temperature forging, high temperature forging achieves dynamic recrystallization refinement, quenching achieves solid solution strengthening, and combined with the precipitation strengthening and work hardening effect achieved by medium temperature forging, the synergistic improvement of strength and plasticity is achieved.

[0057] The aluminum-based alloy forgings prepared by the preparation method provided by the present disclosure can obtain excellent mechanical properties, including high tensile strength, high yield strength and appropriate elongation, making them suitable for the needs of modern industry for lightweight, high-strength and corrosion-resistant materials.

[0058] Optionally, the step of melting the aluminum ingot, zinc ingot, aluminum-copper alloy and magnesium ingot to obtain the melt comprises: mixing the aluminum ingot, zinc ingot and aluminum-copper alloy and heating them. When the mixture is heated to a first temperature, a magnesium ingot is added and stirred to melt to obtain the melt.

[0059] In this embodiment, aluminum ingots, zinc ingots and aluminum-copper alloys are melted, and when the first temperature is reached, a magnesium ingot is pressed into the melt to melt, the melt is stirred evenly, and the surface scum is scraped off to obtain the melt. When the first temperature is reached, the magnesium ingot is pressed into the melt to melt. Magnesium is easily oxidized, and pressing it into the melt can reduce oxidation loss and ensure the accuracy of the alloy design composition.

[0060] Optionally, an aluminum ingot, a zinc ingot and an aluminum-copper alloy are added to a crucible resistance furnace for heating and melting. When heated to a first temperature, a magnesium ingot is added to the crucible resistance furnace, stirred and melted to obtain a melt. The crucible resistance furnace is used for smelting and adapted to the forging heat treatment process, with a simple process and high production efficiency, and low-cost large-scale industrial production can be achieved.

[0061] Optionally, the first temperature is 700°C to 750°C.

[0062] In this embodiment, considering the boiling point and melting point of magnesium, a temperature range of 700°C to 750°C is selected, which can fully melt the metal, avoid excessive burning of magnesium and reduce the evaporation of magnesium during the melting process, thereby maintaining the accuracy of the alloy composition. In addition, a higher melting temperature may cause grain growth and affect the mechanical properties of the final forging. The temperature of 700°C to 750°C can ensure melting and better control the grain size.

[0063] Optionally, specific values ​​of the first temperature include but are not limited to 700°C, 705°C, 710°C, 715°C, 720°C, 722°C, 724°C, 726°C, 728°C or 730°C.

[0064] Optionally, the purity of the aluminum ingots, zinc ingots, aluminum-copper alloys and magnesium ingots used for alloy smelting is greater than or equal to 99.9%, ensuring the purity of the alloy components and reducing the adverse effects of impurities on mechanical properties.

[0065] Optionally, the step of performing ultrasonic treatment on the melt includes: controlling an ultrasonic device to perform ultrasonic treatment on the melt according to a preset power and a preset frequency.

[0066] In this embodiment, the melt is ultrasonically treated according to a preset power and a preset frequency, and by setting appropriate power and frequency, an extremely fine and uniform cast structure is obtained, thereby improving the composition homogenization and microstructural refinement of the prepared aluminum-based alloy forgings, thereby improving the overall performance of the forgings and providing good conditions for the plastic deformation processing of lightweight high-entropy alloys.

[0067] Optionally, the conditions for ultrasonic treatment include: a preset power value of 1 kW to 3 kW; and / or a preset frequency of 1.5 kHz to 2.5 kHz.

[0068] In this embodiment, the power directly affects the propagation effect of the ultrasonic wave in the melt and the intensity of the cavitation effect. By setting the preset power value to 1kW to 3kW, the ultrasonic wave can effectively stir the melt, enhance the flow of the melt, promote the uniform distribution of elements, and reduce component segregation.

[0069] In this embodiment, the frequency determines the characteristics of ultrasonic vibration and affects its penetration ability and effect in the melt. By setting the preset frequency value to 1.5kHz to 2.5kHz, the ultrasonic wave can produce sufficient cavitation effect, which is conducive to the transmission effect of ultrasonic energy in the melt.

[0070] By subjecting the melt to ultrasonic treatment at 1kW to 3kW power and 1.5kHz to 2.5kHz frequency, the liquid alloy melt solidifies into an ingot under the action of ultrasonic waves. Ultrasonic waves are used to break dendrites through cavitation effect, and the acoustic streaming effect promotes the homogenization of components, significantly refines grains to micron level, and improves the uniformity of cast structure, providing a basis for subsequent plastic processing.

[0071] Optionally, specific values ​​of the preset power include but are not limited to 1 kW, 1.5 kW, 2 kW, 2.5 kW or 3 kW.

[0072] Optionally, the preset frequency has a value including but not limited to: 1.5kHz, 1.7kHz, 1.9kHz, 2kHz, 2.2kHz, 2.4kHz or 2.5kHz. Optionally, the mold is provided with a circulating cooling water system. The circulating cooling water can quickly absorb the heat of the melt, thereby accelerating the solidification rate. This helps to obtain a fine grain structure and improve the mechanical properties of the alloy. In addition, the mold absorbs a large amount of heat during the continuous pouring process. The circulating cooling water system utilizes the cooling water circulation to effectively take away the heat, prevent the mold from overheating, and maintain the stability of the mold temperature, thereby ensuring the quality of the casting and the life of the mold. The rapid cooling of the circulating cooling water system suppresses grain coarsening, and the double refinement effect is achieved in conjunction with ultrasound.

[0073] Optionally, the step of homogenizing the ingot includes: keeping the ingot at a first set temperature for a first time, heating the ingot to a second set temperature, and keeping the ingot at a second time.

[0074] In this embodiment, the microstructure of the ingot is improved by heating and heat preservation, and the component segregation is reduced to prepare for subsequent processing steps such as forging. The ingot is first kept at the first set temperature for a first time to allow the elements in the ingot to fully diffuse and reduce microsegregation. Then, the ingot is kept at the second set temperature for a second time to further promote the uniform distribution of elements, and the large amount of eutectic precipitation phases in the cast structure are gradually dissolved and diffused and dissolved back into the matrix to form an alloy structure of "α solid solution + part of the excess phase".

[0075] Optionally, the first set temperature is 450° C. to 465° C. and / or the first duration is 10 h to 24 h.

[0076] In this embodiment, by setting the first set temperature to 450°C to 465°C, the diffusion of elements can be promoted without causing excessive grain growth. By keeping the temperature at 450°C to 465°C for 10h to 24h, the recrystallization of the grains is promoted, the plasticity of the ingot is improved, and it is easier to form during the forging process. Optionally, the specific value of the first set temperature includes but is not limited to: 450°C, 455°C, 460°C, 461°C, 462°C, 463°C, 464°C or 465°C.

[0077] Optionally, specific values ​​of the first duration include but are not limited to: 10h, 12h, 14h, 16h, 18h, 20h, 22h or 24h.

[0078] Optionally, the second set temperature is 465° C. to 473° C. and / or the second duration is 10 h to 12 h.

[0079] In this embodiment, the second set temperature is slightly higher than the first set temperature. Keeping warm at a higher temperature can further promote the uniform distribution of elements, especially in the core of the ingot. In addition, keeping warm at 465°C to 473°C for 10h to 12h helps control the growth of grains, avoid excessive grain size, help adjust the microstructure of the ingot, and provide a better material basis for subsequent hot working. Optionally, the specific value of the second set temperature includes but is not limited to: 465°C, 468°C, 470°C, 471°C, 472°C or 473°C.

[0080] Optionally, specific values ​​of the second duration include but are not limited to: 10 hours, 11 hours or 12 hours.

[0081] By maintaining the temperature at 450°C ~ 465°C for 10h ~ 24h and then maintaining the temperature at 465°C ~ 473°C for 10h ~ 12h in a step-by-step heating process, the dissolution of the eutectic phase is promoted in the low temperature section, the atomic diffusion is accelerated in the high temperature section, the component segregation is eliminated, the structure dominated by α solid solution is formed, and the risk of subsequent forging cracking is reduced. The composition homogenization, microstructure optimization and plasticity improvement of the aluminum-based alloy ingot can be effectively achieved, providing a solid foundation for the preparation of high-performance forgings.

[0082] Optionally, the step of subjecting the homogenized ingot to a first forging to obtain a primary forging blank includes: cooling the homogenized ingot to a third set temperature, subjecting the ingot to a first forging, and making the temperature of the obtained primary forging blank greater than or equal to a fourth set temperature.

[0083] Optionally, the third set temperature is between 400°C and 450°C.

[0084] Optionally, the fourth set temperature is between 350°C and 400°C.

[0085] In this embodiment, the ingot after homogenization treatment is cooled to the third set temperature (400°C to 450°C) and the first forging is performed. In the range of 400°C to 450°C, the material still maintains good plasticity, which is conducive to deformation during the forging process. In addition, by performing high-temperature forging in the range of 400°C to 450°C, the lightweight high-entropy alloy is fully broken from the as-cast structure to the deformed structure, thereby breaking the as-cast structure, promoting the rearrangement and refinement of the grains, effectively eliminating casting defects, and improving the plasticity of the high-entropy alloy, thereby improving the mechanical properties of the material.

[0086] Furthermore, it is ensured that the temperature of the primary forging blank after forging is not lower than the fourth set temperature (350℃~400℃), so that the material maintains a sufficient temperature during the forging process to avoid the material from cooling rapidly after forging and becoming too hard, so as to maintain good plasticity, thereby providing good conditions for subsequent quenching and secondary forging.

[0087] Optionally, specific values ​​of the third set temperature include but are not limited to: 400°C, 405°C, 410°C, 415°C, 420°C, 425°C, 430°C, 435°C, 440°C, 445°C or 450°C.

[0088] Optionally, specific values ​​of the fourth set temperature include but are not limited to: 350°C, 360°C, 370°C, 380°C, 390°C or 400°C.

[0089] Optionally, the step of performing the second forging includes: heating the primary forging blank after quenching to a second temperature, and performing the second forging.

[0090] In this embodiment, after the quenching treatment, a second forging is performed until the final forging size is obtained. A large number of deformation dislocations are generated in the lightweight high-entropy alloy through medium-temperature forging, which promotes the precipitation of fine precipitates in the matrix dislocations, so that the alloy produces obvious precipitation strengthening and work hardening effects, resulting in a significant secondary strengthening effect, and the superposition of lattice distortion strengthening and work hardening effects greatly improves the strength of the alloy.

[0091] Optionally, the second temperature is between 200°C and 250°C.

[0092] In this embodiment, the second temperature is set to 200°C to 250°C, and the primary forging blank after quenching is subjected to medium-temperature forging. The second forging is performed in the temperature range of 200°C to 250°C to introduce high-density dislocations in the supersaturated solid solution, and promote the precipitation of fine precipitate phases in the matrix dislocations. In this way, the microstructure refinement, stress release, plasticity improvement, mechanical property optimization and organizational uniformity improvement of the aluminum-based alloy forgings are effectively achieved.

[0093] Optionally, specific values ​​of the second temperature include but are not limited to: 200°C, 210°C, 220°C, 230°C, 240°C or 250°C.

[0094] In some embodiments, in combination Figure 2 As shown, a method for preparing an aluminum-based multi-principal alloy forging is provided, comprising:

[0095] S202, melting the aluminum ingot, the zinc ingot, the aluminum-copper alloy and the magnesium ingot to obtain a melt.

[0096] By melting aluminum ingots, zinc ingots, aluminum-copper alloys and magnesium ingots, a uniform melt is obtained, which provides the basis for the preparation of high entropy alloys. The melting process ensures that the elements can be fully mixed to form a uniform alloy structure.

[0097] S204, using a nozzle with nano-scale pores to connect an inert gas to degas and refine the melt.

[0098] The degassing refining process lasts for 2 to 3 minutes.

[0099] The melt is degassed and refined for 2 to 3 minutes to remove gas and impurities in the melt and improve the purity of the melt. In addition, by setting 2 to 3 minutes, the dehydrogenation efficiency and production efficiency are balanced to avoid excessive cooling of the melt.

[0100] Optionally, the specific duration of the degassing refining includes but is not limited to: 2 min, 2.5 min or 3 min.

[0101] Optionally, a ceramic nozzle with nano-scale pores and an inert gas are used to degas and refine the melt, remove dissolved hydrogen in the melt, reduce pore defects, and improve the density and mechanical properties of the alloy. In this embodiment, a ceramic nozzle is used, and the wettability of the ceramic nozzle is poor, thereby reducing the risk of pores being blocked by the melt to improve the gas access effect. Inert gases are not easy to react with the components of the melt, and the degassing effect is improved by using inert gases. In addition, by injecting an inert gas (such as nitrogen and argon) into the melt, bubbles are used to absorb hydrogen and other impurities in the melt, and then the bubbles float up to take the gas out of the melt. The ceramic nozzle disperses the gas into fine bubbles, increases the contact area with the melt, and improves the degassing efficiency.

[0102] Optionally, the inert gas is selected from one or more of nitrogen and argon.

[0103] Optionally, before the inert gas is connected, the nozzle with nano-scale pores is preheated to 200°C to 300°C. That is, the ceramic nozzle with nano-scale pores is preheated to 200°C to 300°C, and the specific preheating temperature includes but is not limited to 200°C, 220°C, 240°C, 260°C, 280°C or 300°C. High-purity nitrogen is connected to degas and refine the melt, and the dissolved hydrogen elements are removed by a large number of fine bubbles in full contact with the melt. Nitrogen is an inert gas. By introducing nitrogen, the secondary oxidation of the melt is avoided, and the hydrogen in the melt is removed by physical adsorption to reduce casting pore defects. Among them, by preheating the ceramic nozzle to 200°C to 300°C, the temperature difference between the ceramic nozzle and the melt is reduced, thereby reducing damage to the nozzle and extending the service life of the ceramic nozzle. At the same time, nitrogen gas passes through the preheating nozzle: after the gas temperature rises from room temperature to 200-300°C, the volume expands, the flow rate increases, it is easier to break through the surface tension of the melt, and combined with nano-scale pores, tiny bubbles are formed to increase the gas-liquid contact area and improve the dehydrogenation efficiency.

[0104] S206, pouring the degassed and refined melt into a mold, and performing ultrasonic treatment on the melt to obtain an ingot.

[0105] The mechanical vibration of ultrasound is used to continuously break up the dendrites to form new crystal nuclei, forming small and uniform crystal nuclei and obtaining fine casting structure, which is beneficial to subsequent plastic processing.

[0106] S208, homogenizing the ingot.

[0107] The ingot is homogenized so that a large amount of eutectic precipitated phases in the cast structure gradually dissolve and diffuse and dissolve back into the matrix to form an alloy structure of α solid solution + part of excess phase, thereby improving the cast structure, reducing component segregation, and improving the uniformity and stability of the alloy.

[0108] S210, performing the first forging on the homogenized ingot to obtain a primary forging blank.

[0109] The ingot after homogenization treatment is forged at high temperature, so that the lightweight high entropy alloy is fully broken and transformed from the cast structure to the deformed structure, thereby improving the plasticity of the alloy.

[0110] S212, after quenching the primary forging blank, performing a second forging to obtain an aluminum-based multi-principal alloy forging.

[0111] The primary forging billet after high temperature forging is quenched to form a state with supersaturated solid solution deformation structure, which provides conditions for subsequent precipitation strengthening. The primary forging billet with supersaturated solid solution structure is forged at medium temperature until the final forging size is obtained. A large number of deformation dislocations are generated in the lightweight high entropy alloy through medium temperature forging, which promotes the precipitation of fine precipitate phases in the matrix dislocations, so that the alloy produces obvious precipitation strengthening and work hardening effects.

[0112] The preparation method of the aluminum-based alloy forging disclosed in the present invention improves plasticity through grain refinement and high-temperature forging, and significantly improves the strength of the alloy by utilizing the superposition effect of lattice distortion, work hardening and precipitation strengthening, so that the alloy has the advantages of high strength, high plasticity and low density. In addition, the preparation process is simple and the production efficiency is high, and low-cost large-scale industrial production can be achieved, overcoming the problems of high cost, high alloy brittleness, difficult processing and difficulty in large-scale production of current lightweight high-entropy alloys.

[0113] In some embodiments, an aluminum-based alloy forging is provided, including: prepared by the method for preparing an aluminum-based alloy forging of any of the above embodiments.

[0114] The aluminum-based alloy forging provided in the present disclosure is prepared by the method for preparing the aluminum-based alloy forging of any of the above embodiments, and thus has the technical effects described in any of the above embodiments, which will not be described in detail here.

[0115] The following specific examples are given to specifically illustrate the method for preparing the aluminum-based alloy forging according to the embodiment of the present disclosure, so as to more clearly illustrate the technical problems, technical solutions and beneficial effects solved by the present application. Obviously, the described embodiments are only part of the embodiments of the present application, not all of the embodiments. The following description of at least one exemplary embodiment is actually only illustrative and is by no means intended to limit the present application and its applications.

[0116] If no specific techniques or conditions are specified in the examples, the techniques or conditions described in the literature in the field or the product instructions are used. If no manufacturer is specified for the reagents or instruments used, they are all conventional products that can be purchased commercially.

[0117] Example 1

[0118] The aluminum-based alloy prepared in this embodiment has a composition of Al 70 Zn 10 Mg 10 Cu 10 .

[0119] Aluminum ingots, zinc ingots, and aluminum-copper alloy are added to the crucible resistance furnace, heated to 730°C to melt and fully stirred. Magnesium ingots are pressed into the melt to melt, and the melt is stirred and slag is removed.

[0120] The melt is degassed and refined for 2 minutes. The high entropy alloy melt is poured into a mold equipped with circulating cooling water, and the melt is ultrasonically treated with an ultrasonic power of 2Kw and a frequency of 2.2KHz. The liquid alloy solidifies into an ingot under the action of ultrasonic waves. Figure 3The SEM (Scanning Electron Microscope) image of the as-cast structure of the ingot after ultrasonic treatment is shown. Figure 3 As shown, after ultrasonic treatment, the precipitated phases in the as-cast structure are relatively uniform and fine.

[0121] The ingot was homogenized and the heat treatment process was: keep it at 465℃ for 20h, then keep it at 471℃ for 10h, so that a large amount of eutectic precipitated phase in the cast structure gradually dissolved and diffused and dissolved back into the matrix. Figure 4 The SEM image of the ingot after homogenization treatment is shown. Figure 4 As shown in the figure, a large amount of eutectic precipitated phases in the cast structure gradually dissolve and diffuse and dissolve back into the matrix to form an alloy structure of α solid solution + part of excess phase, which is evenly distributed.

[0122] The ingot is then cooled to 420°C for high temperature forging to obtain a primary forging blank, and the final forging temperature is greater than 350°C.

[0123] The high entropy alloy after high temperature forging is quenched to form a state with a supersaturated solid solution deformation structure.

[0124] After quenching, the primary forging blank is heated to 250°C for medium-temperature forging to obtain the final forging product.

[0125] Example 2

[0126] The aluminum-based alloy prepared in this embodiment has a composition of Al 75 Zn 10 Mg 10 Cu5.

[0127] Aluminum ingots, zinc ingots, and aluminum-copper alloy are added to the crucible resistance furnace, heated to 730°C to melt and fully stirred. Magnesium ingots are pressed into the melt to melt, and the melt is stirred and slag is removed.

[0128] The melt is degassed and refined for 2 minutes. The high entropy alloy melt is poured into a mold equipped with circulating cooling water, and the melt is ultrasonically treated with an ultrasonic power of 2Kw and a frequency of 2.2KHz. The liquid alloy solidifies into an ingot under the action of ultrasonic waves.

[0129] The ingot is homogenized and the heat treatment process is as follows: keeping it at 465°C for 20 hours and then keeping it at 471°C for 10 hours, so that a large amount of eutectic precipitation phase in the cast structure gradually dissolves and diffuses and dissolves back into the matrix. The ingot is then cooled to 420°C for forging to obtain a primary forging blank, and the final forging temperature is greater than 350°C.

[0130] The high entropy alloy after high temperature forging is quenched to form a state with a supersaturated solid solution deformation structure.

[0131] The primary forging blank is heated to 240°C for medium-temperature forging to obtain the final forging product.

[0132] Example 3

[0133] The aluminum-based alloy prepared in this embodiment has a composition of Al 80 Zn 10 Mg5Cu5.

[0134] Aluminum ingots, zinc ingots, and aluminum-copper alloy are added to the crucible resistance furnace, heated to 730°C to melt and fully stirred. Magnesium ingots are pressed into the melt to melt, and the melt is stirred and slag is removed.

[0135] The melt is degassed and refined for 2 minutes. The high entropy alloy melt is poured into a mold equipped with circulating cooling water, and the melt is ultrasonically treated with an ultrasonic power of 2Kw and a frequency of 2.2KHz. The liquid alloy solidifies into an ingot under the action of ultrasonic waves.

[0136] The ingot is homogenized and the heat treatment process is as follows: keeping it at 465°C for 20 hours and then keeping it at 471°C for 10 hours, so that a large amount of eutectic precipitation phase in the cast structure gradually dissolves and diffuses and dissolves back into the matrix. The ingot is then cooled to 420°C for forging to obtain a primary forging blank, and the final forging temperature is greater than 350°C.

[0137] The high entropy alloy after high temperature forging is quenched to form a state with a supersaturated solid solution deformation structure.

[0138] The primary forging blank is heated to 230°C for medium-temperature forging to obtain the final forging product.

[0139] Example 4

[0140] The aluminum-based alloy prepared in this embodiment has a composition of Al 73 Zn 10 Mg 10 Cu7.

[0141] Aluminum ingots, zinc ingots, and aluminum-copper alloy are added to the crucible resistance furnace, heated to 730°C to melt and fully stirred. Magnesium ingots are pressed into the melt to melt, and the melt is stirred and slag is removed.

[0142] The melt is degassed and refined for 2 minutes. The high entropy alloy melt is poured into a metal mold equipped with circulating cooling water, and the melt is ultrasonically treated with an ultrasonic power of 2Kw and a frequency of 2.2KHz. The liquid alloy solidifies into an ingot under the action of ultrasonic waves.

[0143] The ingot is homogenized and the heat treatment process is as follows: keeping it at 465°C for 20 hours and then keeping it at 471°C for 10 hours, so that a large amount of eutectic precipitation phase in the cast structure gradually dissolves and diffuses and dissolves back into the matrix. The ingot is then cooled to 420°C for forging to obtain a primary forging blank, and the final forging temperature is greater than 350°C.

[0144] The high entropy alloy after high temperature forging is quenched to form a state with a supersaturated solid solution deformation structure.

[0145] The primary forging blank is heated to 220°C for medium-temperature forging to obtain the final forging product.

[0146] Example 5

[0147] The aluminum-based alloy prepared in this embodiment has a composition of Al 85 Zn5Mg5Cu5.

[0148] Aluminum ingots, zinc ingots, and aluminum-copper alloy are added to the crucible resistance furnace, heated to 730°C to melt and fully stirred. Magnesium ingots are pressed into the melt to melt, and the melt is stirred and slag is removed.

[0149] The melt is degassed and refined for 2 minutes. The high entropy alloy melt is poured into a mold equipped with circulating cooling water, and the melt is ultrasonically treated with an ultrasonic power of 2Kw and a frequency of 2.2KHz. The liquid alloy solidifies into an ingot under the action of ultrasonic waves. Figure 5 Shown is the SEM image of the as-cast structure of the ingot after ultrasonic treatment. After ultrasonic treatment, the precipitated phases of the as-cast structure are relatively fine and evenly distributed.

[0150] The ingot was homogenized and the heat treatment process was: keep it at 465℃ for 10h, then keep it at 471℃ for 10h, so that a large amount of eutectic precipitated phase in the cast structure gradually dissolved and diffused and dissolved back into the matrix. Figure 6 The figure shows the SEM image of the ingot after homogenization treatment. A large amount of eutectic precipitated phases in the cast structure gradually dissolve, diffuse and dissolve back into the matrix to form an alloy structure of α solid solution + part of excess phase, which is evenly distributed.

[0151] The ingot is then cooled to 420°C for forging to obtain a primary forging blank, and the final forging temperature is greater than 350°C.

[0152] The high entropy alloy after high temperature forging is quenched to form a state with a supersaturated solid solution deformation structure.

[0153] The primary forging blank is heated to 230°C for medium-temperature forging to obtain the final forging product.

[0154] Comparative Example 1

[0155] The aluminum-based alloy prepared in this comparative example has a composition of Al92 Zn3Mg3Cu2.

[0156] Aluminum ingots, zinc ingots, and aluminum-copper alloy are added to the crucible resistance furnace, heated to 730°C to melt and fully stirred. Magnesium ingots are pressed into the melt to melt, and the melt is stirred and slag is removed.

[0157] The melt is degassed and refined for 2 minutes. The high entropy alloy melt is poured into a mold equipped with circulating cooling water, and the melt is ultrasonically treated with an ultrasonic power of 2Kw and a frequency of 2.2KHz. The liquid alloy solidifies into an ingot under the action of ultrasonic waves.

[0158] The ingot is homogenized and the heat treatment process is as follows: keeping it at 465°C for 10 hours and then keeping it at 471°C for 10 hours, so that a large amount of eutectic precipitation phase in the cast structure gradually dissolves and diffuses and dissolves back into the matrix. The ingot is then cooled to 420°C for forging to obtain a primary forging blank, and the final forging temperature is greater than 350°C.

[0159] The high entropy alloy after high temperature forging is quenched to form a state with a supersaturated solid solution deformation structure.

[0160] The primary forging blank is heated to 230°C for medium-temperature forging to obtain the final forging product.

[0161] Comparative Example 2

[0162] The aluminum-based alloy prepared in this comparative example has a composition of Al 55 Zn 15 Mg 15 Cu 15 .

[0163] Aluminum ingots, zinc ingots, and aluminum-copper alloy are added to the crucible resistance furnace, heated to 730°C to melt and fully stirred. Magnesium ingots are pressed into the melt to melt, and the melt is stirred and slag is removed.

[0164] The melt is degassed and refined for 2 minutes. The high entropy alloy melt is poured into a mold equipped with circulating cooling water, and the melt is ultrasonically treated with an ultrasonic power of 2Kw and a frequency of 2.2KHz. The liquid alloy solidifies into an ingot under the action of ultrasonic waves. Figure 7 The figure shows the SEM image of the as-cast structure of the ingot after ultrasonic treatment. The precipitated phases in the as-cast structure are large and uneven, which seriously reduces the plasticity of the alloy.

[0165] The ingot was homogenized and the heat treatment process was as follows: keeping the temperature at 460℃ for 20h and then keeping the temperature at 470℃ for 20h, so that a large amount of eutectic phases in the as-cast structure gradually dissolved and diffused and dissolved back into the matrix. Figure 8The SEM image of the ingot after homogenization treatment is shown, and it can be seen that the precipitated phase is relatively coarse and unevenly distributed, which affects the plasticity of the alloy. The ingot is then cooled to 420°C for forging.

[0166] The high entropy alloy after high temperature forging is quenched to form a state with a supersaturated solid solution deformation structure.

[0167] The alloy in this comparative example has poor plasticity and cannot be forged at medium temperature, so it is only subjected to high temperature aging treatment at 200°C / 15h.

[0168] The properties of the aluminum-based high entropy alloy forgings prepared in the above examples and comparative examples are shown in the following table.

[0169] Table 1 Performance test results of aluminum-based alloy forgings

[0170]

[0171] From the performance test results in Table 1, it can be seen that the aluminum-based alloy forgings prepared by the aluminum-based alloy and preparation method provided in the embodiments of the present invention have a tensile strength greater than or equal to 800 MPa, a yield strength greater than or equal to 680 MPa, an elongation greater than or equal to 5%, and a density less than or equal to 3.5 g / cm3.

[0172] It can be seen from Comparative Example 1 that a high aluminum content in the aluminum-based alloy will result in low tensile strength and yield strength. It can be seen from Comparative Example 2 that reducing the aluminum content and increasing the zinc, magnesium, and copper contents will result in low plasticity and high brittleness of the aluminum-based alloy, which is not easy to process and produce.

[0173] Compared with Comparative Examples 1 and 2, the aluminum-based alloy forgings prepared by the aluminum-based alloy and preparation method provided in the embodiments of the present invention have improved plasticity through grain refinement and high-temperature forging, and significantly improved the strength of the alloy by utilizing the superposition effect of lattice distortion, work hardening and precipitation strengthening, so that the alloy has the advantages of high strength, high plasticity and low density.

[0174] The technical features of the above-described embodiments may be arbitrarily combined. To make the description concise, not all possible combinations of the technical features in the above-described embodiments are described. However, as long as there is no contradiction in the combination of these technical features, they should be considered to be within the scope of this specification.

[0175] The above-mentioned embodiments only express several implementation methods of the present application, and the descriptions thereof are relatively specific and detailed, but they cannot be understood as limiting the scope of the invention patent. It should be pointed out that, for a person of ordinary skill in the art, several variations and improvements can be made without departing from the concept of the present application, and these all belong to the protection scope of the present application. Therefore, the protection scope of the patent of the present application shall be subject to the attached claims.

Claims

1. An aluminum-based alloy, characterized in that: include: Al, Zn, Mg and Cu; The contents of the components are as follows, in terms of atomic mole percentage: 70 mol % to 85 mol % of Al, 5 mol % to 10 mol % of Zn, 5 mol % to 10 mol % of Mg, and 5 mol % to 10 mol % of Cu.

2. The aluminum-based alloy according to claim 1, characterized in that The density of the aluminum-based alloy is less than or equal to 3.5 g / cm 3 and / or, The tensile strength of the aluminum-based alloy is greater than or equal to 800 MPa; and / or, The yield strength of the aluminum-based alloy is greater than or equal to 680 MPa; and / or, The elongation of the aluminum-based alloy is greater than or equal to 5%.

3. A method for preparing an aluminum-based alloy forging, characterized in that: include: Melting aluminum ingots, zinc ingots, aluminum-copper alloys and magnesium ingots to obtain a melt; pouring the melt into a mold, subjecting the melt to ultrasonic treatment to obtain an ingot; Homogenizing the ingot; The homogenized ingot is forged for the first time to obtain a primary forging blank; After the primary forging blank is quenched, it is forged a second time to obtain an aluminum-based alloy forging; Among them, in terms of atomic molar percentage, the content of each component in the aluminum-based alloy forging is as follows: 70 mol% to 85 mol% of Al, 5 mol% to 10 mol% of Zn, 5 mol% to 10 mol% of Mg, and 5 mol% to 10 mol% of Cu.

4. The preparation method according to claim 3, characterized in that: The step of melting the aluminum ingot, the zinc ingot, the aluminum-copper alloy and the magnesium ingot to obtain a melt comprises: The aluminum ingot, the zinc ingot and the aluminum-copper alloy are mixed and heated; When heated to the first temperature, adding magnesium ingot, stirring and melting to obtain a melt; Preferably, the first temperature is 700°C to 750°C.

5. The preparation method according to claim 3 or 4, characterized in that: The conditions of the ultrasonic treatment include: The preset power is 1 kW to 3 kW; and / or the preset frequency is 1.5 kHz to 2.5 kHz.

6. The preparation method according to any one of claims 3 to 5, characterized in that: The step of homogenizing the ingot comprises: The ingot is kept at a first set temperature for a first time period; Raise the temperature to the second set temperature and keep warm for the second time; Preferably, the first set temperature is 450° C. to 465° C., and / or the first duration is 10 h to 24 h; Preferably, the second set temperature is 465° C. to 473° C., and / or the second duration is 10 h to 12 h.

7. The preparation method according to any one of claims 3 to 6, characterized in that: The step of forging the homogenized ingot for the first time to obtain a primary forging blank comprises: Cooling the homogenized ingot to a third set temperature, performing a first forging, and making the temperature of the obtained primary forging blank greater than or equal to a fourth set temperature; Preferably, the third set temperature is 400°C to 450°C; Preferably, the fourth set temperature is between 350°C and 400°C.

8. The preparation method according to any one of claims 3 to 7, characterized in that: The steps of performing the second forging include: heating the quenched primary forging blank to a second temperature and performing a second forging; Preferably, the second temperature is between 200°C and 250°C.

9. The preparation method according to any one of claims 3 to 8, characterized in that: Before the step of pouring the melt into the mold and subjecting the melt to ultrasonic treatment, the preparation method further comprises: The inert gas is connected to the nozzle with nano-scale pores to degas and refine the melt; Preferably, the duration of degassing refining is 2 to 3 minutes; Preferably, before the inert gas is connected, the nozzle of the nano-scale pores is preheated to 200° C. to 300° C.; Preferably, the inert gas is selected from one or more of nitrogen and argon.

10. An aluminum-based alloy forging, characterized in that: include: The aluminum-based alloy forging is prepared by the preparation method of any one of claims 3 to 9.

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