CN116479281A - Aluminum alloy profile with mixed crystal heterostructure characteristics and preparation method thereof - Google Patents
Aluminum alloy profile with mixed crystal heterostructure characteristics and preparation method thereof Download PDFInfo
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- CN116479281A CN116479281A CN202310479380.0A CN202310479380A CN116479281A CN 116479281 A CN116479281 A CN 116479281A CN 202310479380 A CN202310479380 A CN 202310479380A CN 116479281 A CN116479281 A CN 116479281A
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- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 76
- 239000013078 crystal Substances 0.000 title claims abstract description 44
- 238000002360 preparation method Methods 0.000 title claims abstract description 29
- 239000000956 alloy Substances 0.000 claims abstract description 129
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 127
- 239000002245 particle Substances 0.000 claims abstract description 88
- 238000010438 heat treatment Methods 0.000 claims abstract description 76
- 238000003723 Smelting Methods 0.000 claims abstract description 58
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 27
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims abstract description 27
- 238000004519 manufacturing process Methods 0.000 claims abstract description 23
- 238000005266 casting Methods 0.000 claims abstract description 22
- 238000001192 hot extrusion Methods 0.000 claims abstract description 17
- 229910052751 metal Inorganic materials 0.000 claims abstract description 15
- 239000002184 metal Substances 0.000 claims abstract description 15
- 238000001125 extrusion Methods 0.000 claims description 32
- 238000000034 method Methods 0.000 claims description 27
- 238000004321 preservation Methods 0.000 claims description 13
- 238000001816 cooling Methods 0.000 claims description 9
- 239000000155 melt Substances 0.000 claims description 8
- 238000003756 stirring Methods 0.000 claims description 8
- 238000007872 degassing Methods 0.000 claims description 6
- 239000011261 inert gas Substances 0.000 claims description 6
- 238000007670 refining Methods 0.000 claims description 6
- 238000009749 continuous casting Methods 0.000 claims description 5
- 239000002994 raw material Substances 0.000 claims description 5
- 238000002844 melting Methods 0.000 claims description 3
- 230000008018 melting Effects 0.000 claims description 3
- 239000004411 aluminium Substances 0.000 claims description 2
- 229910052725 zinc Inorganic materials 0.000 claims description 2
- 150000002739 metals Chemical class 0.000 claims 1
- 239000007769 metal material Substances 0.000 abstract description 10
- 230000009286 beneficial effect Effects 0.000 abstract description 2
- 239000000243 solution Substances 0.000 description 28
- 239000006104 solid solution Substances 0.000 description 25
- 238000002474 experimental method Methods 0.000 description 18
- 230000000052 comparative effect Effects 0.000 description 12
- 239000000463 material Substances 0.000 description 12
- 229910018594 Si-Cu Inorganic materials 0.000 description 10
- 229910008465 Si—Cu Inorganic materials 0.000 description 10
- 238000001887 electron backscatter diffraction Methods 0.000 description 10
- 230000008569 process Effects 0.000 description 9
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 8
- 238000011282 treatment Methods 0.000 description 6
- 238000004458 analytical method Methods 0.000 description 5
- 238000010586 diagram Methods 0.000 description 5
- 238000012986 modification Methods 0.000 description 5
- 230000004048 modification Effects 0.000 description 5
- YLZOPXRUQYQQID-UHFFFAOYSA-N 3-(2,4,6,7-tetrahydrotriazolo[4,5-c]pyridin-5-yl)-1-[4-[2-[[3-(trifluoromethoxy)phenyl]methylamino]pyrimidin-5-yl]piperazin-1-yl]propan-1-one Chemical compound N1N=NC=2CN(CCC=21)CCC(=O)N1CCN(CC1)C=1C=NC(=NC=1)NCC1=CC(=CC=C1)OC(F)(F)F YLZOPXRUQYQQID-UHFFFAOYSA-N 0.000 description 4
- 229910052786 argon Inorganic materials 0.000 description 4
- 238000012545 processing Methods 0.000 description 4
- 238000001953 recrystallisation Methods 0.000 description 4
- 238000005096 rolling process Methods 0.000 description 4
- 230000002159 abnormal effect Effects 0.000 description 3
- 238000009826 distribution Methods 0.000 description 3
- 230000000694 effects Effects 0.000 description 3
- 239000011159 matrix material Substances 0.000 description 3
- 239000000126 substance Substances 0.000 description 3
- QYEXBYZXHDUPRC-UHFFFAOYSA-N B#[Ti]#B Chemical compound B#[Ti]#B QYEXBYZXHDUPRC-UHFFFAOYSA-N 0.000 description 2
- 229910033181 TiB2 Inorganic materials 0.000 description 2
- 238000005299 abrasion Methods 0.000 description 2
- 239000000654 additive Substances 0.000 description 2
- 230000000996 additive effect Effects 0.000 description 2
- 230000001186 cumulative effect Effects 0.000 description 2
- 238000013461 design Methods 0.000 description 2
- 238000007429 general method Methods 0.000 description 2
- 238000000227 grinding Methods 0.000 description 2
- 125000005842 heteroatom Chemical group 0.000 description 2
- 238000004663 powder metallurgy Methods 0.000 description 2
- 238000005480 shot peening Methods 0.000 description 2
- 238000004381 surface treatment Methods 0.000 description 2
- 238000003466 welding Methods 0.000 description 2
- 229910018569 Al—Zn—Mg—Cu Inorganic materials 0.000 description 1
- 229910017818 Cu—Mg Inorganic materials 0.000 description 1
- 230000032683 aging Effects 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 230000001276 controlling effect Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000002425 crystallisation Methods 0.000 description 1
- 230000008025 crystallization Effects 0.000 description 1
- 238000004146 energy storage Methods 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 238000013508 migration Methods 0.000 description 1
- 230000005012 migration Effects 0.000 description 1
- 239000002105 nanoparticle Substances 0.000 description 1
- 230000003287 optical effect Effects 0.000 description 1
- 238000000746 purification Methods 0.000 description 1
- 230000001105 regulatory effect Effects 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
Classifications
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/10—Alloys containing non-metals
- C22C1/1036—Alloys containing non-metals starting from a melt
- C22C1/1047—Alloys containing non-metals starting from a melt by mixing and casting liquid metal matrix composites
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/02—Alloys based on aluminium with silicon as the next major constituent
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/06—Alloys based on aluminium with magnesium as the next major constituent
- C22C21/08—Alloys based on aluminium with magnesium as the next major constituent with silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C32/00—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ
- C22C32/0047—Non-ferrous alloys containing at least 5% by weight but less than 50% by weight of oxides, carbides, borides, nitrides, silicides or other metal compounds, e.g. oxynitrides, sulfides, whether added as such or formed in situ with carbides, nitrides, borides or silicides as the main non-metallic constituents
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/043—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with silicon as the next major constituent
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/04—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon
- C22F1/047—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working of aluminium or alloys based thereon of alloys with magnesium as the next major constituent
Abstract
The invention relates to the technical field of metal material preparation, in particular to an aluminum alloy section bar with a mixed crystal heterostructure characteristic and a preparation method thereof. The preparation method of the aluminum alloy section with the mixed crystal heterostructure characteristics comprises the following steps: smelting with pureAl, tiB-containing 2 And TiC particles, and aluminum intermediate alloy and pure metal which are added for manufacturing different series of aluminum alloy sections are smelted at the temperature of 800-850 ℃; casting, namely casting the smelted alloy at the temperature of 720-750 ℃. The beneficial effects of the invention are as follows: the preparation method comprises the steps of adding a small amount of TiB in the preparation of the aluminum alloy 2 And TiC particles, after hot extrusion and solution heat treatment, mixed grains containing coarse grains and fine grains can be prepared, the proportion of the coarse grains and the fine grains is adjustable and controllable, and the alloy with the characteristics of the mixed crystal heterostructure can synchronously improve the strength performance and the elongation of the aluminum alloy section.
Description
Technical Field
The invention relates to the technical field of metal material preparation, in particular to an aluminum alloy section bar with a mixed crystal heterostructure characteristic and a preparation method thereof.
Background
The aluminum alloy has the advantages of good electric conduction and thermal conductivity, higher strength-mass ratio, corrosion resistance, damage resistance and the like, is widely used in various fields of aerospace, rail transit, automobiles, ships, pressure vessels, electronic appliances, furniture and the like, and is one of the most widely used metal materials in the industry at present. In general, metallic materials have an inverse relationship of "strength-plasticity", i.e., increasing the strength of a material is accompanied by a decrease in the plasticity of the material. Therefore, the comprehensive mechanical properties of the alloy are difficult to synchronously improve by the conventional way. In recent years, scholars at home and abroad break through the previous design concept of ' homogeneity ' of grain structure, design and prepare a plurality of ' hetero ' -structure ' metal materials with different sizes and even cross-scale grains, and break through the strong plasticity limit of the existing metal materials.
So far, a plurality of bottlenecks still exist in batch preparation of aluminum alloy heterostructure materials, how to prepare heterostructure aluminum alloy sections, and the improvement of the comprehensive mechanical properties of the aluminum alloy sections by fully utilizing the advantages of heterostructures is a key for realizing industrial application of the heterostructure aluminum alloy sections. The current method for preparing heterostructure metal material mainly comprises the following steps: (1) Surface treatments (e.g., surface Mechanical Grinding Treatment (SMGT), surface Mechanical Abrasion Treatment (SMAT), shot peening, etc.), which form a heterostructure of micro-regions only on the surface of the material; (2 powder metallurgy, which is a general method of manufacturing heterostructure and harmonic structural materials, (3) Additive Manufacturing (AM), which can produce heterostructures with controlled structure and tailored properties, (4) mechanical thermal processing treatments such as asymmetric rolling (ASR), cumulative rolling welding (ARB), friction Stir Processing (FSP), etc. it can be seen that none of the methods reported in the prior art for producing heterostructure metallic materials are well suited for mass production in large scale and are also not suited for the preparation of alloy profiles.
The invention discloses an aluminum alloy section with a mixed crystal heterostructure characteristic and a preparation method thereof, and the aluminum alloy section can be used for large-scale industrial preparation in batches.
Disclosure of Invention
Aiming at the technical problems in the prior art, the invention provides an aluminum alloy section with a mixed crystal heterostructure characteristic and a preparation method thereof to solve the problem that the aluminum alloy with the heterostructure cannot be produced in a large scale in a batch manner.
The technical scheme for solving the technical problems is as follows: the preparation method of the aluminum alloy section with the mixed crystal heterostructure characteristics comprises the following steps:
smelting with pure Al and TiB 2 And TiC particles, and aluminum intermediate alloy and pure metal which are added for manufacturing different series of aluminum alloy sections are smelted at the temperature of 800-850 ℃;
casting, namely casting the smelted alloy at the temperature of 720-750 ℃ to form an ingot;
uniformly heat-treating, namely heating the cast ingot to 450-560 ℃ for 8-24 hours;
hot extrusion, namely, casting the ingot after uniform heat treatment at the temperature of 400-450 ℃ according to the extrusion ratio: 20 to 60 and extrusion speed: extruding the cast ingot at 0.5-10 m/min;
solution heat treatment is carried out for 0.5 to 10 hours at the temperature of 460 to 570 ℃ for heat preservation.
The beneficial effects of the invention are as follows:
1) The preparation method comprises the steps of adding a small amount of TiB in the preparation of the aluminum alloy 2 And TiC particles, after hot extrusion and solution heat treatment, the mixed grain structure containing coarse grains and fine grains can be prepared, the proportion of the coarse grains and the fine grains is adjustable and controllable, and the alloy with the characteristic of the mixed crystal heterostructure can synchronously improve the strength performance and the elongation of the aluminum alloy section.
On the basis of the technical scheme, the invention can be improved as follows.
Further, the smelting step of the alloy includes:
s1, selecting TiB 2 And TiC particles (10 wt% -50 wt%) and smelting raw material for adding aluminium intermediate alloy and pure metal (7 wt% -21 wt%) required for making different series aluminium alloy section and the rest is pure Al, and making TiB-containing alloy material 2 And TiC particles, aluminum intermediate alloy added for manufacturing different series aluminum alloy sections and pure Al are put into a smelting furnace, wherein TiB is contained 2 The aluminum intermediate alloy with TiC particles comprises the following components: tiB (TiB) 2 And TiC particles (3 wt% -6 wt%) and the rest being pure Al, while TiB 2 The proportion of the TiC particles to the TiC particles is 2:5-1:1;
s2, adding inert gas for protection when the temperature in the smelting furnace reaches over 780 ℃;
s3, heating the temperature in the smelting furnace to 800-850 ℃;
s4, after the alloy in the smelting furnace is completely melted, immersing at least one pure metal with the melting point lower than that of Al into the alloy melt;
s5, uniformly stirring the pure metal and the alloy melt by using a stirrer;
s6, a melt purifying procedure, wherein refining, degassing and deslagging are carried out in the smelting furnace.
Further, the aluminum intermediate alloy required to be added for manufacturing the aluminum alloy profiles of different series comprises Al-20Si, al-50Cu and Al-10Mn, and the metal simple substances in S4 and S5 are Mg.
Further, the aluminum intermediate alloy required to be added for manufacturing different series of aluminum alloy sections comprises Al-50Cu and Al-10Mn, and the metal simple substances in S4 and S5 are Mg.
Further, the aluminum intermediate alloy required to be added for manufacturing different series of aluminum alloy sections comprises Al-50Cu and Al-5Cr, and the metal simple substances in S4 and S5 are Mg and Zn.
Further, the casting step of the alloy includes:
s1', firstly, cooling the alloy in the smelting furnace to 720-750 ℃;
s2', casting the smelted alloy into a round ingot by casting or semi-continuous casting.
Further, the uniform heat treatment comprises the steps of putting the cast ingot into a heating furnace to heat at 530-560 ℃ for 8-16 hours, and the hot extrusion comprises the steps of passing the cast ingot after the uniform heat treatment through an extruder at 400-450 ℃ according to the extrusion ratio: 30-60 and extrusion speed: extruding the ingot at a temperature of between 550 and 570 ℃ for between 0.5 and 10 hours.
Further, the uniform heat treatment comprises the steps of putting the cast ingot into a heating furnace to heat at 480-530 ℃ for 16-24 hours, and the hot extrusion comprises the steps of passing the cast ingot after the uniform heat treatment through an extruder at the temperature of 400-450 ℃ according to the extrusion ratio: 20-50 and extrusion speed: extruding the ingot at 0.8-4 m/min, wherein the solution heat treatment comprises the step of continuously heating at 500-530 ℃ for 0.5-10 hours.
Further, the uniform heat treatment comprises the steps of putting the cast ingot into a heating furnace to heat at the temperature of 450-470 ℃ for 18-24 hours, and the hot extrusion comprises the steps of passing the cast ingot after the uniform heat treatment through an extruder at the temperature of 400-450 ℃ according to the extrusion ratio: 20-40 and extrusion speed: the ingot is extruded at 0.5 m-2 m/min, and the solution heat treatment comprises the step of continuously heating at 460-475 ℃ for 0.5-10 hours.
An aluminum alloy profile with mixed crystal heterostructure features, the aluminum alloy profile having grains with mixed coarse and fine crystals, wherein the ratio of coarse and fine crystal distributions within the grains is different.
Further, coarse crystals and fine crystals with different proportions in the crystal grains can be obtained by regulating and controlling the time of solution heat treatment.
Drawings
FIG. 1 is a schematic diagram of the overall structure of the present invention;
FIG. 2 shows the TiB added according to the present invention 2 -EBSD grain morphology pattern of extruded heterogeneous aluminum alloy profile after TiC particle modification;
FIG. 3 shows the invention without TiB addition 2 -EBSD grain morphology map of the extruded conventional aluminum alloy profile after TiC particle modification;
FIG. 4 shows the TiB added according to the present invention 2 TiC particles modified with and without TiB addition 2 -drawing mechanical property comparison graph of extruded alloy section bar after TiC particle modification;
FIG. 5 shows the invention without TiB addition 2 Drawing mechanical properties of the TiC particles modified solid solution state conventional aluminum alloy section bar;
FIG. 6 shows the TiB added according to the present invention 2 -drawing mechanical property diagram of solid solution state heterogeneous aluminum alloy section bar after TiC particle modification;
FIG. 7 shows the TiB added according to the present invention 2 -an EBSD crystal grain morphology diagram with coarse grain and fine grain ratio of 1:3 when the TiC particle modified solid solution state heterogeneous aluminum alloy section is solid solution for 1 hour at 560 ℃;
FIG. 8 shows the TiB added according to the present invention 2 -an EBSD crystal grain morphology diagram with coarse grain and fine grain ratio of 1:1 when the TiC particle modified solid solution state heterogeneous aluminum alloy section is solid solution for 1.5 hours at 560 ℃;
FIG. 9 shows the TiB added according to the present invention 2 Solid solution state heterogeneous aluminum alloy section bar modified by TiC particles is solid solution for 3 hours at 560 DEG CAn EBSD crystal grain morphology graph with the coarse-grain and fine-grain ratio of 2:1;
FIG. 10 shows the TiB added according to the present invention 2 -an EBSD crystal grain morphology diagram with a coarse-grain and fine-grain ratio of 3:1 when the TiC particle modified solid-solution heterogeneous aluminum alloy section is solid-solution for 10 hours at 560 ℃;
FIG. 11 is a schematic view showing the microstructure evolution of the alloy section of the present invention after extrusion and solid solution.
Detailed Description
The principles and features of the present invention are described below with reference to the drawings, the examples are illustrated for the purpose of illustrating the invention and are not to be construed as limiting the scope of the invention.
The batch preparation of the aluminum alloy heterostructure material still has a plurality of bottlenecks, and how to prepare the heterostructure aluminum alloy section, the comprehensive mechanical properties of the aluminum alloy section is improved by fully utilizing the advantages of the heterostructure, so that the key for realizing the industrialized application of the heterostructure aluminum alloy section is realized. The current method for preparing heterostructure metal material mainly comprises the following steps: (1) Surface treatments (e.g., surface Mechanical Grinding Treatment (SMGT), surface Mechanical Abrasion Treatment (SMAT), shot peening, etc.), which form a heterostructure of micro-regions only on the surface of the material; (2 powder metallurgy, which is a general method for manufacturing heterogeneous sheet structure and harmonic structure materials, (3) Additive Manufacturing (AM), which can manufacture heterogeneous materials with controllable structure and custom properties, (4) mechanical thermal processing treatment such as asymmetric rolling (ASR), cumulative rolling welding (ARB), friction Stir Processing (FSP), etc. it can be seen that none of the methods reported in the prior art for manufacturing heterogeneous structure metal materials is suitable for mass production in large scale, and is not suitable for manufacturing alloy sections, and the inventors propose an aluminum alloy section with mixed crystal heterogeneous structure characteristics and a manufacturing method thereof to solve the above problems.
The present invention provides the following preferred embodiments
Example 1
As shown in fig. 1 to 10, a method for preparing an aluminum alloy section with mixed crystal heterostructure features includes:
s1, selecting TiB 2 And TiC particles (10 wt% -50 wt%), al-20Si (4 wt% -7 wt%)Smelting raw materials of Al-50Cu (0 wt% -1 wt%), al-10Mn (2 wt% -8 wt%), mg ingot (1.3 wt% -1.8 wt%) and the balance being pure Al ingot, and TiB is contained 2 And TiC particles, the Al intermediate alloy ingot, al-20Si, al-50Cu, al-10Mn and pure Al ingot are put into a smelting furnace (while TiB is added in the step 2 And TiC particulate aluminum intermediate alloy ingots may be prepared by the process described in this patent CN 113373367A), which contains TiB 2 The aluminum intermediate alloy ingot with TiC particles comprises the following components: tiB (TiB) 2 And TiC particles (3 wt% -6 wt%) and the rest being pure Al, while TiB 2 The respective proportion of TiC particles is 2:5-1:1 (the configuration proportion can be but is not limited to 2.2:1, 2.0:1, 1.8:1 and the like), and TiB 2 The particles are submicron, and the TiC particles are nano-scale;
(Here, it should be noted that Al-50Cu and Al-10Mn are represented by 50wt% of Cu and the balance of pure Al, respectively, and 10wt% of Mn and the balance of pure Al, respectively, and similar formats appear hereinafter to be described herein, which are conventional terms to those skilled in the art, and are not repeated here)
S2, when the temperature in the smelting furnace reaches over 780 ℃, inert gas argon is added into the smelting furnace for protection;
s3, heating the temperature in the smelting furnace to 800-850 ℃ (through the high temperature of 800-850 ℃), and increasing TiB 2 And wettability between TiC particles and aluminum matrix);
s4, after the alloy in the smelting furnace is completely melted, immersing the Mg ingot into an alloy melt;
s5, uniformly stirring the Mg ingot and the alloy melt by using a stirrer;
s6, a melt purifying procedure, wherein refining, degassing and deslagging are carried out in a smelting furnace, and the final components of the residual alloy after smelting are Mg:1.2 to 1.8 weight percent of Si:0.8 to 1.4wt%, mn 0.2 to 0.8wt%, cu 0 to 0.5wt%, and TiB 2 +tic particles: 0.5 to 2.5 weight percent, and the rest is pure aluminum ingot;
s7, cooling the alloy in the smelting furnace to 720 ℃ -750 ℃ (the smelting furnace can be closed, and naturally cooling the alloy in the smelting furnace to 720 ℃ -750 ℃;
s8, casting the smelted alloy into a round ingot by casting or semi-continuous casting;
s9, uniformly performing heat treatment, namely placing the round ingot into a heating furnace to heat the ingot to 530-560 ℃ for 8-16 hours;
s10, hot extrusion, namely passing the cast ingot subjected to uniform heat treatment through an extruder at the temperature of 400-450 ℃ according to the extrusion ratio: 30-60 and extrusion speed: extruding the cast ingot at a speed of 5-10 m/min;
s11, carrying out solution heat treatment, and preserving heat at 550-570 ℃ for 0.5-10 hours.
In this example, the submicron TiB added in S1 2 And nano-scale TiC particles effectively refine the solidification structure of the Al-Mg-Si-Cu alloy, so that the average grain size is thinned from 74.7 mu m to 51.6 mu m, the recrystallization of the alloy in the hot extrusion process is inhibited, the abnormal growth of grains is prevented, and the stability of the Al-Mg-Si-Cu alloy structure in the hot extrusion process is improved.
Thus, in order to highlight sub-micron TiB 2 And the criticality of nano-scale TiC particles in the process of preparing the mixed crystal heterostructure characteristic aluminum alloy section bar, two groups of comparative examples and four groups of experiments are provided by the applicant; (comparative example and experiment used were each made of 6000 series aluminum alloy section bar, namely 6000 series Al-Mg-Si-Cu aluminum alloy prepared in example 1, and in order to characterize the structure and performance characteristics of the aluminum alloy section bar, the microstructure of the section bar was observed with an optical microscope (model: lecia DFC, standard: JB/T7946-2017), the hardness value of the section bar was measured with a micro Vickers hardness tester (model: zwick/Roell ZHV. Mu., standard: GB/T4340), and a tensile curve was obtained with an electronic Universal Material tester (model: CMT 5105, standard: GB/T228.1)
The parameters and steps used in the comparative examples and experiments are as follows:
step 1, tiB containing submicron order 2 And nano-sized TiC particles of aluminum intermediate alloy ingots (2200 g), al-20Si (325 g), al-50Cu (30 g), al-10Mn (200 g) and pure Al ingots(2175g) Putting into a smelting furnace, wherein the smelting furnace contains TiB 2 The aluminum intermediate alloy ingot with TiC particles comprises the following components: tiB (TiB) 2 And TiC particles (11 g) and pure Al (2090 g), while TiB 2 The proportion of the TiC particles (110 g) to the TiC particles is 2:1;
step 2, when the temperature in the smelting furnace reaches 780 ℃, adding inert gas argon into the smelting furnace for protection;
step 3, heating the temperature in the smelting furnace to 840 ℃;
step 4, after the alloy in the smelting furnace is completely melted, immersing an Mg ingot (70 g) into the alloy melt;
step 5, stirring the Mg ingot and the alloy melt uniformly by using a stirrer;
step 6, a melt purifying procedure, wherein refining, degassing and deslagging are carried out in a smelting furnace, and the final components of the residual alloy after smelting are Mg:1.3wt%, si:1.3wt%, mn 0.4wt%, cu 0.3wt%, and TiB 2 +tic particles: 2.2wt% of pure Al ingot;
step 7, cooling the alloy in the smelting furnace to 730 ℃;
step 8, casting the smelted alloy into a round ingot by using a casting mode;
step 9, uniformly performing heat treatment, namely placing the round ingot into a heating furnace to heat the round ingot to 550 ℃ for 10 hours;
step 10, hot extrusion, namely passing the cast ingot subjected to uniform heat treatment through an extruder at the temperature of 450 ℃ according to the extrusion ratio: 35 and extrusion speed: extruding the cast ingot at 8 m/min;
and 11, carrying out solution heat treatment, and carrying out heat preservation at 560 ℃ for 0.5 to 10 hours.
Comparative example 1
As shown in FIG. 4, in the step 1, no TiB is added in the preparation of 6000 series Al-Mg-Si-Cu aluminum alloy section 2 And TiC particles with added TiB 2 And TiC particle alloy after step 2-step 10, yield strength, tensile strength and extensibility; (it should also be noted here that no TiB was added in the preparation step) 2 The alloy of TiC particle aluminum intermediate alloy is conventional alloyGold with TiB added 2 The alloys of TiC particulate aluminum intermediate alloy are heterogeneous alloys, and the conventional alloys and heterogeneous alloys appearing hereinafter are described herein and are not described in detail herein
Wherein, no TiB is added 2 And TiC particles, and after the steps 1 to 10 (extrusion state conventional alloy section bar), the yield strength is 105 (+ -5) MPa, the tensile strength is 225 (+ -4) MPa, and the elongation is 30.7%;
with addition of TiB 2 And TiC particles, after the above steps 1 to 10 (extruded hetero alloy profile), have a yield strength of 148 (+ -5) MPa, a tensile strength of 255 (+ -4) MPa, and an elongation of 12.7 (+ -0.5)%, and therefore, tiB is added 2 Compared with the non-added TiB, the extruded heterogeneous alloy section prepared by TiC particles 2 And the yield strength and the tensile strength of the TiC particle extrusion state heterogeneous alloy section bar are respectively improved by 41 percent and 13 percent, and the elongation after fracture is kept at good 12.5 percent. (it is also noted here that the extruded heterogeneous alloy profile is added with TiB 2 And TiC particles are processed by the steps 1 to 10 to prepare 6000 series Al-Mg-Si-Cu aluminum alloy section with a heterostructure, and the extruded conventional alloy section is free of TiB 2 And TiC particles, and the conventional alloy is prepared into a conventional 6000 series Al-Mg-Si-Cu aluminum alloy section through the steps 1 to 10, wherein the solid solution state heterogeneous alloy section is added with TiB 2 And TiC particles are processed in the steps 1 to 11 to prepare 6000 series Al-Mg-Si-Cu aluminum alloy section with a heterostructure, and the solid solution state conventional alloy section is free of TiB 2 And TiC particles, and then the conventional 6000 series Al-Mg-Si-Cu aluminum alloy section is manufactured after the steps 1 to 11
Comparative example 2
In the case of adopting the same parameter steps as those used in steps 1 to 10 in comparative example 1, as shown in FIG. 5, 6000 series Al-Mg-Si-Cu aluminum alloy section is prepared without TiB being added in the process of step 1 2 After the conventional alloy with TiC particles passes through the steps 2 to 10, and in the solid solution heat treatment step 11, the heat preservation temperature is set to 560 ℃, and the solid solution heat treatment is carried outA line graph of yield strength, tensile strength and elongation of the solid solution state conventional alloy section after 1h, 1.5h, 3h and 10h respectively;
wherein, the yield strength of the conventional alloy after solution heat for 1 h: 104MPa, tensile strength: 232MPa, elongation: 25.2%;
yield strength of conventional alloys after 1.5h solution heat: 100MPa, tensile strength: 230MPa, elongation: 27.2%;
yield strength of conventional alloys after 3h solution heat: 101MPa, tensile strength: 232MPa, elongation: 22.2%;
yield strength of conventional alloys after 10h solution heat: 95MPa, tensile strength: 226MPa, elongation: 23.3%.
As shown in FIG. 6, in the process of step 1, the heterogeneous alloy with TiB2 and TiC particles added is subjected to step 2-step 10 in the preparation of 6000 series Al-Mg-Si-Cu aluminum alloy section, and the heat preservation temperature is set to 560 ℃ in the solid solution heat treatment link of step 11, and the solid solution heat treatment time is respectively 1h, 1.5h, 3h and 10h, and is a line graph of yield strength, tensile strength and elongation;
wherein, the yield strength of the heterogeneous alloy after solution heat for 1 h: 174MPa, tensile strength: 293MPa, elongation: 13.5%;
yield strength of the heterogeneous alloy after 1.5h solution heat: 180MPa, tensile strength: 303MPa, elongation: 15.0%;
yield strength of the heterogeneous alloy after 3h solution heat: 227MPa, tensile strength: 345MPa, elongation: 12.0%;
yield strength of the heterogeneous alloy after 10h solution heat: 163MPa, tensile strength: 288MPa, elongation: 15.2%;
please refer to fig. 4 and 6, there is an added TiB 2 And TiC particles, wherein the alloy section structure passing through the step 11 reaches specific heterostructure characteristics after passing through the step 1 to the step 10 and the step 1 to the step 11 respectively, namely, the situation that coarse crystals and fine crystals in crystal grains are distributed in different proportions exists, and the ratio of coarse crystals to fine crystals in solution heat treatment of the heterogeneous alloy is 2:1, the tensile strength and the tensile strength of the solid solution state heterogeneous alloy section bar are obtainedThe yield strength is improved by 35 percent and 53 percent compared with the extruded heterogeneous alloy section bar, the elongation is not lost, and the performance of the alloy section bar is close to the peak aging strength of the conventional alloy section bar with the same component;
in addition, please refer to fig. 5 and 6, tiB is added 2 And TiC particles in steps 1 to 11, compared with the non-TiB added material 2 And TiC particles, wherein after the conventional alloy is subjected to the steps 1-11, when the heat preservation temperature is set to 560 ℃ in the step 11, the yield strength and the tensile strength of the prepared solid solution state heterogeneous alloy section are respectively improved by 67% and 26%, 80% and 32%, 125% and 49%, 71% and 27% after the solid solution heat treatment time is respectively 1h, 1.5h, 3h and 10h, and the elongation is averagely kept above 12%. (in FIG. 5 st represents that TiB was not added 2 And TiC particles, C-F in FIG. 6 represents the addition of TiB 2 And TiC particles, and the following numbers represent the ratio of fine to coarse grains of the grains after solution heat treatment of different duration
In order to verify the influence of the different proportion distribution of coarse crystals and fine crystals in crystal grains on the yield strength, the tensile strength and the elongation of the alloy section, the applicant provides four groups of experiments;
experiment 1
Referring to FIGS. 6 and 7, tiB was added in the experiment as in comparative example 2 2 After TiC particles, the heterogeneous alloy is subjected to the same preparation steps and parameters from step 1 to step 10, wherein the difference is that the set heat preservation temperature of step 11 in the experiment is 560 ℃, when the solution heat treatment time is 1h, the ratio of coarse grains to fine grains in the alloy section is 1:3 through analysis of an EBSD grain morphology graph, and the yield strength is: 174MPa, tensile strength: 293MPa, elongation: 13.5%;
experiment 2
Referring to FIGS. 6 and 8, tiB was added in the experiment as in comparative example 2 2 After TiC particles, the heterogeneous alloy is subjected to the same preparation steps and parameters from step 1 to step 11, wherein the difference is that when the set heat preservation temperature of S11 in the experiment is 560 ℃ and the solution heat treatment time is 1.5h, the heterogeneous alloy is subjected to EBSDThe ratio of coarse grains to fine grains in the alloy section bar is 1:1, and the yield strength is: 180MPa, tensile strength: 303MPa, elongation: 15.0%;
experiment 3
Referring to FIGS. 6 and 9, tiB was added in the experiment as in comparative example 2 2 After TiC particles, the heterogeneous alloy is subjected to the same preparation steps and parameters from step 1 to step 10, wherein the difference is that the set heat preservation temperature of S11 in the experiment is 560 ℃, when the solution heat treatment time is 3h, the ratio of coarse grains to fine grains in the alloy section is 2:1 through analysis of an EBSD grain morphology graph, and the yield strength is: 227MPa, tensile strength: 345MPa, elongation: 12.0%;
experiment 4
Referring to FIGS. 6 and 10, tiB was added in the experiment as in comparative example 2 2 After TiC particles, the heterogeneous alloy is subjected to the same preparation steps and parameters from step 1 to step 10, wherein the difference is that the set heat preservation temperature of S11 in the experiment is 560 ℃, when the solution heat treatment time is 10 hours, the ratio of coarse grains to fine grains in the alloy section is 3:1 through analysis of an EBSD grain morphology graph, and the yield strength is: 163MPa, tensile strength: 288MPa, elongation: 15.2%;
referring to FIG. 11 (FIG. 11, A is a row of TiB-free under the same preparation steps and parameters as in the experiment) 2 And TiC particles, respectively, after extrusion and solution heat of 1h, 3h and 10h, and B is a schematic drawing of the microstructure evolution of the hetero-alloy added with TiB2 and TiC particles after extrusion and solution heat of 1h, 3h and 10h, respectively, and thus, through the comparative examples and experimental analysis described above: adding a small amount of TiB in the process of preparing the aluminum alloy 2 And TiC particles to cause TiB 2 And TiC particles are distributed in a discontinuous layer in the matrix, most particles are gathered along the extrusion direction except the particles in the matrix, the particle distribution leads to the formation of a particle gathering area and a particle sparse area, the non-uniformly distributed particles are the premise of realizing heterogeneous grain crystallization of the aluminum alloy full-section material in the subsequent heat treatment, and the particles lead to the non-uniform flow of the alloy during the hot extrusion, so that most cast grains are subjected to the following conditionsThe grains are crushed into fine equiaxed grains, the rest of grains are severely deformed and become slender grains, the grains play a zener pinning effect, the sliding and migration of grain boundaries are blocked, recrystallization is restrained, and then the growth of the grains is effectively prevented, after solution heat treatment, the grains in an enrichment region have a strong pinning effect, the driving force of the solution heat treatment is insufficient to activate extensive recrystallization, most of crushed fine extruded grains are still stored in the enrichment region and the periphery of the grains, the grains in a sparse region undergo more serious deformation in the extrusion process, the grains have higher deformation energy storage, the pinning effect is weaker due to the rarefaction of the grains, and the grains are more prone to recrystallization;
on the other hand, in the solution heat treatment process of grains with high abnormal growth tendency of the grains subjected to severe plastic deformation at high temperature, the grains in the grain-sparse region undergo more serious extrusion deformation, abnormal growth of the grains occurs, and the alloy profile with the heterostructure is formed.
Combining with the comparative example and experiments, it is found that: with the increase of the solid solution time, the content of coarse grains in the heterogeneous structure is increased, the content of fine grains is reduced, and the heterogeneous structure with different coarse/fine grain ratios can be obtained by adjusting the solid solution heat treatment time, so as to manufacture the aluminum alloy with different properties and also having the heterogeneous structure, further the application field and the application are more, and the practicability is stronger, especially when TiB is added 2 After the step 1 to the step 11, the solid solution state heterogeneous alloy section is set to have the heat preservation temperature of 560 ℃ in the step 11, the solid solution heat treatment time is 3 hours, and when the ratio of coarse grains to fine grains in the alloy section is 2:1 through analysis of an EBSD grain morphology graph, the yield strength is improved by 125%, the tensile strength is improved by 49%, the elongation is kept good, and the comprehensive mechanical property is good.
Example 2
In comparison with example 1, the 2000-series Al-Cu-Mg aluminum alloy profile is prepared in the embodiment 2, and the specific preparation steps include:
s1' is selected to contain TiB 2 And TiC particles, and Al-50Cu (7.6 wt% -9.8 wt)Raw materials for smelting Al-10Mn (3 wt% -9 wt%), mg ingot (1.3 wt% -1.8 wt%) and the balance being pure Al ingot, and TiB is to be contained 2 And TiC particles, wherein the aluminum intermediate alloy ingot, al-50Cu, al-10Mn and pure Al ingot are placed into a smelting furnace, and TiB is contained 2 The aluminum intermediate alloy ingot with TiC particles comprises the following components: tiB (TiB) 2 And TiC particles (3 wt% -6 wt%) and the rest being pure Al, while TiB 2 The respective proportion of TiC particles is 2:5-1:1 (the configuration proportion can be but is not limited to 2.2:1, 2.0:1, 1.8:1 and the like);
s2', when the temperature in the smelting furnace reaches over 780 ℃, adding inert gas argon for protection;
s3', heating the temperature in the smelting furnace to 800-850 ℃;
s4', after the alloy in the smelting furnace is completely melted, adding an Mg ingot into the melt;
s5', stirring the Mg ingot and the alloy uniformly by using a stirrer;
s6', a melt purifying procedure, refining, degassing and deslagging in a smelting furnace, wherein the residual alloy components after smelting are 1.2-1.8 wt% of Mg, 0.3-0.9 wt% of Mn, 3.8-4.9 wt% of Cu and TiB 2 +tic particles: 0.5 to 2.5 weight percent, and the rest is pure Al ingot;
s7', cooling the alloy in the smelting furnace to 720 ℃ -750 ℃ (the smelting furnace can be closed, and naturally cooling the alloy in the smelting furnace to 720 ℃ -750 ℃;
s8', casting the smelted alloy into a round ingot by casting or semi-continuous casting;
s9', uniformly performing heat treatment, namely putting the round ingot into a heating furnace to heat the ingot to 480-530 ℃ for 16-24 hours;
s10', hot extrusion, namely passing the cast ingot subjected to uniform heat treatment through an extruder at the temperature of 400-450 ℃ according to the extrusion ratio: 20-50 and extrusion speed: extruding the cast ingot at 0.8-4 m/min;
s11', solution heat treatment, and heat preservation at 500-530 ℃ for 0.5-10 hours.
Example 3
In example 3, as compared with example 1, 7000 series Al-Zn-Mg-Cu aluminum alloy sections were prepared, and the specific preparation steps include:
s1' contains TiB 2 And TiC particles (10 wt% -50 wt%), al-50Cu (0 wt% -4 wt%), al-5Cr (1 wt% -5 wt%), mg ingot (2 wt% -3 wt%), zn ingot (5 wt% -7 wt%) and the balance being pure Al ingot are placed into a smelting furnace, wherein the smelting raw materials contain TiB 2 The aluminum intermediate alloy ingot with TiC particles comprises the following components: tiB (TiB) 2 And TiC particles (3 wt% -6 wt%) and the rest being pure Al, while TiB 2 The respective proportion of TiC particles is 2:5-1:1 (the configuration proportion can be but is not limited to 2.2:1, 2.0:1, 1.8:1 and the like);
s2', when the temperature in the smelting furnace reaches over 780 ℃, adding inert gas argon for protection;
s3', heating the temperature in the smelting furnace to 800-850 ℃;
s4', after the alloy in the smelting furnace is completely melted, immersing the Mg ingot and the Zn ingot into the melt;
s5', uniformly stirring the Mg ingot, the Zn ingot and the alloy by using a stirrer;
s6", a melt purification procedure, refining, degassing and deslagging are carried out in a smelting furnace, wherein the final components of the alloy after smelting are 2.0-3.0 wt% of Mg, 5.0-7.0 wt% of Zn, 0-2 wt% of Cu, 0.05-0.25 wt% of Cr and TiB 2 +tic particles: 0.5 to 2.5 weight percent, and the rest is pure Al ingot;
s7', cooling the alloy in the smelting furnace to 720 ℃ -750 ℃ (the smelting furnace can be closed, and naturally cooling the alloy in the smelting furnace to 720 ℃ -750 ℃;
s8', casting the smelted alloy into a round ingot by casting or semi-continuous casting;
s9', uniformly heating, namely putting the round ingot into a heating furnace to heat 450-470 ℃ for 18-24 hours;
s10', hot extrusion, namely passing the round cast ingot subjected to uniform heat treatment through an extruder at the temperature of 400-450 ℃ according to the extrusion ratio: 20-40 and extrusion speed: extruding the cast ingot at a speed of 0.5-2 m/min;
s11', carrying out solution heat treatment, and carrying out heat preservation at the temperature of 460-475 ℃ for 0.5-10 hours.
The foregoing description of the preferred embodiments of the invention is not intended to limit the invention to the precise form disclosed, and any such modifications, equivalents, and alternatives falling within the spirit and scope of the invention are intended to be included within the scope of the invention.
Claims (11)
1. The preparation method of the aluminum alloy section with the mixed crystal heterostructure characteristics is characterized by comprising the following steps of:
smelting with pure Al and TiB 2 And TiC particles, and aluminum intermediate alloy and pure metal which are added for manufacturing different series of aluminum alloy sections are smelted at the temperature of 800-850 ℃;
casting, namely casting the smelted alloy at the temperature of 720-750 ℃ to form an ingot;
uniformly heat-treating, namely heating the cast ingot to 450-560 ℃ for 8-24 hours;
hot extrusion, namely, casting the ingot after uniform heat treatment at the temperature of 400-450 ℃ according to the extrusion ratio: 20 to 60 and extrusion speed: extruding the cast ingot at 0.5-10 m/min;
solution heat treatment is carried out for 0.5 to 10 hours at the temperature of 460 to 570 ℃ for heat preservation.
2. The method for preparing an aluminum alloy section with mixed crystal heterostructure features according to claim 1, wherein the step of melting the alloy comprises:
s1, selecting TiB 2 And TiC particles (10 wt% -50 wt%) and smelting raw material for adding aluminium intermediate alloy and pure metal (7 wt% -21 wt%) required for making different series aluminium alloy section and the rest is pure Al, and making TiB-containing alloy material 2 Aluminum intermediate alloy with TiC particles, aluminum intermediate alloy added for manufacturing different series aluminum alloy profilesPure Al is put into a smelting furnace, wherein the pure Al contains TiB 2 The aluminum intermediate alloy with TiC particles comprises the following components: tiB (TiB) 2 And TiC particles (3 wt% -6 wt%) and the rest being pure Al, while TiB 2 The proportion of the TiC particles to the TiC particles is 2:5-1:1;
s2, adding inert gas for protection when the temperature in the smelting furnace reaches over 780 ℃;
s3, heating the temperature in the smelting furnace to 800-850 ℃;
s4, after the alloy in the smelting furnace is completely melted, immersing at least one pure metal with the melting point lower than that of Al into the alloy melt;
s5, uniformly stirring the pure metal and the alloy melt by using a stirrer;
s6, a melt purifying procedure, wherein refining, degassing and deslagging are carried out in the smelting furnace.
3. The method for preparing the aluminum alloy section with the mixed crystal heterostructure features according to claim 2, wherein the aluminum intermediate alloy added for manufacturing the aluminum alloy section of different series comprises Al-20Si, al-50Cu and Al-10Mn, and the pure metal in S4 and S5 is Mg.
4. The method for preparing the aluminum alloy section with the mixed crystal heterostructure features according to claim 2, wherein the aluminum intermediate alloy added for manufacturing the aluminum alloy section of different series comprises Al-50Cu and Al-10Mn, and the pure metal in S4 and S5 is Mg.
5. The method for preparing the aluminum alloy section with the mixed crystal heterostructure features according to claim 2, wherein the aluminum intermediate alloy added for manufacturing the aluminum alloy section of different series comprises Al-50Cu and Al-5Cr, and pure metals in S4 and S5 are Mg and Zn.
6. The method for producing an aluminum alloy profile with mixed crystal heterostructure features according to claim 1, wherein the casting step of the alloy comprises:
s1', firstly, cooling the alloy in the smelting furnace to 720-750 ℃;
s2', casting the smelted alloy into a round ingot by casting or semi-continuous casting.
7. The method for preparing the aluminum alloy section with the mixed crystal heterostructure features according to claim 3, wherein the uniform heat treatment comprises the steps of putting an ingot into a heating furnace to heat at 530-560 ℃ for 8-16 hours, and the hot extrusion comprises the steps of passing the ingot after the uniform heat treatment through an extruder at the temperature of 400-450 ℃ according to the extrusion ratio: 30-60 and extrusion speed: extruding the ingot at a temperature of between 550 and 570 ℃ for between 0.5 and 10 hours.
8. The method for preparing an aluminum alloy section with mixed crystal heterostructure features according to claim 4, wherein the uniform heat treatment comprises heating an ingot in a heating furnace at 480 ℃ to 530 ℃ for 16 hours to 24 hours, and the hot extrusion comprises passing the ingot after the uniform heat treatment through an extruder at a temperature of 400 ℃ to 450 ℃ according to an extrusion ratio: 20-50 and extrusion speed: extruding the ingot at 0.8-4 m/min, wherein the solution heat treatment comprises the step of continuously heating at 500-530 ℃ for 0.5-10 hours.
9. The method for preparing an aluminum alloy section with mixed crystal heterostructure features according to claim 5, wherein the uniform heat treatment comprises the steps of placing an ingot into a heating furnace to heat 450-470 ℃ for 18-24 hours, and the hot extrusion comprises the steps of passing the ingot after the uniform heat treatment through an extruder at a temperature of 400-450 ℃ according to an extrusion ratio: 20-40 and extrusion speed: the ingot is extruded at 0.5 m-2 m/min, and the solution heat treatment comprises the step of continuously heating at 460-475 ℃ for 0.5-10 hours.
10. An aluminum alloy profile with mixed crystal heterostructure characteristics, manufactured by the method according to any one of claims 1 to 9, characterized in that the aluminum alloy profile has grains in which coarse crystals and fine crystals are mixed.
11. The aluminum alloy section with mixed crystal heterostructure features of claim 10, wherein different proportions of coarse grains and fine grains within a grain can be obtained by adjusting the time of the solution heat treatment.
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