CN117512409A - Aluminum alloy wire with high thermal stability and preparation method thereof - Google Patents
Aluminum alloy wire with high thermal stability and preparation method thereof Download PDFInfo
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- CN117512409A CN117512409A CN202311477275.XA CN202311477275A CN117512409A CN 117512409 A CN117512409 A CN 117512409A CN 202311477275 A CN202311477275 A CN 202311477275A CN 117512409 A CN117512409 A CN 117512409A
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- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 111
- 238000002360 preparation method Methods 0.000 title claims abstract description 18
- 239000000956 alloy Substances 0.000 claims abstract description 63
- 238000001125 extrusion Methods 0.000 claims abstract description 42
- 239000000463 material Substances 0.000 claims abstract description 38
- 230000032683 aging Effects 0.000 claims abstract description 37
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 33
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims abstract description 33
- 229910000542 Sc alloy Inorganic materials 0.000 claims abstract description 20
- 238000003723 Smelting Methods 0.000 claims abstract description 20
- 229910045601 alloy Inorganic materials 0.000 claims description 37
- 238000000034 method Methods 0.000 claims description 21
- 238000000265 homogenisation Methods 0.000 claims description 16
- 238000005266 casting Methods 0.000 claims description 15
- 230000008569 process Effects 0.000 claims description 13
- 239000002994 raw material Substances 0.000 claims description 12
- 238000003756 stirring Methods 0.000 claims description 12
- 238000007670 refining Methods 0.000 claims description 11
- 238000012360 testing method Methods 0.000 claims description 11
- 238000010438 heat treatment Methods 0.000 claims description 10
- 238000004519 manufacturing process Methods 0.000 claims description 9
- 239000010936 titanium Substances 0.000 claims description 9
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 9
- 238000002844 melting Methods 0.000 claims description 8
- 230000008018 melting Effects 0.000 claims description 8
- 238000001816 cooling Methods 0.000 claims description 7
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 6
- 239000003795 chemical substances by application Substances 0.000 claims description 6
- 238000007872 degassing Methods 0.000 claims description 6
- 239000012535 impurity Substances 0.000 claims description 6
- 239000007788 liquid Substances 0.000 claims description 6
- 238000010791 quenching Methods 0.000 claims description 6
- 230000000171 quenching effect Effects 0.000 claims description 6
- 239000010935 stainless steel Substances 0.000 claims description 6
- 229910001220 stainless steel Inorganic materials 0.000 claims description 6
- 230000007423 decrease Effects 0.000 claims description 5
- 229910052799 carbon Inorganic materials 0.000 claims description 4
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 3
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 claims description 3
- 229910052786 argon Inorganic materials 0.000 claims description 3
- 239000011248 coating agent Substances 0.000 claims description 3
- 238000000576 coating method Methods 0.000 claims description 3
- 238000001035 drying Methods 0.000 claims description 3
- 230000003647 oxidation Effects 0.000 claims description 3
- 238000007254 oxidation reaction Methods 0.000 claims description 3
- 238000005498 polishing Methods 0.000 claims description 3
- 238000004321 preservation Methods 0.000 claims description 3
- 229910052719 titanium Inorganic materials 0.000 claims description 3
- 239000011159 matrix material Substances 0.000 description 10
- 239000000523 sample Substances 0.000 description 9
- 239000002245 particle Substances 0.000 description 7
- 239000006185 dispersion Substances 0.000 description 5
- 230000001427 coherent effect Effects 0.000 description 4
- 230000007797 corrosion Effects 0.000 description 4
- 238000005260 corrosion Methods 0.000 description 4
- 230000000694 effects Effects 0.000 description 4
- 238000005728 strengthening Methods 0.000 description 4
- 238000004458 analytical method Methods 0.000 description 3
- 238000010146 3D printing Methods 0.000 description 2
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 2
- 230000009286 beneficial effect Effects 0.000 description 2
- 239000012496 blank sample Substances 0.000 description 2
- 150000001875 compounds Chemical class 0.000 description 2
- 238000005336 cracking Methods 0.000 description 2
- 238000002425 crystallisation Methods 0.000 description 2
- 230000008025 crystallization Effects 0.000 description 2
- 230000007547 defect Effects 0.000 description 2
- 238000013461 design Methods 0.000 description 2
- 230000005496 eutectics Effects 0.000 description 2
- 239000007789 gas Substances 0.000 description 2
- 239000011521 glass Substances 0.000 description 2
- 230000017525 heat dissipation Effects 0.000 description 2
- 229910052751 metal Inorganic materials 0.000 description 2
- 239000002184 metal Substances 0.000 description 2
- 230000006911 nucleation Effects 0.000 description 2
- 238000010899 nucleation Methods 0.000 description 2
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- 239000000243 solution Substances 0.000 description 2
- 239000000126 substance Substances 0.000 description 2
- 238000009864 tensile test Methods 0.000 description 2
- 229910018131 Al-Mn Inorganic materials 0.000 description 1
- 229910018461 Al—Mn Inorganic materials 0.000 description 1
- 229910000882 Ca alloy Inorganic materials 0.000 description 1
- 229910015136 FeMn Inorganic materials 0.000 description 1
- 239000002253 acid Substances 0.000 description 1
- 230000009471 action Effects 0.000 description 1
- 239000000654 additive Substances 0.000 description 1
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- 230000003247 decreasing effect Effects 0.000 description 1
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- 238000005137 deposition process Methods 0.000 description 1
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- 230000010354 integration Effects 0.000 description 1
- 229910000765 intermetallic Inorganic materials 0.000 description 1
- 230000007246 mechanism Effects 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- 238000010587 phase diagram Methods 0.000 description 1
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- 239000006104 solid solution Substances 0.000 description 1
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- 230000008023 solidification Effects 0.000 description 1
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- 239000011573 trace mineral Substances 0.000 description 1
- 235000013619 trace mineral Nutrition 0.000 description 1
- 230000007704 transition Effects 0.000 description 1
- 238000003466 welding Methods 0.000 description 1
- 238000005491 wire drawing Methods 0.000 description 1
Classifications
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- 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
- C22C21/003—Alloys based on aluminium containing at least 2.6% of one or more of the elements: tin, lead, antimony, bismuth, cadmium, and titanium
-
- 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
- C22C1/02—Making non-ferrous alloys by melting
- C22C1/026—Alloys based on aluminium
-
- 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
- C22C1/02—Making non-ferrous alloys by melting
- C22C1/03—Making non-ferrous alloys by melting using master alloys
-
- 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
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
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- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Extrusion Of Metal (AREA)
Abstract
The invention discloses an aluminum alloy wire with high thermal stability, which comprises a base material of a pure aluminum material, wherein a Sc, si, ti, mn, zr element material is added in the base material of the pure aluminum material to form an Al-Si-Ti-Mn-Zr-Sc alloy material. The invention also provides a preparation method of the aluminum alloy wire with high thermal stability, which comprises the steps of batching, preheating, smelting, homogenizing, pre-aging and extrusion.
Description
Technical Field
The invention relates to the technical field of aluminum alloy materials, in particular to an aluminum alloy wire with high thermal stability and a preparation method thereof.
Background
The aluminum alloy has low density, high strength and excellent conductivity and corrosion resistance, so that the aluminum alloy is widely used in the fields of automobiles, mechanical ships, aerospace and the like, wherein the aluminum alloy wire has light weight, low density, good heat dissipation and strong compression resistance, can fully meet the requirements of high integration, light weight, miniaturization, crash and impact resistance, electromagnetic shielding and heat dissipation of a 3C product, and has the hardness which is several times that of the traditional glass wire, but the weight is only one third of that of the traditional glass wire.
At present, most of aluminum alloy wire processing is extrusion or drawing technology, and the existing commercial aluminum alloy wire has the defects of weak high-temperature stability and softening and early failure in service under a high-temperature environment. The patent No. CN202310791726.0 discloses a high-strength heat-resistant aluminum alloy wire and a preparation method and an electric arc additive manufacturing method thereof, and adopts a Cold Metal Transition (CMT) deposition mode to prepare the aluminum alloy wire with strength meeting the requirements of high temperature and high temperature performance by optimizing deposition process parameters and combining alloy element design, but the preparation process is complex and the flow is complex. Patent number CN202010362332.X discloses an Al-Zn-Mg-Sc aluminum alloy wire for 3D printing and a preparation method thereof, and discloses a preparation method of the Al-Zn-Mg-Sc aluminum alloy wire for 3D printing, which comprises the steps of batching, vacuum melting, casting, homogenizing treatment, ingot surface post-treatment and wire drawing, but the obtained wire is not subjected to heat resistance detection and cannot be used for explaining high-temperature stability.
Disclosure of Invention
The invention aims to provide an aluminum alloy wire with high thermal stability, which has good high-temperature stability and good mechanical property.
In order to solve the technical problems, the invention adopts a technical scheme that: the aluminum alloy wire with high thermal stability comprises a base material of a pure aluminum material, wherein Sc, si, ti, mn, zr elements are added into the base material of the pure aluminum material to form an Al-Si-Ti-Mn-Zr-Sc alloy material, the balance is an impurity element material, the Sc element material accounts for 0.05% -0.15% of the total mass of the Al-Si-Ti-Mn-Zr-Sc alloy material, the Si element material accounts for 0.3% -0.5% of the total mass of the Al-Si-Ti-Mn-Zr-Sc alloy material, the Ti element material accounts for 0.5% -1.0% of the total mass of the Al-Si-Ti-Mn-Zr-Sc alloy material, the Mn element material accounts for 0.05% -0.1% of the total mass of the Al-Si-Ti-Mn-Zr-Sc alloy material, and the impurity element material accounts for less than 0.03% of the total mass of the Al-Si-Ti-Mn-Zr-Sc alloy material.
The invention provides a preparation method of an aluminum alloy wire with high thermal stability, which comprises the following steps:
(1) Preparing raw materials according to the components of the alloy materials and the mass content of the components, and carrying out surface dirt removal and oxidation skin treatment on the raw materials;
(2) Preheating and drying the raw materials in a resistance furnace to evaporate the surface moisture of the raw materials;
(3) Adding preheated pure aluminum into a crucible, after the pure aluminum is completely melted, sequentially adding Sc, si, ti, mn, zr element materials for smelting, wherein the smelting temperature is 710-750 ℃, then pouring alloy materials to obtain an aluminum alloy casting, and then standing and preserving heat;
(4) Homogenizing the aluminum alloy casting, and quenching with warm water after the homogenization;
(5) And carrying out pre-ageing treatment and extrusion treatment on the aluminum alloy casting subjected to the homogenization treatment to obtain the aluminum alloy wire.
Preferably, the preheating in step (2) is carried out at a temperature ranging from 200 ℃ to 300 ℃ and for a preheating time ranging from 0.5 to 2 hours.
Preferably, the smelting furnace temperature is set to 730 ℃ in the smelting in the step (3), when the smelting furnace temperature rises to the preset temperature of 730 ℃, the preheated pure aluminum ingot is put into a crucible of the smelting furnace, and after the pure aluminum ingot is kept stand and melted, the preheated pure titanium, the Al-30Mn intermediate alloy, the Al-20Si alloy, the Al-20Ca intermediate alloy and the Al-20Zr intermediate alloy are respectively added into the crucible of the smelting furnace; then raising the smelting temperature to 750 ℃ and preserving heat for 10 minutes; finally adding Mg-30Sc intermediate alloy preheated to 200 ℃, preserving heat for 5 minutes, and stirring for 5 minutes; next, starting refining treatment, adding a refining agent into the molten liquid in the crucible, continuously stirring the molten liquid by using a stainless steel screw stirrer in the adding process, wherein the stirring speed of the stirrer is 30r/min, the stirring time is 5-10min, and keeping the temperature and standing for 10-15 min after the refining agent is added; introducing argon for 10-15 minutes after standing is finished, and carrying out degassing treatment; after the degassing is finished, carrying out surface skimming, and removing surface scum by using a stainless steel spoon; finally, the furnace temperature is reduced by 730 ℃, and the furnace is kept stand for 10 to 15 minutes; pouring the aluminum alloy melt after standing into a cylindrical mold preheated to 250 ℃ to prepare a rod-shaped as-cast aluminum alloy cast ingot.
Preferably, the homogenization treatment in the step (4) comprises heating the obtained rod-shaped as-cast aluminum alloy ingot to 400-480 ℃ along with a furnace, preserving the temperature for 12-15 hours for homogenization treatment, and immediately placing the rod-shaped as-cast aluminum alloy ingot into warm water at 60-80 ℃ for quenching treatment at the end.
Preferably, the pre-ageing treatment in the step (5) comprises the steps of carrying out heat preservation treatment at 150-300 ℃ in a resistance furnace, taking out a rod-shaped as-cast aluminum alloy ingot blank every 1-2 hours for water cooling, then carrying out hardness test until the hardness reaches the highest value, wherein the blank with the highest hardness is a peak ageing blank, and the blank is in an overageing state after the hardness value is reduced. In order to ensure that the blank is in an overaging state, an ingot casting 80-100 hours after peak aging is used as a pre-aging treatment time, namely the pre-aging treatment time is 100-120 hours.
Preferably, the pre-ageing treatment in the step (5) comprises ageing treatment at 200 ℃ of the blank after the homogenization treatment, taking out the blank every 2 hours and carrying out hardness test until the hardness starts to decrease after the peak value appears, and selecting the blank 100 hours after the peak ageing time as an overageing blank to carry out the subsequent extrusion deformation.
Preferably, the extrusion treatment in the step (5) comprises the preparation work before extrusion, namely coating graphite powder on the inner cavity and the surface of an extrusion die, heating the extrusion die to 380 ℃ along with the furnace in a resistance furnace, polishing and removing oxidized skin on the surface of the rod-shaped as-cast aluminum alloy ingot before extrusion starts, heating the rod-shaped as-cast aluminum alloy ingot to 380 ℃ in the resistance furnace, preserving heat for 30 minutes, installing the preheated extrusion die into an extruder, and raising the temperature of the extruder to the extrusion temperature.
Preferably, the extrusion treatment in the step (5) comprises extrusion molding of the preheated rod-shaped as-cast aluminum alloy ingot in an extruder at 380 ℃ and at 0.5-1mm/s, obtaining an aluminum alloy wire after extrusion, and air-cooling the aluminum alloy wire to room temperature.
The beneficial effects of the invention are as follows: according to the aluminum alloy wire with high thermal stability, the trace elements such as Sc, ti and Si are added into pure aluminum for modification, and the pre-ageing treatment process is added into the preparation method, so that the novel aluminum alloy wire has good high-temperature stability, and the mechanical property is greatly improved compared with that of a commercial 5183 aluminum alloy wire.
Drawings
For a clearer description of the technical solutions of the embodiments of the present invention, the drawings that are needed in the description of the embodiments will be briefly introduced below, it being obvious that the drawings in the description below are only some embodiments of the present invention, and that other drawings can be obtained according to these drawings without inventive effort for a person skilled in the art, wherein:
FIG. 1 is a graph comparing mechanical properties of novel aluminum alloy wires prepared in the present invention with those of commercial 5183 alloy wires;
FIG. 2 is a graph of thermal expansion analysis of a commercial 5183 alloy wire in accordance with the present invention;
FIG. 3 is a graph showing thermal expansion analysis of the novel aluminum alloy wire according to the present invention.
Detailed Description
The following description of the technical solutions in the embodiments of the present invention will be clear and complete, and it is obvious that the described embodiments are only some embodiments of the present invention, but not all embodiments. All other embodiments, which can be made by those skilled in the art based on the embodiments of the invention without making any inventive effort, are intended to be within the scope of the invention.
The embodiment of the invention comprises the following steps:
the invention provides an aluminum alloy wire with high thermal stability, which comprises a base material of a pure aluminum material, wherein Sc, si, ti, mn, zr elements are added in the base material of the pure aluminum material to form an Al-Si-Ti-Mn-Zr-Sc alloy material, the balance is an impurity element material, wherein the Sc element material accounts for 0.05% -0.15% of the total mass of the Al-Si-Ti-Mn-Zr-Sc alloy material, the Si element material accounts for 0.3% -0.5% of the total mass of the Al-Si-Ti-Mn-Zr-Sc alloy material, the Ti element material accounts for 0.5% -1.0% of the total mass of the Al-Si-Ti-Mn-Zr-Sc alloy material, the Mn element material accounts for 0.05% -0.1% of the total mass of the Al-Si-Ti-Mn-Zr-Sc alloy material, and the impurity element material accounts for less than 0.03% of the total mass of the Al-Si-Ti-Mn-Zr-Sc alloy material.
Sc used in the present invention is a light metal having a density ρ.about.3g.cm-3 and a melting point 1541 ℃. The Sc-containing aluminum alloy has excellent performance and wide application field, the simple substance form of Sc is already applied to the doping of the aluminum alloy, and a new phase of Al3Sc can be generated by adding a few thousandths of Sc into aluminum, so that the performance of the aluminum alloy is obviously improved. The maximum solid solubility of Sc in aluminum at the eutectic temperature is 0.38at%, and during solidification, the solubility of Sc in aluminum decreases sharply with decreasing temperature, so that the Sc-containing aluminum alloy is a remarkable age-strengthened aluminum alloy, and Sc and aluminum can form four intermediate compounds of Al3Sc, al2Sc, alSc and AlSc 3. The vast majority of Sc in Sc-containing aluminum alloys tends to be in supersaturated solid solution in the non-equilibrium state and form a dispersed and coherent secondary Al3Sc phase with the matrix during subsequent heat treatment. Al3Sc is L12 (Cu 3Au type) structure, the lattice constant is 0.410nm, the degree of mismatching with the aluminum matrix is very small (1.34% at 24 ℃), so that the precipitated Al3Sc and the matrix are coherent, dislocation can be strongly pinned, grain growth is hindered, and the alloy is obviously refined and strengthened. Therefore, the addition amount of Sc element in the invention is more than or equal to 0.05 percent and less than or equal to 0.15 percent, and the aluminum alloy can be obviously thinned and strengthened.
The addition of Si in the invention improves the casting performance of the aluminum alloy, and the content of the Si is important to the strengthening effect of the aluminum alloy. The increased Si content can improve the fluidity of the aluminum alloy, thereby being more beneficial to manufacturing complex and precise thin-wall products, reducing the hot cracking tendency of the aluminum alloy and improving the air tightness of the alloy, because the shrinkage rate of Si element is small, and the linear shrinkage rate of the alloy is reduced after the Si element is added. In addition, si has high chemical stability and high hardness, and has hardness of 880-1040HV, and the corrosion resistance of the alloy in medium acid environment can be improved by Si, so that the aluminum alloy containing Si has good high heat stability, corrosion resistance and wear resistance. Therefore, in summary, the addition amount of Si element in the invention is 0.3 percent or more and 0.5 percent or less, and the requirement of improving the performance of the aluminum alloy can be met.
Ti is also added in the invention, ti element can form an Al3Ti dispersion phase with dispersion strengthening effect with an aluminum matrix, and meanwhile, as a good common relation is formed between the Al3Ti dispersion phase and the aluminum matrix, the alloy can serve as a hard nucleation site in the alloy crystallization process, and the effect of grain refinement can be achieved. In addition, the Ti element can inhibit the growth of the alpha-Al matrix after being added, thereby achieving the effect of further refining the structure and improving the toughness and the fatigue resistance of the alloy. Therefore, in summary, the addition amount of Ti element in the invention is more than or equal to 0.5% and less than or equal to 1.0%, so that the toughness and fatigue resistance of the aluminum alloy can be improved.
The invention also adds Mn, the maximum solubility of Mn in aluminum matrix is 1.82wt.% when Al-Mn alloy equilibrium phase diagram part is at eutectic temperature 658 ℃, the alloy strength is increased along with the increase of solubility, and the plasticity of the alloy reaches the maximum when the Mn content is 0.8 wt.%. The dispersion particles generated by Mn in the aluminum alloy can exist stably in the homogenization treatment process, and the dispersion particles can prevent the grains after recrystallization from growing up so as to play a role in refining the grains. Meanwhile, mn particles can be combined with iron element in the aluminum alloy to form an Al6 (FeMn) compound, so that the defects of poor corrosion performance and the like caused by the existence of the iron element in the alloy are overcome. However, when the Mn content exceeds 0.8wt.%, coarse dendritic AlFeSiMn-based intermetallic compounds are easily generated, and the plasticity and formability of the aluminum alloy are seriously deteriorated. Therefore, in summary, the addition amount of Mn element is more than or equal to 0.05% and less than or equal to 0.1% in the invention, so that the plasticity of the aluminum alloy can be improved.
Zr is a common micro-alloy element, and the solid solubility of Zr in an aluminum matrix is extremely low, so that the Zr element can react with the aluminum matrix to generate a large amount of dispersed Al3Zr phases, and the dispersed phases can play a role of nucleation sites in the alloy crystallization process and play a role of grain refinement; meanwhile, the Al3Zr particles and the aluminum matrix have good coherent relation, dislocation can be pinned, and the coherent phase can pin the dislocation and can not excessively cause stress concentration, so that plasticity is not excessively damaged while strengthening. However, if an excessive amount of Zr element is added to the alloy, the excessive Al3Zr phase may aggregate to form a coarse phase, resulting in a great decrease in mechanical properties of the alloy. Therefore, in summary, the addition amount of Zr element in the invention is 0.05 percent or more and is less than or equal to 0.1 percent or less, and the plastic property and the mechanical property of the aluminum alloy can be improved.
In the present invention, the al—cu—mn—ca alloy may be used as a product such as recycled aluminum to improve recycling of resources, while ensuring that the above elements fall within the above-described limit.
The invention provides a preparation method of an aluminum alloy wire with high thermal stability, which comprises the following steps:
(1) Preparing raw materials according to the components of the alloy materials and the mass content of the components, and carrying out surface dirt removal and oxidation skin treatment on the raw materials;
(2) Preheating and drying the raw materials in a resistance furnace to evaporate the surface moisture of the raw materials;
(3) Adding preheated pure aluminum into a crucible, after the pure aluminum is completely melted, sequentially adding Sc, si, ti, mn, zr element materials for smelting, wherein the smelting temperature is 710-750 ℃, then pouring alloy materials to obtain an aluminum alloy casting, and then standing and preserving heat;
(4) Homogenizing the aluminum alloy casting, and quenching with warm water after the homogenization;
(5) And carrying out pre-ageing treatment and extrusion treatment on the aluminum alloy casting subjected to the homogenization treatment to obtain the aluminum alloy wire.
The aluminum alloy wire with high thermal stability, plasticity and mechanical property can be manufactured by the process method.
Preferably, the preheating in step (2) is carried out at a temperature ranging from 200 ℃ to 300 ℃ and for a preheating time ranging from 0.5 to 2 hours.
Preferably, the smelting furnace temperature is set to 730 ℃ in the smelting in the step (3), when the smelting furnace temperature rises to the preset temperature of 730 ℃, the preheated pure aluminum ingot is put into a crucible of the smelting furnace, and after the pure aluminum ingot is kept stand and melted, the preheated pure titanium, the Al-30Mn intermediate alloy, the Al-20Si alloy, the Al-20Ca intermediate alloy and the Al-20Zr intermediate alloy are respectively added into the crucible of the smelting furnace; then raising the smelting temperature to 750 ℃ and preserving heat for 10 minutes; finally adding Mg-30Sc intermediate alloy preheated to 200 ℃, preserving heat for 5 minutes, and stirring for 5 minutes; next, starting refining treatment, adding a refining agent into the molten liquid in the crucible, continuously stirring the molten liquid by using a stainless steel screw stirrer in the adding process, wherein the stirring speed of the stirrer is 30r/min, the stirring time is 5-10min, and keeping the temperature and standing for 10-15 min after the refining agent is added; introducing argon for 10-15 minutes after standing is finished, and carrying out degassing treatment; after the degassing is finished, carrying out surface skimming, and removing surface scum by using a stainless steel spoon; finally, the furnace temperature is reduced by 730 ℃, and the furnace is kept stand for 10 to 15 minutes; pouring the aluminum alloy melt after standing into a cylindrical mold preheated to 250 ℃ to prepare a rod-shaped as-cast aluminum alloy cast ingot, wherein protective gas is not required to be introduced in the casting process.
Preferably, the homogenization treatment in the step (4) comprises heating the obtained rod-shaped cast aluminum alloy ingot to 400-480 ℃ along with a furnace, preserving the temperature for 12-15 hours for homogenization treatment, and immediately placing the rod-shaped cast aluminum alloy ingot into warm water at 60-80 ℃ for quenching treatment at the end to avoid cracking of the cast due to excessively high alloy cooling rate, wherein the whole homogenization treatment process is carried out in the natural atmosphere of a hearth without gas protection.
Preferably, the pre-ageing treatment in the step (5) comprises the steps of carrying out heat preservation treatment at 150-300 ℃ in a resistance furnace, taking out a rod-shaped as-cast aluminum alloy ingot blank every 1-2 hours for water cooling, then carrying out hardness test until the hardness reaches the highest value, wherein the blank with the highest hardness is a peak ageing blank, and the blank is in an overageing state after the hardness value is reduced. In order to ensure that the blank is in an overaging state, an ingot casting 80-100 hours after peak aging is used as a pre-aging treatment time, namely the pre-aging treatment time is 100-120 hours.
Preferably, the pre-ageing treatment in the step (5) comprises ageing treatment at 200 ℃ of the blank after the homogenization treatment, taking out the blank every 2 hours and carrying out hardness test until the hardness starts to decrease after the peak value appears, and selecting the blank 100 hours after the peak ageing time as an overageing blank to carry out the subsequent extrusion deformation.
On the basis of a large number of researches, the applicant of the invention discovers that the addition of a trace amount of Sc element can obviously improve the high-temperature stability of the aluminum alloy, and the action mechanism is mainly due to the fact that a large amount of Al3Sc second phase particles are formed in an alloy microstructure, and the Al3Sc phase has excellent high-temperature stability and excellent stability in a medium-high-temperature environment. In addition, the pre-ageing treatment is adopted before extrusion, and the main function of the pre-ageing treatment is to enable the second-phase particles precipitated by ageing to be coarsened continuously after the overageing treatment, and then the second-phase particles are crushed in the extrusion process so as to be distributed more uniformly. In addition, the second phase generated in the pre-ageing process can still play a role in strengthening after extrusion, so that the strength and high-temperature stability of the aluminum alloy are improved.
Preferably, the extrusion treatment in the step (5) comprises the preparation work before extrusion, namely coating graphite powder on the inner cavity and the surface of an extrusion die, heating the extrusion die to 380 ℃ along with the furnace in a resistance furnace, polishing and removing oxidized skin on the surface of the rod-shaped as-cast aluminum alloy ingot before extrusion starts, heating the rod-shaped as-cast aluminum alloy ingot to 380 ℃ in the resistance furnace, preserving heat for 30 minutes, installing the preheated extrusion die into an extruder, and raising the temperature of the extruder to the extrusion temperature.
Preferably, the extrusion treatment in the step (5) comprises extrusion molding of the preheated rod-shaped as-cast aluminum alloy ingot in an extruder at 380 ℃ and at 0.5-1mm/s, obtaining an aluminum alloy wire after extrusion, and air-cooling the aluminum alloy wire to room temperature.
The performance of the aluminum alloy wire in the embodiment of the invention is detected:
test 1: referring to fig. 1 to 3, the extruded aluminum alloy wire was subjected to thermal expansion analysis, and the results showed that CTE curves were substantially coincident after 20 thermal cycles, and thermal stability was excellent. The aluminum alloy wire is processed into a tensile sample shape for room temperature tensile test, the specification of the tensile sample meets the GB/T16865-2013 standard, the tensile test method meets the GB/T228.1-2010 standard, the yield strength of the obtained extruded wire sample is 225MPa, the tensile strength is 370Pa, and the elongation is 35%.
Test 2: changing the 100-hour overaging blank sample in the step (5) into a 64-hour Shi Feng aging blank sample, wherein the stable thermal cycle times of the obtained extrusion sample are 15 times, and larger fluctuation starts to appear in more than 15 times. The yield strength of the obtained sample was 233MPa, the tensile strength was 374MPa, and the elongation was 34%.
Test 3: the test sample is different from the test 1 in that the sample does not undergo the pre-ageing treatment stage in the step (5), the blank which does not undergo the pre-ageing treatment is extruded, the stable thermal cycle times of the obtained extruded sample are 10 times, and larger fluctuation starts to appear in more than 10 times. The yield strength of the obtained sample was 229MPa, the tensile strength was 367MPa, and the elongation was 29%.
The traditional aluminum alloy wire in the prior art has low high-temperature stability, and the aluminum alloy wire with excellent high-temperature stability can be obtained by adopting the method. The curve overlap ratio of the Al-Sc alloy for ten times is very high in the temperature range of 80-200 ℃, the stability under thermal cycle is better, and the thermal expansion coefficient is about 25. In addition, after curve fitting for cycles 1,5, and 10, the CTE curves substantially coincide. However, the commercial 5183 welding wire fluctuates in ten cycles, wherein the regularity fluctuates greatly at 100200-200 ℃, as shown in fig. 2; in addition, the strength of the novel aluminum alloy wire prepared by the method is higher than that of the traditional commercial aluminum alloy wire, and the tensile strength of the novel aluminum alloy wire is improved by 50-80MPa compared with that of the commercial 5183 aluminum alloy wire.
In the invention, the novel aluminum alloy wire with excellent performance is prepared by combining the two methods of novel alloy element design and pre-ageing treatment, the preparation process flow is simple, and the preparation cost is not obviously increased compared with the traditional aluminum alloy wire.
Compared with the prior art, the strength and the high-temperature stability of the novel aluminum alloy wire are better than those of the existing aluminum alloy wire in the aspect of performance; in the aspect of preparation cost, as the alloy elements are added in a trace manner, complex process methods and flows are not involved, and the preparation cost is low; therefore, the novel aluminum alloy wire has potential for commercial production.
The foregoing description is only illustrative of the present invention and is not intended to limit the scope of the invention, and all equivalent structures or equivalent processes or direct or indirect application in other related arts are included in the scope of the present invention.
Claims (9)
1. An aluminum alloy wire with high thermal stability comprises a base material of a pure aluminum material, and is characterized in that Sc, si, ti, mn, zr elements are added in the base material of the pure aluminum material to form an Al-Si-Ti-Mn-Zr-Sc alloy material, and the balance is an impurity element material, wherein the Sc element material accounts for 0.05% -0.15% of the total mass of the Al-Si-Ti-Mn-Zr-Sc alloy material, the Si element material accounts for 0.3% -0.5% of the total mass of the Al-Si-Ti-Mn-Zr-Sc alloy material, the Ti element material accounts for 0.5% -1.0% of the total mass of the Al-Si-Ti-Mn-Zr-Sc alloy material, the Mn element material accounts for 0.05% -0.1% of the total mass of the Al-Si-Ti-Mn-Zr-Sc alloy material, and the impurity element material accounts for less than 0.03% of the total mass of the Al-Si-Ti-Mn-Zr-Sc alloy material.
2. A method for producing an aluminum alloy wire having high heat stability as defined in claim 1, comprising the steps of:
(1) Preparing raw materials according to the components of the alloy materials and the mass content of the components, and carrying out surface dirt removal and oxidation skin treatment on the raw materials;
(2) Preheating and drying the raw materials in a resistance furnace to evaporate the surface moisture of the raw materials;
(3) Adding preheated pure aluminum into a crucible, after the pure aluminum is completely melted, sequentially adding Sc, si, ti, mn, zr element materials for smelting, wherein the smelting temperature is 710-750 ℃, then pouring alloy materials to obtain an aluminum alloy casting, and then standing and preserving heat;
(4) Homogenizing the aluminum alloy casting, and quenching with warm water after the homogenization;
(5) And carrying out pre-ageing treatment and extrusion treatment on the aluminum alloy casting subjected to the homogenization treatment to obtain the aluminum alloy wire.
3. The method of producing an aluminum alloy wire having high heat stability according to claim 2, wherein the preheating in step (2) is performed at a temperature ranging from 200 ℃ to 300 ℃ for a preheating time ranging from 0.5 to 2 hours.
4. The method for producing an aluminum alloy wire with high heat stability according to claim 2, wherein the temperature of the melting furnace is set to 730 ℃ in the melting in the step (3), and when the temperature of the melting furnace is raised to 730 ℃ which is a predetermined temperature, the preheated pure aluminum ingot is placed into a crucible of the melting furnace, and after the pure aluminum ingot is placed in the crucible for melting, the preheated pure titanium, the Al-30Mn intermediate alloy, the Al-20Si alloy, the Al-20Ca intermediate alloy and the Al-20Zr intermediate alloy are respectively added into the crucible of the melting furnace; then raising the smelting temperature to 750 ℃ and preserving heat for 10 minutes; finally adding Mg-30Sc intermediate alloy preheated to 200 ℃, preserving heat for 5 minutes, and stirring for 5 minutes; next, starting refining treatment, adding a refining agent into the molten liquid in the crucible, continuously stirring the molten liquid by using a stainless steel screw stirrer in the adding process, wherein the stirring speed of the stirrer is 30r/min, the stirring time is 5-10min, and keeping the temperature and standing for 10-15 min after the refining agent is added; introducing argon for 10-15 minutes after standing is finished, and carrying out degassing treatment; after the degassing is finished, carrying out surface skimming, and removing surface scum by using a stainless steel spoon; finally, the furnace temperature is reduced by 730 ℃, and the furnace is kept stand for 10 to 15 minutes; pouring the aluminum alloy melt after standing into a cylindrical mold preheated to 250 ℃ to prepare a rod-shaped as-cast aluminum alloy cast ingot.
5. The method for producing an aluminum alloy wire with high heat stability according to claim 2, wherein the homogenization treatment in the step (4) comprises heating the obtained rod-like as-cast aluminum alloy ingot to 400-480 ℃ with a furnace, preserving the temperature for 12-15 hours for homogenization treatment, and immediately placing the rod-like as-cast aluminum alloy ingot into warm water at 60-80 ℃ for quenching treatment at the end.
6. The method for producing an aluminum alloy wire with high heat stability according to claim 5, wherein the pre-aging treatment in step (5) comprises performing heat preservation treatment at 150-300 ℃ in a resistance furnace, taking out a rod-shaped as-cast aluminum alloy ingot blank every 1-2 hours, performing water cooling, and performing hardness test until the hardness reaches the highest value, wherein the blank with the highest hardness is a peak aging blank, and the blank is in an overaging state after the hardness value is reduced. In order to ensure that the blank is in an overaging state, an ingot casting 80-100 hours after peak aging is used as a pre-aging treatment time, namely the pre-aging treatment time is 100-120 hours.
7. The method of manufacturing an aluminum alloy wire with high heat stability according to claim 2, wherein the pre-aging treatment in step (5) comprises aging the homogenized body at 200 ℃, taking out the body every 2 hours and performing hardness test until the hardness starts to decrease after the peak value occurs, and selecting the body 100 hours after the peak aging time as an overaged body for subsequent extrusion deformation.
8. The method of manufacturing an aluminum alloy wire with high thermal stability according to claim 2, wherein the extrusion treatment in step (5) comprises the preparation before extrusion, i.e., coating graphite powder on the inside and the surface of the extrusion die cavity, heating the extrusion die to 380 ℃ in a resistance furnace along with the furnace, polishing and removing oxidized skin on the surface of the rod-shaped as-cast aluminum alloy ingot before extrusion starts, heating the rod-shaped as-cast aluminum alloy ingot to 380 ℃ in the resistance furnace, preserving heat for 30 minutes, installing the preheated extrusion die into an extruder, and raising the temperature of the extruder to the extrusion temperature.
9. The method of producing an aluminum alloy wire having high heat stability according to claim 2, wherein the extrusion treatment in step (5) comprises extrusion molding of a preheated rod-like as-cast aluminum alloy ingot in an extruder at a temperature of 380 ℃ and at a speed of 0.5 to 1mm/s, and air-cooling the aluminum alloy wire to room temperature after completion of extrusion.
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