A production method of high-strength high-silicon aluminum alloy with quick extrusion by using recycled waste aluminum

Abstract

The application discloses a production method of high-strength high-silicon aluminum alloy which can be quickly extruded by using recycled waste aluminum, and comprises the following steps: crushing and screening aluminum waste to leave aluminum-containing fragments, and sorting the aluminum-containing fragments to obtain aluminum material; preheating the aluminum material and melting the aluminum material into a liquid aluminum melt A; refining the melt A, stirring and skimming, and blowing gas to remove hydrogen; adjusting the components of the refined melt to obtain an aluminum alloy melt B; adding AlTiB wires into the melt B, and obtaining a melt C after online degassing and filtration; casting the melt C to obtain an aluminum alloy round ingot D; and homogenizing annealing the round ingot D to obtain an aluminum alloy round ingot E, and completing the production and processing of the high-strength high-silicon aluminum alloy. The application uses recycled waste aluminum as the raw material, has high tolerance for the contents of Si and Fe, realizes the level-keeping utilization of the waste aluminum, solves the immature problem of the use of the recycled aluminum in the extruded profiles, and has important significance for the recycling of aluminum resources and the sustainable development of the aluminum production industry.

Description

Technical Field

[0001] This invention relates to the field of non-ferrous metals technology, specifically to a production method for manufacturing high-strength, high-silicon aluminum alloys that can be rapidly extruded using recycled waste aluminum. Background Technology

[0002] Aluminum alloys, due to their high strength, light weight, corrosion resistance, and long service life, have become the second most widely used alloy globally. Extruded aluminum rods are made by melting and casting aluminum ingots, and bauxite, the raw material for producing aluminum ingots, is a non-renewable resource. In my country, the proven reserves of bauxite have less than 30 years of exploitable time remaining. Therefore, using scrap aluminum as a raw material to produce aluminum alloys not only conserves the limited bauxite resources but also significantly achieves energy conservation and emission reduction.

[0003] Specifically, the energy consumption of recycled aluminum is only 3%-5% of that of electrolytic aluminum. For every ton of recycled aluminum produced, the emissions of carbon dioxide and sulfur oxides are reduced by 0.8 tons and 0.06 tons respectively compared to the traditional primary aluminum production process, water resources are saved by 10.5 tons, and the discharge of waste residue, waste liquid and solid waste is also significantly reduced, resulting in significant energy conservation and emission reduction effects.

[0004] Internationally, some developed countries have established relatively mature aluminum recycling systems. Currently, these countries' annual recycled aluminum production exceeds half of their total aluminum production, generally remaining around 70%, while Japan's figure is over 99%. In contrast, my country's recycled aluminum production accounts for less than 20%, and a comprehensive waste aluminum recycling system has not yet been established. Therefore, promoting the recycling and utilization of recycled aluminum is urgently needed.

[0005] The recycling of recycled aluminum mainly falls into two categories: downgrading and preservation. Downgrading involves simply processing scrap aluminum alloys for use in applications with lower performance requirements, such as low-end cast aluminum alloys. In my country's recycled aluminum industry, a large amount of scrap aluminum is downgraded, which not only fails to fully realize its potential value but also results in significant resource waste. Preservation, on the other hand, uses technological means to reuse scrap aluminum alloys in high-performance applications, such as the aerospace industry. However, due to the complex origins of recycled aluminum, achieving preservation faces numerous challenges, including high equipment costs, complex processes, and stringent requirements for the quality and origin of the scrap aluminum.

[0006] In the preservation and utilization of recycled aluminum alloys, the extrusion process is particularly important, but current technology still faces bottlenecks, namely, the inability to achieve rapid extrusion of recycled aluminum alloys. Although domestic and foreign research institutions and enterprises have conducted extensive research on the recycling and utilization of recycled aluminum in recent years and have achieved certain results, rapid extrusion technology remains insufficient.

[0007] For example, patent CN 112176200A discloses a recycling process for aluminum die-casting waste, but does not address the extrudability of the alloy; patent CN Patent 111926186A proposes an aluminum alloy recycling process but does not analyze the subsequent properties of the alloy; Patent CN200510002497.1 achieves rapid extrusion by cooling the mold and profile with nitrogen and liquid nitrogen; Patents CN202210622378.X, CN201910899542.X, and CN201910898972.X achieve rapid extrusion by adding rare earth elements to improve the microstructure; Patent CN202210597369.X refines the grains by adding Al-5Ti-B alloy refiner and combines it with stirring and vibration to achieve low-temperature rapid extrusion; Patent CN201410596826.9 achieves low-temperature rapid extrusion by controlling the Mg and Si content and the decompression angle of the flow divider to reduce the temperature of the aluminum rod; Patent CN202122576938.6 utilizes the multi-level distribution of the flow divider to reduce the extrusion pressure on the bearing surface and the mold, thereby increasing the extrusion speed.

[0008] Although the above research has made some progress in certain aspects, there is still a lack of a mature production method that can manufacture high-strength, high-silicon aluminum alloys that can be rapidly extruded from recycled aluminum scrap.

[0009] Therefore, how to overcome the shortcomings of the existing technology is the subject of this invention. Summary of the Invention

[0010] The purpose of this invention is to provide a method for manufacturing high-strength, high-silicon aluminum alloys that can be rapidly extruded using recycled waste aluminum.

[0011] To achieve the above objectives, the technical solution adopted by the present invention is as follows:

[0012] A method for producing a high-strength, high-silicon aluminum alloy that can be rapidly extruded using recycled aluminum waste includes:

[0013] Step 1: Pre-process the aluminum scrap, including crushing and sorting, to obtain aluminum material;

[0014] Step 2: Preheat the aluminum material to remove moisture and some organic matter; then melt the preheated aluminum material to obtain melt A.

[0015] Step 3: Refine melt A by stirring and skimming to remove inclusions from melt A;

[0016] Step 4: Transfer the refined melt A to the alloying furnace, adjust the composition to obtain aluminum alloy melt B;

[0017] Step 5: Add AlTiB wire as a grain refiner to melt B, the amount added is 0.1-0.15% of the weight of melt B; then degas and filter melt B online to obtain melt C;

[0018] Step 6: Cast the melt C to obtain aluminum alloy round ingot D;

[0019] Step 7: Homogenize and anneal the round ingot D, and after cooling, obtain aluminum alloy round ingot E, thus completing the production and processing of high-strength, high-silicon aluminum alloy.

[0020] In the above scheme, the aluminum scrap is preferably primary and secondary aluminum scrap, conforming to standard GB / T 34640.1-2017. The non-metallic impurities include plastics, cardboard, etc. The paint stripping process is carried out in a rotary kiln. The purity of the aluminum material obtained in step one is higher than that of the aluminum scrap.

[0021] A further technical solution is to utilize the high-temperature flue gas emitted from the melting chamber for preheating in step two, thereby achieving effective energy saving.

[0022] A further technical solution involves a high-strength, high-silicon aluminum alloy comprising the following components by mass percentage:

[0023] Si 4.0-4.9%, Mg 0.6-0.9%, Cu≤0.1%, Mn 0.36-0.72%, Cr≤0.1%, Fe 0.3-0.6%, Sr 0.05-0.4%, Zn≤0.25%, Ni≤0.05%, Ti≤0.15%, with the balance being Al; and each individual impurity element ≤0.05%.

[0024] In step four, the adjustment of the composition is carried out with the above-mentioned components as the target. Before adjustment, the composition of the molten aluminum is first confirmed by a composition analyzer to determine whether it is necessary to add any elements and the amount of each element to be added.

[0025] In a further technical solution, in step one, the pretreatment is as follows: aluminum waste is fed into a crusher for crushing and screening, leaving aluminum-containing fragments with a diameter of less than 110mm. Then, iron-containing impurities in the aluminum-containing fragments are removed by magnetic separation, non-metallic impurities are removed by eddy current separation, and finally, X-ray separation and paint removal are performed to obtain the aluminum material.

[0026] In step two, the aluminum material preheating process is as follows: the aluminum material is sent into the preheating chamber and preheated to 400-500°C for 20-30 minutes; the aluminum material melting process after preheating is as follows: the preheated aluminum material is transferred to the melting chamber through a closed channel and heated to 700-750°C in the melting chamber to melt into liquid aluminum, thereby obtaining the melt A;

[0027] In step three, the refining process is as follows: a refining agent is added to melt A, and melt A is stirred at least twice. The stirring speed for each stirring operation is 300-800 rpm and the time is 8-12 minutes. After each stirring operation, the mixture is allowed to stand for at least 5 minutes. After standing, the inclusions in melt A are removed by skimming.

[0028] While refining melt A, inert gas is continuously introduced into the melting chamber to remove hydrogen from the melting chamber;

[0029] In step four, when adjusting the composition of melt A, the temperature of melt A is controlled at 720-740℃;

[0030] In step seven, the round ingot D is subjected to homogenization annealing. First, it is heated to 550°C at a heating rate of 90°C / h, then held at that temperature for 8 hours, and finally removed from the furnace and water-cooled. After cooling, the aluminum alloy round ingot E is obtained.

[0031] In a further technical solution, in step five, the TiAl3 phase in the AlTiB filament is uniformly distributed within the AlTiB filament, with a TiAl3 phase density ≥ 120 phases / mm². 2 Furthermore, the size of each TiAl3 phase is less than 25 μm.

[0032] Further technical solutions also include step eight: heating the round ingot E to 490°C and then extruding it, followed by online water cooling and quenching to obtain the aluminum profile F;

[0033] The aluminum profile F was artificially aged at an extrusion speed of 5-7.5 mm / s, with an aging regime of 175℃ and a holding time of 8 hours, to obtain a high-strength, high-silicon aluminum alloy profile. During extrusion, the extrusion ratio was controlled at 70.

[0034] A further technical solution involves step eight, during extrusion, where the extrusion die adopts a flow guide design, and the number of flow dividers is greater than or equal to four, with the thickness D of the flow guide plate ≥ The depth H of the welding chamber is (5~6). The diameter of the aluminum rod is the same as the diameter of the round ingot E.

[0035] The thickness of the guide plate and the depth of the welding chamber are both in mm.

[0036] In a further technical solution, during step eight, the length L1 of the die working belt is 2-6 mm, the length L2 of the part in contact with the aluminum rod is 0.2-0.5 mm, and the remaining part of the working belt has an inclination angle α of 5-10°.

[0037] In the above scheme, the remaining part of the working belt is the part of L1 minus L2.

[0038] In the above scheme, the thickness D of the guide plate and the depth H of the welding chamber are both in mm.

[0039] A further technical solution includes an upper mold and a lower mold, wherein the upper mold is the guide plate; and the welding chamber is formed between the upper mold and the lower mold.

[0040] In a further technical solution, the upper mold has four feeding cavities, and the lower mold has one discharging cavity.

[0041] In a further technical solution, the welding chamber located on the upper surface of the lower mold is cross-shaped, and the cross-shaped portion is aligned with the four feeding chambers of the upper mold in the vertical direction.

[0042] In a further technical solution, the discharge chamber is cross-shaped.

[0043] In a further technical solution, the highest point of the welding chamber is located in the middle of the upper surface of the lower mold, and the number of such points is four.

[0044] The lowest point of the welding chamber is recessed on the upper surface of the lower mold and located on the side of the circumferential direction of each highest point.

[0045] In a further technical solution, in step three, the stirring operation is performed using a stirring paddle;

[0046] The impeller includes bottom blades, middle blades and upper blades arranged axially from bottom to top at intervals;

[0047] The bottom blades serve as propulsion blades for the upward flow of molten aluminum, and their blades form an angle of 35-55° with the horizontal plane.

[0048] The middle blade is a variable cross-section blade, and the thickness of each blade gradually decreases from the root to the tip, and a serrated structure is provided on the edge of the blade; several spiral grooves are opened on the surface of the blade.

[0049] The upper blades are an anchor-type blade assembly, consisting of an outer layer and an inner layer; the outer layer is an upwardly curved arc-shaped stirring rod, and the inner layer is a guide blade with protrusions.

[0050] A further technical solution involves placing the stirring paddle within a molten pool, with the diameter of the bottom blades being 0.7-0.85 times the diameter of the bottom of the molten pool. This design allows the bottom blades to expand the stirring coverage area at the bottom of the molten pool, pushing the molten aluminum upwards.

[0051] In a further technical solution, each blade of the bottom blade has several protrusions evenly distributed on its upper surface, and several grooves are provided at intervals.

[0052] In a further technical solution, the outer edge of each blade of the bottom blade is an arc-shaped curve.

[0053] In a further technical solution, the diameter of the middle blade is larger than that of the bottom blade, and the main body of each blade of the middle blade is designed to be straight.

[0054] In a further technical solution, there are two arc-shaped stirring rods on the outer layer of the upper blade, which are arranged symmetrically.

[0055] In a further technical solution, the guide vanes in the inner layer of the upper blade are arranged radially upwards.

[0056] In a further technical solution, the stirring paddle is configured to have a heat-resistant alloy steel body and a nitrided surface.

[0057] In the above scheme, the protrusions are used to further disrupt the flow of molten aluminum.

[0058] In the above scheme, the special blade structure of the bottom blade can enhance the turbulence generated when the blade pushes the aluminum liquid, increase the collision and shearing opportunities with Si, Fe and Mn particles, and use the turbulence to stir up the Fe and Mn particles deposited at the bottom, creating conditions for subsequent uniform distribution.

[0059] In the above design, the edge of the middle blade is serrated with a spacing of 10-15 mm and a depth of 5-8 mm; several spiral grooves with a depth of 2-3 mm are formed on the blade surface. Through these design requirements, the middle blade significantly enhances the shear force and vortex effect on the molten aluminum during blade rotation, causing Si particles to be dispersed and sphericalized in the complex flow field. Simultaneously, Fe and Mn particles lifted from the bottom are fully dispersed radially, resulting in better connection between the bottom and top molten aluminum. This structure significantly enhances the shear force and vortex effect on the molten aluminum during blade rotation, and the spiral grooves guide the molten aluminum to form a local spiral flow, increasing the opportunity for element mixing, ensuring thorough mixing of the molten aluminum throughout the molten pool, and promoting the uniform distribution of Si, Fe, and Mn particles.

[0060] In the above scheme, the upper blades can change the flow direction of the molten aluminum at the top, forming a complex circulating flow field and preventing Si, Fe, and Mn particles from accumulating at the top. Furthermore, the stirring process does not damage the top covering agent and oxide layer, ensuring that the molten aluminum is not subject to secondary contamination. Through a special flow field design, the Si, Fe, and Mn particles, after being treated at the bottom and middle sections, are further evenly dispersed at the top, avoiding local concentration differences and enhancing the stirring effect on the entire molten aluminum pool.

[0061] The protrusions are used to further disrupt the flow of molten aluminum, and can be implemented using circular protrusions with a diameter of 8-10mm.

[0062] A further technical solution involves making the stirring paddle from heat-resistant alloy steel, and subjecting its surface to nitriding treatment. This enhances surface hardness and anti-adhesion properties, preventing the adhesion of Si, Fe, and Mn particles and ensuring that the stirring effect remains unaffected.

[0063] The terms “include,” “including,” and “have” used in this article are all open-ended, meaning they include but are not limited to.

[0064] Unless otherwise specified, the terms used herein generally have their ordinary meaning in the context of the art, the subject matter, and the specific context. Certain terms used to describe this case will be discussed below or elsewhere in this specification to provide additional guidance to those skilled in the art in describing the case.

[0065] The working principle and advantages of this invention are as follows:

[0066] This invention utilizes recycled aluminum as raw material, exhibiting strong tolerance for Si and Fe content. By adjusting the alloy composition, a high-strength, high-silicon aluminum alloy capable of rapid extrusion is ultimately obtained using recycled aluminum. This successfully achieves the preservation and utilization of recycled aluminum, solving the current problem of the immature application of recycled aluminum in extruded profiles in my country. It has significant practical implications for aluminum resource recycling, cost savings in aluminum ingots and profiles, and the sustainable development of the aluminum production industry.

[0067] Furthermore, the Si content of this invention is 4.0-4.9%, which has a large tolerance for different types of scrap aluminum in the raw materials. This is because recycled aluminum contains some cast aluminum alloys, and the Si content of cast aluminum alloys is much higher than that of extrudable wrought aluminum alloys, thus greatly increasing the Si content in the alloy. The Si content in this invention exceeds the Si content of 6XXX series wrought aluminum alloys (for example, the Si content of a certain 6-series aluminum alloy is 0.4-0.8%). The Si element mainly exists in the alloy in the form of spherical elemental Si, and its content reaches the range of cast aluminum alloys. However, it can still be used with reference to wrought aluminum alloy extrusion, and the final profile has good performance and high tensile and yield strength.

[0068] Furthermore, the three-layer stirring blade design of this invention can effectively remove hydrogen from the melt, promoting the homogenization of the melt composition. The bottom blades push the bottom aluminum liquid upwards and, with their special blade structure, increase the opportunities for collision and shearing with Si, Fe, and Mn particles. In particular, for Fe and Mn particles, turbulence is used to stir them up from the bottom deposit layer of the molten pool, creating conditions for subsequent uniform distribution. The middle blades are not only responsible for radially dispersing the aluminum liquid, but also promote the spheroidization of Si particles and the uniform distribution of Fe and Mn particles in the aluminum liquid under strong shear force and vortex action. The upper blades, through a special flow field design, further uniformly disperse the Si, Fe, and Mn particles that have been treated at the bottom and middle sections at the top, avoiding local concentration differences. This invention guides the aluminum liquid to form a local spiral flow through an original spiral groove, increasing the opportunity for element mixing. In addition, the serrated structure at the end, the protrusions on the blades, and the arc-shaped stirring rods effectively disperse the Si, Fe, Mn, and other phases.

[0069] Furthermore, this invention strictly controls the grade of the grain refiner: TiAl3 grains are uniformly distributed throughout the refined filaments, and the size of the TiAl3 grains is controlled to be below 25 μm, with a density of not less than 120 grains / mm. 2 Through repeated experiments and summaries, aluminum rods cast using high-quality grain refiners exhibited superior surface finish, a lack of coarse grains, and higher mechanical properties in the final extruded profiles. Furthermore, the anodized profiles showed very few defects such as streaks or white lines. The final extruded profiles demonstrated a superior surface quality compared to those produced using cast rods cast with ordinary-grade grain refiners.

[0070] Furthermore, the extrusion ratio of the product extruded in this invention is controlled between 60 and 140. In the industry, the extrusion ratio is typically between 20 and 60. The purpose of increasing the extrusion ratio in this invention is to increase the pressure during the extrusion process, increase the flow stress and strain rate, and promote the breakage of elemental Si. Under high stress, dislocations multiply more rapidly, and the high pressure promotes grain boundary migration and recrystallization nucleation, thus refining the grains. Specifically, increasing the extrusion ratio can be achieved by increasing the tonnage of the extruder, i.e., placing the product on a large-tonnage extruder. In addition, the die uses a flow guide die (with ≥4 flow bridges), and the thickness of the flow guide plate is increased on the conventional basis. These two measures, besides enhancing the overall deformation resistance of the flow guide plate, are also intended to further increase the extrusion pressure, promote deformation, accelerate the breakage of elemental Si, refine the grains, and enhance the alloy strength.

[0071] Furthermore, the welding chamber of this invention is deeper than that of conventional molds, where the welding chamber is typically designed to be H deep. 常 =(3~5) This invention increases the depth of the welding chamber to H = (5~6). The purpose is to strengthen the welding and compensate for the poor welding caused by the presence of the shunt bridge.

[0072] Furthermore, this invention shortens the working strip of the die, with an effective length of only 0.2-0.5mm, avoiding increased pressure caused by changes in the previous machine selection and die structure. Additionally, the extremely short working strip aims to reduce friction between elemental silicon and the working strip, allowing aluminum to quickly deform into profiles. This facilitates rapid extrusion and helps maintain a smooth profile surface, reducing the occurrence of cracks, scratches, and other defects. Attached Figure Description

[0073] Appendix Figure 1 This is a schematic diagram of the method flow of Embodiment 1 of the present invention;

[0074] Appendix Figure 2 This is a cross-sectional schematic diagram of the extrusion die according to Embodiment 1 of the present invention;

[0075] Appendix Figure 3 for Figure 2 Enlarged view of point I in the middle;

[0076] Appendix Figure 4 This is a side view of the extrusion die according to Embodiment 1 of the present invention;

[0077] Appendix Figure 5 for Figure 4 Sectional view along the middle AA direction;

[0078] Appendix Figure 6 This is a top view of the extrusion die according to Embodiment 1 of the present invention;

[0079] Appendix Figure 7 for Figure 6 Sectional view along the BB direction;

[0080] Appendix Figure 8 for Figure 6 Sectional view along the DD direction;

[0081] Appendix Figure 9 The shape of the secondary welding chamber in the extrusion die of Embodiment 1 of the present invention (top view angle);

[0082] Appendix Figure 10 This is a top view of an embodiment of the present invention;

[0083] Appendix Figure 11 for Figure 10 A cross-sectional view along the CC direction;

[0084] Appendix Figure 12 This is a schematic diagram of the structure of the stirring paddle in Embodiment 1 of the present invention;

[0085] Appendix Figure 13 This is an electron microscope image of the AlTiB filament added in step five of Embodiment 1 of the present invention;

[0086] Appendix Figure 14 This is a metallographic image of the round ingot D before homogenization annealing in step seven of Embodiment 1 of the present invention;

[0087] Appendix Figure 15 The image shows the metallographic structure of the round ingot D after homogenization annealing in step seven of Embodiment 1 of the present invention.

[0088] Appendix Figure 16 This is a photograph of the profile product of Embodiment 1 of the present invention;

[0089] Appendix Figure 17 This is a photograph of the profile product of Comparative Example 1 of the present invention;

[0090] Appendix Figure 18 This is a photograph of the profile product of Comparative Example 2 of the present invention;

[0091] Appendix Figure 19 This is a photograph of the profile product of Comparative Example 3 of the present invention;

[0092] Appendix Figure 20 This is a photograph of the profile product of Comparative Example 4 of the present invention;

[0093] Appendix Figure 21 This is a photograph of the profile product of Comparative Example 5 of the present invention;

[0094] Appendix Figure 22 This is a photograph of the profile product of Comparative Example 6 of the present invention.

[0095] In the attached diagrams: 1. Guide plate (upper mold); 2. Diverter bridge; 3. Welding chamber; 4. Working zone; D. Thickness of guide plate; H. Depth of welding chamber; L1. Length of mold working zone; 8. Part in contact with aluminum rod; L2. Length of part in contact with aluminum rod; α. Inclined angle; 5. Lower mold; 6. Feed chamber; 7. Discharge chamber; 9. Secondary welding chamber; P1. High point of welding chamber; P2. Low point of welding chamber; 11. Bottom blade; 12. Middle blade; 13. Upper blade; 14. Protrusion; 15. Groove; 16. Serrated structure; 17. Spiral groove; 31. Arc-shaped stirring rod; 32. Guide blade. Detailed Implementation

[0096] The present invention will be further described below with reference to the accompanying drawings and embodiments:

[0097] The present invention will be clearly described below with illustrations and detailed description. Any person skilled in the art who understands the embodiments of the present invention can make changes and modifications based on the technology taught in the present invention without departing from the spirit and scope of the present invention.

[0098] The terminology used herein is for the purpose of describing specific embodiments only and is not intended to limit the scope of this work. Singular forms such as “a,” “this,” “this,” “the,” and “the” as used herein also include plural forms. Example

[0099] like Figure 1 As shown, a method for manufacturing a high-strength, high-silicon aluminum alloy that can be rapidly extruded using recycled waste aluminum includes:

[0100] Step 1: Feed the aluminum scrap into a crusher for crushing and screening, leaving aluminum-containing fragments with a diameter of less than 110mm. Then, use a permanent magnet (or electromagnetic) magnetic separator to remove iron-containing impurities (such as large pieces of iron, small pieces of iron, and aluminum-clad iron) from the aluminum fragments.

[0101] Aluminum fragments are separated into aluminum blocks using eddy current separation. Non-metallic materials such as granules, plastics, and cardboard are removed from the separation. The aluminum blocks are then X-ray separated to obtain aluminum material, while copper and zinc are removed. Finally, the material is sent to a rotary kiln for paint removal to obtain relatively pure aluminum material (relatively purer than scrap aluminum).

[0102] Step 2: The aluminum material is fed into the preheating chamber in the double-chamber furnace by a conveyor belt. It is preheated using the high-temperature flue gas discharged from the melting chamber. The temperature is increased to 400-500℃ in 20-30 minutes to remove moisture and some organic matter.

[0103] The preheated aluminum material is transferred to the melting chamber through a closed channel, where it is heated to 700-750℃ and melted into liquid aluminum to obtain melt A.

[0104] Step 3: Add a NaCl-KCl-NaF mixed salt as a refining agent to melt A, and stir melt A at least twice. Each stirring operation should be at a speed of 300-800 rpm for 8-12 minutes. After each stirring operation, let it stand for at least 5 minutes. After standing, remove the inclusions (i.e., solid impurities) in melt A by skimming to homogenize the composition of melt A.

[0105] While refining melt A, high-purity argon gas is continuously introduced into the melting chamber at a flow rate of 1-3 L / min·t to remove hydrogen gas from the melting chamber.

[0106] Step 4: Transfer the refined melt A to the alloying furnace, control the temperature of melt A at 720-740℃, and adjust the composition to obtain aluminum alloy melt B;

[0107] Step 5: During the transfer process in the ladle, AlTiB wire is added to melt B in the ladle as a grain refiner, with the amount added being 0.1-0.15% of the weight of melt B; then melt B is degassed and filtered online to remove hydrogen and other harmful gases from the melt, and a two-stage foam ceramic filter plate is used to filter out large harmful compounds in the melt, making the melt as pure as possible to obtain melt C;

[0108] Step 6: Semi-continuous casting of melt C at 730℃ to obtain aluminum alloy round ingot D with a diameter of ϕ152mm;

[0109] Step 7: Homogenize the round ingot D by heating it to 550℃ at a rate of 90℃ / h, holding it at that temperature for 8 hours, and finally removing it from the furnace and water-cooling it to obtain aluminum alloy round ingot E (see...). Figure 14 , Figure 15 ), and complete the production and processing.

[0110] The high-strength, high-silicon aluminum alloy produced and processed in Example 1 contains the following components by mass percentage:

[0111] Si 4.6%, Mg 0.74%, Cu 0.03%, Mn 0.42%, Cr 0.06%, Fe 0.35%, Sr 0.25%, Zn≤0.25%, Ni≤0.05%, Ti≤0.15%, balance Al. Individual impurity elements ≤0.05%.

[0112] In step four, the adjustment of the composition is aimed at the above-mentioned components. Before adjustment, the composition of the molten aluminum is first confirmed using a composition analyzer to determine whether any elements need to be added and the amount of each element to be added. The following materials can be used for adjustment:

[0113] Aluminum ingots: Al99.7 aluminum ingots conforming to GB / T 1196-2023 are used, and the mass percentage of Al in the ingots is not less than 99.7%;

[0114] Magnesium ingots: Magnesium ingots conforming to GB / T 3499-2023 and designated as Mg9990 are used, with a Mg mass percentage of not less than 99.9% in the ingots;

[0115] Master alloy: The master alloys are aluminum-based master alloys conforming to GB / T 27677-2017, with grades AlSi20, AlCu50, AlMn10, AlCr5, and AlSr10.

[0116] Preferably, in step five, the TiAl3 phase in the AlTiB filament is uniformly distributed within the AlTiB filament, with a TiAl3 phase density ≥ 120 phases / mm². 2 Furthermore, the size of each TiAl3 phase is less than 25 μm (see...). Figure 13 ).

[0117] Preferably, the process also includes step eight: heating and extruding the round ingot E, followed by online water cooling and quenching to obtain the aluminum profile F;

[0118] The aluminum profile F is subjected to artificial aging treatment at an extrusion speed of 5-7.5 mm / s, with an aging regime of 175℃ and a holding time of 8 hours, to obtain a high-strength, high-silicon aluminum alloy profile.

[0119] During extrusion, the extrusion ratio is controlled between 60 and 140.

[0120] During extrusion, the extrusion die adopts a flow guide die design, such as... Figures 2-11 Furthermore, the number of diversion bridges 2 is greater than or equal to four, and the thickness D of the guide plate 1 is greater than or equal to four. The depth H of welding chamber 3 is (5~6). Aluminum rods are also known as round ingots (E).

[0121] The length L1 of the working zone 4 of the mold is 2-6 mm, of which the length L2 of the part 8 in contact with the aluminum rod is 0.2-0.5 mm. The remaining part of the working zone (i.e., the part L1 minus L2) has an inclination angle α of 5-10°. Afterwards, the discharge empty knife is the same as that of a conventional mold. The flow rate at different points of the profile is controlled by the shape and height of the secondary welding chamber 9. The specific control principle is existing technology and will not be described in detail here as it is not the point of invention of this case.

[0122] During extrusion, the extrusion ratio is controlled between 60 and 140.

[0123] During extrusion, a 1400T machine is preferred, the extrusion speed is preferred to be 7.5mm / s, the temperature of the profile exiting the front beam of the extrusion is greater than 500℃, and the extruded profile is subjected to online water quenching to room temperature to obtain profile F.

[0124] Preferably, the extrusion die includes an upper die and a lower die 5, the upper die being the guide plate 1; the welding chamber 3 is formed between the upper die and the lower die 5.

[0125] Preferably, the upper mold has four feeding cavities 6, and the lower mold 5 has one discharging cavity 7.

[0126] Preferred, such as Figure 9 As shown, the portion of the welding chamber 3 located on the upper surface of the lower mold 5 is cross-shaped, and this cross-shaped portion is aligned vertically with the four feeding chambers 6 of the upper mold.

[0127] Preferably, the discharge chamber 7 is cross-shaped.

[0128] Preferably, the high point P1 of the welding chamber 3 is located in the middle of the upper surface of the lower mold 5, and there are four of them; the low point P2 of the welding chamber 3 is recessed in the upper surface of the lower mold 5 and is located on the side of each high point P1 in the circumferential direction.

[0129] In this embodiment, the thickness D of the guide plate 1 and the depth H of the welding chamber 3 are both in mm.

[0130] In step three, the stirring operation is performed using a stirring paddle. For example... Figure 12 As shown, the impeller includes bottom blades 11, middle blades 12 and upper blades 13 arranged axially from bottom to top.

[0131] The bottom blade 11 serves as a propulsion blade for the upflow of molten aluminum, and its blade forms an angle of 35-55° with the horizontal plane.

[0132] The diameter of the bottom blade 11 is 0.7-0.85 times the diameter of the bottom of the molten pool, thereby expanding the stirring coverage of the bottom area of ​​the molten pool and pushing the molten aluminum upward. Each blade of the bottom blade has several protrusions 14 evenly distributed on its upper surface, and several grooves 15 (or ridges) are provided at intervals. At the same time, the outer edge of each blade is an arc-shaped curve.

[0133] The bottom blade 11 is a turbulence blade. Its special blade structure can enhance the turbulence generated when the blade pushes the aluminum liquid, increase the collision and shearing opportunities with Si, Fe and Mn particles in the aluminum liquid, and use turbulence to stir up the Fe and Mn particles deposited at the bottom, creating conditions for subsequent uniform distribution, so as to ensure the quality of aluminum alloy production.

[0134] The middle blade 12 is a variable cross-section blade, and the thickness of each blade gradually decreases from the root to the tip. A serrated structure 16 is provided on the edge of the blade, with a serration spacing of 10-15 mm and a depth of 5-8 mm. Several spiral grooves 17 are opened on the surface of the blade, with a depth of 2-3 mm.

[0135] The diameter of the middle blade 12 is larger than that of the bottom blade 11, and the main body of each blade of the middle blade 12 is designed to be straight.

[0136] Through the aforementioned design requirements of the special central blade 12, the central blade 12 can significantly enhance the shear force and vortex effect on the molten aluminum during blade rotation, causing Si particles to be dispersed and spherical in the complex flow field. At the same time, Fe and Mn particles lifted from the bottom are fully dispersed in the radial direction, allowing for better connection between the bottom and top molten aluminum. This structure can significantly enhance the shear force and vortex effect on the molten aluminum during blade rotation. The spiral groove 17 guides the molten aluminum to form a local spiral flow, increasing the opportunity for element mixing, ensuring thorough mixing of the molten aluminum throughout the molten pool, and promoting the uniform distribution of Si, Fe, and Mn particles.

[0137] The upper blade 13 is an anchor-type blade assembly with an outer layer and an inner layer; the outer layer is an upwardly curved arc-shaped stirring rod 31, and the inner layer is a guide blade 32 with protrusions 14.

[0138] There are two arc-shaped stirring rods 31 on the outer layer of the upper blade, and they are arranged symmetrically.

[0139] The guide vanes 32 of the inner layer of the upper blade are arranged radially upwards at an angle.

[0140] Based on the above design requirements, the upper blade 13 can change the flow direction of the molten aluminum at the top, forming a complex circulating flow field to prevent Si, Fe, and Mn particles from accumulating at the top. Furthermore, the stirring process will not damage the top layer of covering agent and oxide layer, ensuring that the molten aluminum in the melt is not subject to secondary contamination. Through the special flow field design, the Si, Fe, and Mn particles, after being treated at the bottom and middle sections, are further evenly dispersed at the top, avoiding local concentration differences and enhancing the stirring effect on the molten aluminum throughout the entire pool.

[0141] Preferably, the stirring impeller is configured to have a heat-resistant alloy steel body and a nitrided surface. This enhances surface hardness and anti-adhesion properties, prevents the adhesion of Si, Fe, and Mn particles, and ensures that the stirring effect is not affected.

[0142] In this embodiment, the protrusion 14 is used to further disrupt the flow of molten aluminum, and a circular protrusion with a diameter of 8-10 mm can be used for specific implementation.

[0143] Comparative Example 1:

[0144] Comparative Example 1 describes the preparation of a high-strength, high-silicon aluminum alloy that can be rapidly extruded from recycled waste aluminum. The composition, by weight percentage, comprises: Si 4.6%, Mg 0.74%, Cu 0.03%, Mn 0.42%, Cr 0.06%, Fe 0.35%, Sr 0.25%, Zn≤0.25%, Ni≤0.05%, Ti≤0.15%, with the balance being Al. Individual impurity elements are ≤0.05%.

[0145] In step three, a single stirring paddle is used to rotate the jet, and the jet is rotated and stirred only once. Finally, the material is melted, cast, and extruded to obtain the profile of Comparative Example 1.

[0146] The remaining implementation steps of this embodiment are the same as those of Embodiment 1.

[0147] Comparative Example 2:

[0148] Comparative Example 2 prepared a high-strength, high-silicon aluminum alloy that can be rapidly extruded using recycled waste aluminum. The composition of this alloy, by weight percentage, is as follows: Si 4.6%, Mg 0.74%, Cu 0.03%, Mn 0.42%, Cr 0.06%, Fe 0.35%, Sr 0.25%, Zn≤0.25%, Ni≤0.05%, Ti≤0.15%, with the balance being Al. Individual impurity elements are ≤0.05%.

[0149] In step five, during the transfer process in the laminator, a common grade of aluminum-titanium-boron (AlTiB) wire grain refiner is added to the laminator. The TiAl3 particles are between 35-45 μm in size and are unevenly distributed within the AlTiB wire. Under a metallographic microscope, the TiAl3 particles are found to be unevenly distributed, with denser particles at the center and sparser particles near the outer surface. The melt is then passed through an online degassing and filtration device using a two-stage foam ceramic filter plate to obtain the melt. Finally, an aluminum rod is obtained and extruded and aged to produce the profile of Comparative Example 2.

[0150] The remaining implementation steps of this comparative example are the same as those of Example 1.

[0151] Comparative Example 3:

[0152] Comparative Example 3 prepared a high-strength, high-silicon aluminum alloy that can be rapidly extruded using recycled waste aluminum. The composition of this alloy, by weight percentage, is as follows: Si 4.6%, Mg 0.74%, Cu 0.03%, Mn 0.42%, Cr 0.06%, Fe 0.35%, Sr 0.25%, Zn≤0.25%, Ni≤0.05%, Ti≤0.15%, with the balance being Al. Individual impurity elements are ≤0.05%.

[0153] In step six, semi-continuous casting is carried out to obtain an aluminum alloy round ingot with a diameter of ϕ120mm.

[0154] In step eight, the ingot E is heated to 490℃ and then extruded into a round bar. The extrusion is carried out on a 1000T extrusion press with an extrusion ratio of 41 and an extrusion speed of 5.0 mm / s. After extrusion, the profile is subjected to online water cooling quenching to obtain the profile of Comparative Example 3.

[0155] The remaining implementation steps of this comparative example are the same as those of Example 1.

[0156] Comparative Example 4:

[0157] Comparative Example 4 prepared a high-strength, high-silicon aluminum alloy that can be rapidly extruded using recycled waste aluminum. The composition of this alloy, by weight percentage, is as follows: Si 4.6%, Mg 0.74%, Cu 0.03%, Mn 0.42%, Cr 0.06%, Fe 0.35%, Sr 0.25%, Zn≤0.25%, Ni≤0.05%, Ti≤0.15%, with the balance being Al. Individual impurity elements are ≤0.05%.

[0158] Step 8: After heating the ingot E to 485℃, extrude it into a round bar using an integral die. The welding chamber depth is 20mm, the working strip length is 0.4mm, the machine is 1400T, and the extrusion speed is 7.2mm / s. After extrusion, the profile is subjected to online water cooling quenching to obtain the profile of Comparative Example 4.

[0159] The remaining implementation steps of this comparative example are the same as those of Example 1.

[0160] Comparative Example 5:

[0161] Comparative Example 5 prepared a high-strength, high-silicon aluminum alloy that can be rapidly extruded using recycled waste aluminum. The composition of this alloy, by weight percentage, is as follows: Si 4.6%, Mg 0.74%, Cu 0.03%, Mn 0.42%, Cr 0.06%, Fe 0.35%, Sr 0.25%, Zn≤0.25%, Ni≤0.05%, Ti≤0.15%, with the balance being Al. Individual impurity elements are ≤0.05%.

[0162] Step 8: After heating ingot E to 480℃, extrude 18mm round bars. Use a flow guide die with specifications ϕ220*140, where the flow guide plate is 70mm thick, the welding chamber is 30mm deep, and the working belt is 5.0mm long. Select a 1400T machine, with an extrusion ratio of 70 and an extrusion speed of 4.5mm / s. After extrusion, the profile is subjected to online water cooling quenching to obtain the profile of Comparative Example 5.

[0163] The remaining implementation steps of this comparative example are the same as those of Example 1.

[0164] Comparative Example 6:

[0165] Comparative Example 6 prepared a high-strength, high-silicon aluminum alloy that can be rapidly extruded using recycled waste aluminum. The composition of this alloy, by weight percentage, is as follows: Si 4.6%, Mg 0.74%, Cu 0.03%, Mn 0.42%, Cr 0.06%, Fe 0.35%, Sr 0.25%, Zn≤0.25%, Ni≤0.05%, Ti≤0.15%, with the balance being Al. Individual impurity elements are ≤0.05%.

[0166] Step 8: After heating the ingot E to 490℃, extrude it into a round bar with an extrusion ratio of 70 and an extrusion speed of 7.5 mm / s. After extrusion, the profile is subjected to strong air cooling quenching to room temperature to obtain the profile of Comparative Example 6.

[0167] The remaining implementation steps of this comparative example are the same as those of Example 1.

[0168] The aluminum alloy profiles obtained in Example 1 and Comparative Examples 1-6 were subjected to mechanical property tests according to GB / T228.1-2021 "Metallic materials - Tensile testing - Part 1: Test method at room temperature". The deformation of the profiles was also checked. The test results are shown in Table 1. Rm represents tensile strength (MPa), Rp0.2 represents yield strength (MPa), which is the strength at a non-proportional elongation of 0.2%, and A50 represents elongation after fracture (%), which is the elongation at a gauge length of 50 mm.

[0169] Table 1 Mechanical performance test results

[0170]

[0171] According to the test results, the mechanical properties of Example 1 of this invention are superior to the tensile and yield strength standards for 6XXX aluminum profiles in the national standard. This shows that adding an appropriate amount of Mn to the recycled aluminum alloy can effectively neutralize the adverse effects of Fe. A unique three-stage stirring paddle is used to stir the aluminum alloy melt, fully dispersing elements such as Fe, Mn, and Si in the melt. A high-grade grain refiner is used to further refine the grains in the round ingot. Increasing the extrusion ratio and designing an extremely short working strip, the combined use of these measures, enables rapid extrusion and results in aluminum profiles with high strength.

[0172] See photos of the profile products. Figures 16-22 .

[0173] In Comparative Example 1, only a single impeller was used for rotary jetting, and degassing was performed only once, resulting in poor degassing compared to the three-impeller system. The dual-impeller system reduced the hydrogen content to below 0.1 mL / 100g within 8-12 minutes, achieving a 30-50% efficiency improvement compared to the traditional single-impeller system (15-20 minutes). Using a three-impeller rotary jetting system reduced inclusions, increased density, achieved a high hydrogen removal rate, and suppressed the hazards caused by hydrogen embrittlement. Example 1 showed a 3.9% increase in tensile strength and a 14% increase in elongation compared to Comparative Example 1.

[0174] In Comparative Example 2, a common grade grain refiner was selected. The TiAl3 grains were relatively coarse compared to the higher grade, and did not have a good grain refinement effect in the flow channel. As a result, the grains of the profile obtained in Comparative Example 2 were not uniform, and coarse grains appeared on the surface. Its mechanical properties and elongation were lower than those of Example 1.

[0175] In Comparative Example 3, the metal was extruded on a conventional extrusion press (1000T). The pressure during the extrusion process was lower than that of 1400T, resulting in a smaller degree of metal deformation, a smaller dislocation density inside the microstructure, and a smaller deformation resistance. This led to lower mechanical properties in the subsequent tensile test results.

[0176] In Comparative Example 4, the profile is extruded by an integral die. After a brief deformation, the aluminum rod flows out of the die hole and becomes a solid round rod. It does not undergo large deformation, so the internal deformation energy storage is small and the dislocation density is low. The elemental Si does not undergo the deformation and breakage process, so the mechanical properties are relatively low.

[0177] In Comparative Example 5, the die working strip was relatively long. During the final transformation of elemental Si into a round bar, there was strong frictional deformation between the die and the working strip. Even at a relatively slow extrusion speed, this strong friction caused surface scratches and cracks. After extrusion in Comparative Example 5, the die working strip showed severe scratches, and microcracks appeared at the bridge positions. This indicates that when extruding the alloy of this invention, the working strip should not be too long; its length should be minimized to reduce the pressure on the die during extrusion.

[0178] Comparative Example 6 uses air-cooled quenching, and the cooling rate of its profiles is much lower than that of water-cooled quenching in Example 1. See Table 2 below for details:

[0179] Table 2. Effect of quenching method on cooling rate

[0180]

[0181] The mechanical properties of the final profile were lower than those of Example 1. This indicates that when the alloy was cooled at a low rate, the strengthening phase precipitated and was not completely preserved in the form of a solid solution, resulting in lower mechanical properties after aging.

[0182] In summary, this invention uses recycled aluminum as raw material, which has lower requirements for the source of the aluminum and the recycling equipment, and can effectively achieve the grade preservation and utilization of recycled aluminum. During the production process, by optimizing the casting process, a unique three-stage stirring paddle is used to stir the aluminum alloy melt, fully dispersing elements such as Fe, Mn, and Si in the melt, making their distribution more uniform, and refining the elemental Si in the ingot. Simultaneously, high-grade TiAl3 wire is used to ensure the refining effect. Air jet degassing significantly removes harmful impurities and hydrogen from the melt. Combined with a high-temperature superconducting device, the melt is fully homogenized, refining the elemental Si. Then, the extrusion process parameters are controlled, selecting a high extrusion ratio profile to increase the extrusion pressure. A bridged guide plate promotes grain deformation and breakage. Enhanced welding ensures microstructure density. Finally, the working zone is made extremely short to reduce the pressure at the exit and the temperature rise of the profile, ensuring the surface quality of the profile. The flow rate is controlled by the shape and height of the secondary welding chamber. Ultimately, a high-strength, high-silicon aluminum alloy that can be rapidly extruded using recycled waste aluminum was successfully prepared.

[0183] The above embodiments are only for illustrating the technical concept and features of the present invention, and are intended to enable those skilled in the art to understand the content of the present invention and implement it accordingly. They should not be construed as limiting the scope of protection of the present invention. All equivalent changes or modifications made in accordance with the spirit and essence of the present invention should be covered within the scope of protection of the present invention.

Claims

1. A method for producing a high-strength, high-silicon aluminum alloy that can be rapidly extruded using recycled waste aluminum, characterized in that: include: Step 1: Pre-process the aluminum scrap, including crushing and sorting, to obtain aluminum material; Step 2: Preheat the aluminum material to remove moisture and some organic matter; then melt the preheated aluminum material to obtain melt A. Step 3: Refine melt A by stirring and skimming to remove inclusions from melt A; Step 4: Transfer the refined melt A to the alloying furnace, adjust the composition to obtain aluminum alloy melt B; Step 5: Add AlTiB wire as a grain refiner to melt B, the amount added is 0.1-0.15% of the weight of melt B; then degas and filter melt B online to obtain melt C; Step 6: Cast the melt C to obtain aluminum alloy round ingot D; Step 7: Homogenize and anneal the round ingot D, and after cooling, obtain aluminum alloy round ingot E, thus completing the production and processing of high-strength, high-silicon aluminum alloy. High-strength, high-silicon aluminum alloys contain the following components by mass percentage: The composition is as follows: Si 4.0-4.9%, Mg 0.6-0.9%, Cu≤0.1%, Mn 0.36-0.72%, Cr≤0.1%, Fe 0.3-0.6%, Sr 0.05-0.4%, Zn≤0.25%, Ni≤0.05%, Ti≤0.15%, with the balance being Al; and the content of any single impurity element is ≤0.05%; in step four, the adjustment of the composition is carried out with the above-mentioned components as the target. In step one, the pretreatment is as follows: aluminum waste is fed into a crusher for crushing and screening, leaving aluminum-containing fragments with a diameter of less than 110mm. Then, iron-containing impurities in the aluminum-containing fragments are removed by magnetic separation, non-metallic impurities are removed by eddy current separation, and finally, X-ray separation and paint removal are performed to obtain the aluminum material. In step two, the aluminum material preheating process is as follows: the aluminum material is sent into the preheating chamber and preheated to 400-500°C for 20-30 minutes; the aluminum material melting process after preheating is as follows: the preheated aluminum material is transferred to the melting chamber through a closed channel and heated to 700-750°C in the melting chamber to melt into liquid aluminum, thereby obtaining the melt A; In step three, the refining process is as follows: a refining agent is added to melt A, and melt A is stirred at least twice. The stirring speed for each stirring operation is 300-800 rpm and the time is 8-12 minutes. After each stirring operation, the mixture is allowed to stand for at least 5 minutes. After standing, the inclusions in melt A are removed by skimming. While refining melt A, inert gas is continuously introduced into the melting chamber to remove hydrogen from the melting chamber; In step four, when adjusting the composition of melt A, the temperature of melt A is controlled at 720-740℃; In step seven, the round ingot D is subjected to homogenization annealing. First, it is heated to 550°C at a heating rate of 90°C / h, then held at that temperature for 8 hours, and finally removed from the furnace and water-cooled. After cooling, the aluminum alloy round ingot E is obtained. In step five, the TiAl3 phase in the AlTiB filament is uniformly distributed within the AlTiB filament, with a TiAl3 phase density ≥ 120 phases / mm². 2 Furthermore, the size of each TiAl3 phase is less than 25 μm; In step three, the stirring operation is performed using a stirring paddle; The impeller includes bottom blades, middle blades and upper blades arranged axially from bottom to top at intervals; The bottom blades serve as propulsion blades for the upward flow of molten aluminum, with the blades forming an angle of 35-55° with the horizontal plane; the diameter of the bottom blades is 0.7-0.85 times the diameter of the bottom of the molten pool; each blade of the bottom blade has several protrusions evenly distributed on its upper surface, and several grooves are provided at intervals; at the same time, the outer edge of each blade is an arc-shaped curve. The middle blade is a variable cross-section blade, with the thickness of each blade gradually decreasing from the root to the tip, and a serrated structure set on the blade edge; several spiral grooves are opened on the blade surface; the serrated structure on the blade edge of the middle blade has a serrated spacing of 10-15mm and a depth of 5-8mm; several spiral grooves are opened on the blade surface with a depth of 2-3mm; the diameter of the middle blade is larger than that of the bottom blade, and the main body of each blade of the middle blade is designed to be straight; The upper blade is an anchor-type blade assembly, having an outer layer and an inner layer; wherein, the outer layer is an upwardly curved arc-shaped stirring rod, and the inner layer is a guide blade with protrusions; the outer layer of the upper blade has two arc-shaped stirring rods, which are symmetrically arranged; the guide blades of the inner layer of the upper blade are arranged radially upward at an oblique angle.

2. The production method of a rapidly extrudable high-strength, high-silicon aluminum alloy using recycled waste aluminum according to claim 1, characterized in that: It also includes step eight, heating and extruding the round ingot E, and then water-cooling and quenching it online to obtain the aluminum profile F; The aluminum profile F is subjected to artificial aging treatment at an extrusion speed of 5-7.5 mm / s, with an aging regime of 175℃ and a holding time of 8 hours, to obtain a high-strength, high-silicon aluminum alloy profile.

3. The production method for manufacturing a rapidly extrudable high-strength, high-silicon aluminum alloy using recycled waste aluminum according to claim 2, characterized in that: In step eight, during extrusion, the extrusion ratio is controlled between 60 and 140.

4. The production method of a rapidly extrudable high-strength, high-silicon aluminum alloy using recycled waste aluminum according to claim 2, characterized in that: In step eight, during extrusion, the extrusion die adopts a flow guide design, and the number of flow dividers is greater than or equal to four, with the thickness D of the flow guide plate ≥ The depth H of the welding chamber = In the formula, the aluminum rod is a round ingot E.

5. A method for producing a rapidly extrudable high-strength, high-silicon aluminum alloy using recycled waste aluminum according to claim 2, characterized in that: In step eight, during extrusion, the length L1 of the die working belt is 2-6 mm, of which the length L2 of the part in contact with the aluminum rod is 0.2-0.5 mm, and the rest of the working belt has an inclination angle α of 5-10°.

6. The production method of a rapidly extrudable high-strength, high-silicon aluminum alloy using recycled waste aluminum according to claim 1, characterized in that: The impeller is made of heat-resistant alloy steel, and its surface is nitrided.

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