CN117305668A - Al-Mg-Si-Sn-RE rare earth aluminum alloy, preparation method thereof and heat-resistant cable - Google Patents
Al-Mg-Si-Sn-RE rare earth aluminum alloy, preparation method thereof and heat-resistant cable Download PDFInfo
- Publication number
- CN117305668A CN117305668A CN202311540220.9A CN202311540220A CN117305668A CN 117305668 A CN117305668 A CN 117305668A CN 202311540220 A CN202311540220 A CN 202311540220A CN 117305668 A CN117305668 A CN 117305668A
- Authority
- CN
- China
- Prior art keywords
- mass
- aluminum alloy
- rare earth
- mass ratio
- earth aluminum
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Pending
Links
- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 340
- 229910052761 rare earth metal Inorganic materials 0.000 title claims abstract description 111
- 150000002910 rare earth metals Chemical class 0.000 title claims abstract description 110
- 238000002360 preparation method Methods 0.000 title abstract description 7
- 229910052782 aluminium Inorganic materials 0.000 claims description 96
- 230000032683 aging Effects 0.000 claims description 79
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 73
- 229910045601 alloy Inorganic materials 0.000 claims description 34
- 239000000956 alloy Substances 0.000 claims description 34
- 229910052749 magnesium Inorganic materials 0.000 claims description 29
- 229910052742 iron Inorganic materials 0.000 claims description 24
- 239000007788 liquid Substances 0.000 claims description 21
- 229910052796 boron Inorganic materials 0.000 claims description 18
- 229910052712 strontium Inorganic materials 0.000 claims description 15
- 229910052691 Erbium Inorganic materials 0.000 claims description 14
- 229910052746 lanthanum Inorganic materials 0.000 claims description 14
- 229910052802 copper Inorganic materials 0.000 claims description 12
- 238000010438 heat treatment Methods 0.000 claims description 12
- 238000007670 refining Methods 0.000 claims description 12
- 229910052684 Cerium Inorganic materials 0.000 claims description 11
- 229910052688 Gadolinium Inorganic materials 0.000 claims description 10
- 229910052732 germanium Inorganic materials 0.000 claims description 10
- 229910052727 yttrium Inorganic materials 0.000 claims description 10
- 238000005096 rolling process Methods 0.000 claims description 9
- 238000009749 continuous casting Methods 0.000 claims description 8
- 229910052777 Praseodymium Inorganic materials 0.000 claims description 7
- 229910052790 beryllium Inorganic materials 0.000 claims description 7
- 239000002893 slag Substances 0.000 claims description 6
- 238000004519 manufacturing process Methods 0.000 claims description 5
- 238000010791 quenching Methods 0.000 claims description 5
- 230000000171 quenching effect Effects 0.000 claims description 5
- 238000001514 detection method Methods 0.000 claims description 4
- 229910052718 tin Inorganic materials 0.000 claims description 4
- 229910052725 zinc Inorganic materials 0.000 claims description 4
- 229910052797 bismuth 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
- 229910052709 silver Inorganic materials 0.000 claims description 2
- 230000000694 effects Effects 0.000 description 77
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 66
- 239000011159 matrix material Substances 0.000 description 49
- 239000010949 copper Substances 0.000 description 45
- 230000002411 adverse Effects 0.000 description 31
- 238000001556 precipitation Methods 0.000 description 25
- 239000006104 solid solution Substances 0.000 description 18
- 239000012535 impurity Substances 0.000 description 13
- 239000007787 solid Substances 0.000 description 13
- 229910019018 Mg 2 Si Inorganic materials 0.000 description 12
- 238000000034 method Methods 0.000 description 11
- 230000009471 action Effects 0.000 description 10
- 230000008569 process Effects 0.000 description 10
- 238000005728 strengthening Methods 0.000 description 10
- 230000000052 comparative effect Effects 0.000 description 9
- 229910052710 silicon Inorganic materials 0.000 description 9
- 230000035882 stress Effects 0.000 description 9
- 239000010410 layer Substances 0.000 description 7
- 239000000203 mixture Substances 0.000 description 7
- 239000002994 raw material Substances 0.000 description 7
- 229910019021 Mg 2 Sn Inorganic materials 0.000 description 6
- 229910018565 CuAl Inorganic materials 0.000 description 5
- 239000000126 substance Substances 0.000 description 5
- 238000012360 testing method Methods 0.000 description 5
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 4
- 239000002253 acid Substances 0.000 description 4
- 230000008859 change Effects 0.000 description 4
- 238000010622 cold drawing Methods 0.000 description 4
- 230000007547 defect Effects 0.000 description 4
- 230000003993 interaction Effects 0.000 description 4
- 230000006911 nucleation Effects 0.000 description 4
- 238000010899 nucleation Methods 0.000 description 4
- 150000003839 salts Chemical class 0.000 description 4
- 238000003723 Smelting Methods 0.000 description 3
- 230000015572 biosynthetic process Effects 0.000 description 3
- 150000001875 compounds Chemical class 0.000 description 3
- 239000013078 crystal Substances 0.000 description 3
- 238000007872 degassing Methods 0.000 description 3
- 238000011161 development Methods 0.000 description 3
- 230000018109 developmental process Effects 0.000 description 3
- 230000006872 improvement Effects 0.000 description 3
- 238000011056 performance test Methods 0.000 description 3
- -1 rare earth compound Chemical class 0.000 description 3
- 230000009466 transformation Effects 0.000 description 3
- 230000007704 transition Effects 0.000 description 3
- 229910017073 AlLi Inorganic materials 0.000 description 2
- VTYYLEPIZMXCLO-UHFFFAOYSA-L Calcium carbonate Chemical compound [Ca+2].[O-]C([O-])=O VTYYLEPIZMXCLO-UHFFFAOYSA-L 0.000 description 2
- 229910002535 CuZn Inorganic materials 0.000 description 2
- FPIPGXGPPPQFEQ-OVSJKPMPSA-N all-trans-retinol Chemical compound OC\C=C(/C)\C=C\C=C(/C)\C=C\C1=C(C)CCCC1(C)C FPIPGXGPPPQFEQ-OVSJKPMPSA-N 0.000 description 2
- 229910052799 carbon Inorganic materials 0.000 description 2
- 239000003795 chemical substances by application Substances 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 2
- 238000005260 corrosion Methods 0.000 description 2
- 239000006185 dispersion Substances 0.000 description 2
- KWGKDLIKAYFUFQ-UHFFFAOYSA-M lithium chloride Chemical compound [Li+].[Cl-] KWGKDLIKAYFUFQ-UHFFFAOYSA-M 0.000 description 2
- 239000000463 material Substances 0.000 description 2
- 239000003607 modifier Substances 0.000 description 2
- AHLBNYSZXLDEJQ-FWEHEUNISA-N orlistat Chemical compound CCCCCCCCCCC[C@H](OC(=O)[C@H](CC(C)C)NC=O)C[C@@H]1OC(=O)[C@H]1CCCCCC AHLBNYSZXLDEJQ-FWEHEUNISA-N 0.000 description 2
- ZZIZZTHXZRDOFM-XFULWGLBSA-N tamsulosin hydrochloride Chemical compound [H+].[Cl-].CCOC1=CC=CC=C1OCCN[C@H](C)CC1=CC=C(OC)C(S(N)(=O)=O)=C1 ZZIZZTHXZRDOFM-XFULWGLBSA-N 0.000 description 2
- 230000008646 thermal stress Effects 0.000 description 2
- 229910052723 transition metal Inorganic materials 0.000 description 2
- 150000003624 transition metals Chemical class 0.000 description 2
- 229910018084 Al-Fe Inorganic materials 0.000 description 1
- 229910017141 AlTa Inorganic materials 0.000 description 1
- 229910018192 Al—Fe Inorganic materials 0.000 description 1
- 229910018464 Al—Mg—Si Inorganic materials 0.000 description 1
- 229910004261 CaF 2 Inorganic materials 0.000 description 1
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 1
- VEXZGXHMUGYJMC-UHFFFAOYSA-M Chloride anion Chemical compound [Cl-] VEXZGXHMUGYJMC-UHFFFAOYSA-M 0.000 description 1
- KRHYYFGTRYWZRS-UHFFFAOYSA-M Fluoride anion Chemical compound [F-] KRHYYFGTRYWZRS-UHFFFAOYSA-M 0.000 description 1
- 229910017706 MgZn Inorganic materials 0.000 description 1
- GRYLNZFGIOXLOG-UHFFFAOYSA-N Nitric acid Chemical class O[N+]([O-])=O GRYLNZFGIOXLOG-UHFFFAOYSA-N 0.000 description 1
- 108091006629 SLC13A2 Proteins 0.000 description 1
- 241000276425 Xiphophorus maculatus Species 0.000 description 1
- 239000011717 all-trans-retinol Substances 0.000 description 1
- 235000019169 all-trans-retinol Nutrition 0.000 description 1
- 238000000137 annealing Methods 0.000 description 1
- 229910052787 antimony Inorganic materials 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 238000005885 boration reaction Methods 0.000 description 1
- 229910000019 calcium carbonate Inorganic materials 0.000 description 1
- 238000005266 casting Methods 0.000 description 1
- 150000001805 chlorine compounds Chemical class 0.000 description 1
- 238000013329 compounding Methods 0.000 description 1
- 239000004020 conductor Substances 0.000 description 1
- 238000001816 cooling Methods 0.000 description 1
- 229910001610 cryolite Inorganic materials 0.000 description 1
- 230000003247 decreasing effect Effects 0.000 description 1
- FPAFDBFIGPHWGO-UHFFFAOYSA-N dioxosilane;oxomagnesium;hydrate Chemical compound O.[Mg]=O.[Mg]=O.[Mg]=O.O=[Si]=O.O=[Si]=O.O=[Si]=O.O=[Si]=O FPAFDBFIGPHWGO-UHFFFAOYSA-N 0.000 description 1
- 238000001035 drying Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 230000005496 eutectics Effects 0.000 description 1
- 150000004673 fluoride salts Chemical class 0.000 description 1
- 229910000765 intermetallic Inorganic materials 0.000 description 1
- 239000000155 melt Substances 0.000 description 1
- 229910052751 metal Inorganic materials 0.000 description 1
- 239000002184 metal Substances 0.000 description 1
- 150000002736 metal compounds Chemical class 0.000 description 1
- VYQNWZOUAUKGHI-UHFFFAOYSA-N monobenzone Chemical compound C1=CC(O)=CC=C1OCC1=CC=CC=C1 VYQNWZOUAUKGHI-UHFFFAOYSA-N 0.000 description 1
- 229910017604 nitric acid Inorganic materials 0.000 description 1
- 238000004321 preservation Methods 0.000 description 1
- 239000011241 protective layer Substances 0.000 description 1
- 238000001953 recrystallisation Methods 0.000 description 1
- 238000011160 research Methods 0.000 description 1
- 238000007711 solidification Methods 0.000 description 1
- 230000008023 solidification Effects 0.000 description 1
- 239000000243 solution Substances 0.000 description 1
- 238000003756 stirring Methods 0.000 description 1
- 238000005482 strain hardening Methods 0.000 description 1
- 229910052714 tellurium Inorganic materials 0.000 description 1
- 238000009864 tensile test Methods 0.000 description 1
- 239000011573 trace mineral Substances 0.000 description 1
- 235000013619 trace mineral Nutrition 0.000 description 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 description 1
- 238000005491 wire drawing Methods 0.000 description 1
- 229910000859 α-Fe Inorganic materials 0.000 description 1
Classifications
-
- 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
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/0075—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for rods of limited length
-
- 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
- C22C21/00—Alloys based on aluminium
- C22C21/02—Alloys based on aluminium with silicon as the next major constituent
- C22C21/04—Modified aluminium-silicon alloys
-
- 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
- C22C21/10—Alloys based on aluminium with zinc 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
- C22C21/12—Alloys based on aluminium with copper as the next major constituent
- C22C21/18—Alloys based on aluminium with copper as the next major constituent with zinc
-
- 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
- C22F1/002—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working by rapid cooling or quenching; cooling agents used therefor
-
- 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
-
- 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
- C22F1/05—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 of the Al-Si-Mg type, i.e. containing silicon and magnesium in approximately equal proportions
-
- 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
- C22F1/053—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 zinc 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
- C22F1/057—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 copper as the next major constituent
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01B—CABLES; CONDUCTORS; INSULATORS; SELECTION OF MATERIALS FOR THEIR CONDUCTIVE, INSULATING OR DIELECTRIC PROPERTIES
- H01B1/00—Conductors or conductive bodies characterised by the conductive materials; Selection of materials as conductors
- H01B1/02—Conductors or conductive bodies characterised by the conductive materials; Selection of materials as conductors mainly consisting of metals or alloys
- H01B1/023—Alloys based on aluminium
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01B—CABLES; CONDUCTORS; INSULATORS; SELECTION OF MATERIALS FOR THEIR CONDUCTIVE, INSULATING OR DIELECTRIC PROPERTIES
- H01B1/00—Conductors or conductive bodies characterised by the conductive materials; Selection of materials as conductors
- H01B1/02—Conductors or conductive bodies characterised by the conductive materials; Selection of materials as conductors mainly consisting of metals or alloys
- H01B1/026—Alloys based on copper
-
- H—ELECTRICITY
- H01—ELECTRIC ELEMENTS
- H01B—CABLES; CONDUCTORS; INSULATORS; SELECTION OF MATERIALS FOR THEIR CONDUCTIVE, INSULATING OR DIELECTRIC PROPERTIES
- H01B7/00—Insulated conductors or cables characterised by their form
- H01B7/0009—Details relating to the conductive cores
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Conductive Materials (AREA)
Abstract
The Al-Mg-Si-Sn-RE rare earth aluminum alloy provided by the invention contains 0.1-1.3% by mass of Mg, 0.01-0.2% by mass of Cu, 0.1-0.7% by mass of Si, 0.01-0.3% by mass of Sn, 0.001-0.2% by mass of RE, 0-0.2% by mass of Zn, 0-0.15% by mass of B, 0-0.3% by mass of Nb and 0-0.3% by mass of Ge. The invention also provides a preparation method of the Al-Mg-Si-Sn-RE rare earth aluminum alloy and a heat-resistant cable.
Description
Technical Field
The invention relates to the technical field of aluminum alloy, in particular to an Al-Mg-Si-Sn-RE rare earth aluminum alloy, a preparation method of the Al-Mg-Si-Sn-RE rare earth aluminum alloy and a heat-resistant cable using the Al-Mg-Si-Sn-RE rare earth aluminum alloy.
Background
Aluminum alloys are the most widely used class of nonferrous metal structural materials in industry, and find wide application in the aerospace, automotive, mechanical manufacturing, marine and chemical industries. With the rapid development of science, technology and industrial economy, the demand for aluminum alloys is increasing, and the research of aluminum alloys is also in depth. The wide application of the aluminum alloy promotes the development of the aluminum alloy in the power industry, and simultaneously, the development of the power industry expands the application field of the aluminum alloy.
Cables are the resources used to transport and distribute electrical energy. The core is the conductive portion of the cable that is used to carry electrical energy. Copper has good conductivity and is widely used for the core of a cable. However, with the increasing shortage of copper resources, aluminum is becoming very abundant, and the replacement of copper with aluminum has received attention from researchers.
Aluminum alloy cables are becoming a trend to replace copper cables and are widely used. The aluminum alloy conductor material in the prior art is widely applied, and the Al-Mg-Si aluminum alloy has better tensile strength than the Al-Fe alloy, but has poor elongation, conductivity and heat resistance. Therefore, there is an urgent need for an al—mg—si-based aluminum alloy for cables, which is excellent in combination properties, particularly in electric conductivity, elongation, mechanical properties and heat resistance.
Disclosure of Invention
Aiming at the defects in the prior art, the invention provides an Al-Mg-Si-Sn-RE rare earth aluminum alloy, and aims to provide an Al-Mg-Si-Sn-RE rare earth aluminum alloy for a heat-resistant cable, which has excellent comprehensive properties, particularly mechanical properties, electric conductivity and heat resistance.
The invention provides an Al-Mg-Si-Sn-RE rare earth aluminum alloy, which contains Al, 0.1-1.3% of Mg, 0.01-0.2% of Cu, 0.1-0.7% of Si, 0.01-0.3% of Sn, 0.001-0.2% of RE, 0-0.2% of Zn, 0-0.15% of B, 0-0.3% of Nb and 0-0.3% of Ge.
Further, at least one of the following conditions is satisfied:
the mass ratio of Mg, si and Cu is 1-100:1-60:1, a step of;
the mass ratio of Mg, si and Zn is 1-100:1-40:1, a step of;
the mass ratio of Mg, si and Sn is 1-500:1-300:1, a step of;
the mass ratio of Si to Ge is 1-100:1, a step of;
the mass ratio of Si to Nb is 1-150:1.
further, RE is at least one of La, ce, pr, nd, er, sm, Y and Gd, wherein,
when RE is Ce, sm and Er, the mass ratio of Ce, sm and Er is 1-2:0.5-1.5:1, a step of;
when RE is La, Y and Er, the mass ratio of La, Y and Er is 0.5-3:0.5-2:1, a step of;
when RE is Pr, nd and Gd, the mass ratio of Pr, nd and Gd is 1-2:0.1-2.5:1, a step of;
when RE is La and Ce, the mass ratio of La to Ce is 0.5-2:1.
further, the Al-Mg-Si-Sn-RE rare earth aluminum alloy contains 0.2 to 1% by mass of Mg, 0.05 to 0.1% by mass of Cu, 0.2 to 0.5% by mass of Si, 0.01 to 0.1% by mass of Sn, 0.01 to 0.1% by mass of RE, 0.001 to 0.1% by mass of Zn, 0.01 to 0.08% by mass of B, 0.001 to 0.2% by mass of Nb, and 0.001 to 0.1% by mass of Ge.
Further, at least one of the following conditions is satisfied:
the Al-Mg-Si-Sn-RE rare earth aluminum alloy also contains Bi with the mass percent content of 0-0.3 percent;
the Al-Mg-Si-Sn-RE rare earth aluminum alloy also contains 0-0.2% of Sr by mass percent;
the Al-Mg-Si-Sn-RE rare earth aluminum alloy also contains 0-0.2% of Mo by mass percent;
the Al-Mg-Si-Sn-RE rare earth aluminum alloy also contains Be with the mass percent content of 0-0.15 percent;
the Al-Mg-Si-Sn-RE rare earth aluminum alloy also contains 0-0.2 mass percent of Ag;
the Al-Mg-Si-Sn-RE rare earth aluminum alloy also contains Co with the mass percentage content of 0-0.3 percent;
the Al-Mg-Si-Sn-RE rare earth aluminum alloy also contains In with the mass percentage content of 0-0.2 percent;
the Al-Mg-Si-Sn-RE rare earth aluminum alloy also contains Te with the mass percentage content of 0-0.2 percent;
the Al-Mg-Si-Sn-RE rare earth aluminum alloy also contains 0-0.3% of Fe by mass percent.
Further, at least one of the following conditions is satisfied:
when the Al-Mg-Si-Sn-RE rare earth aluminum alloy contains Bi, the mass ratio of Mg to Bi is 1-500:1, the mass ratio of Cu to Bi is 1-40:1, a step of;
when the Al-Mg-Si-Sn-RE rare earth aluminum alloy contains Sr, co, be and Fe, the mass ratio of Fe, cu and Sr is 0.5-20:0.2-10:1, si, fe and Sr with the mass ratio of 1-200:0.5-10:1, the mass ratio of Fe, RE and Sr is 0.5-15:0.5-10:1, the mass ratio of Fe, co and Sr is 0.5-10:0.5-10:1, the mass ratio of Be, co and Fe is 0.5-20:0.5-10:1, RE, B and Be in a mass ratio of 0.5-20:0.1-10:1, the mass ratio of Fe, RE and B is 1-15:0.1-10:1, a step of;
When the Al-Mg-Si-Sn-RE rare earth aluminum alloy contains Mo, the mass ratio of Si to Mo is 1-100:1, a step of;
when the Al-Mg-Si-Sn-RE rare earth aluminum alloy contains Te, the mass ratio of Te to Sn is 0.01-10:1, the mass ratio of Te to Si is 0.001-1:1, a step of;
when the Al-Mg-Si-Sn-RE rare earth aluminum alloy contains Ag, the mass ratio of Mg to Ag is 2-500:1, the mass ratio of Cu to Ag is 1-80:1, a step of;
when the Al-Mg-Si-Sn-RE rare earth aluminum alloy contains In, the mass ratio of Mg to In is 2-600:1, the mass ratio of Cu to In is 0.2-80:1, the mass ratio of in to B is 0.1-15:1.
further, the Al-Mg-Si-Sn-RE rare earth aluminum alloy contains 0.2 to 1% by mass of Mg, 0.05 to 0.1% by mass of Cu, 0.2 to 0.5% by mass of Si, 0.01 to 0.1% by mass of Sn, 0.01 to 0.1% by mass of RE, 0.001 to 0.1% by mass of Zn, 0.01 to 0.08% by mass of B, 0.001 to 0.2% by mass of Nb, 0.001 to 0.1% by mass of Ge, 0.001 to 0.2% by mass of Bi, 0.001 to 0.1% by mass of Sr, 0.001 to 0.1% by mass of Mo, 0.001 to 0.08% by mass of Be, 0.001 to 0.1% by mass of Ag, 0.001 to 0.2% by mass of In, 0.001 to 0.1% by mass of Te, 0.001 to 0.1% by mass of 0.001.
The invention also provides a preparation method of the Al-Mg-Si-Sn-RE rare earth aluminum alloy, which comprises the following steps:
carrying out primary heating treatment on an aluminum source to obtain aluminum liquid;
adding Mg, cu, si, sn, RE, zn, B, nb and Ge into the aluminum liquid, and performing a second heating treatment to obtain an alloy liquid;
refining and slag skimming are carried out on the alloy liquid, and component and content detection is carried out;
after the components and the content are detected to be qualified, carrying out continuous casting and rolling treatment and quenching treatment on the alloy liquid subjected to the refining treatment and the slag skimming treatment to obtain an aluminum alloy rod;
drawing the quenched aluminum alloy rod to obtain an aluminum alloy wire with the diameter smaller than 5 mm;
and aging the aluminum alloy wire to obtain an Al-Mg-Si-Sn-RE rare earth aluminum alloy, wherein the Al-Mg-Si-Sn-RE rare earth aluminum alloy contains Al, 0.1-1.3% of Mg, 0.01-0.2% of Cu, 0.1-0.7% of Si, 0.01-0.3% of Sn, 0.001-0.2% of RE, 0-0.2% of Zn, 0-0.15% of B, 0-0.3% of Nb and 0-0.3% of Ge.
Further, the preparation method of the Al-Mg-Si-Sn-RE rare earth aluminum alloy further comprises the step of adding at least one of Bi, sr, mo, be, ag, co, in, te and Fe into the aluminum liquid.
Further, the aging treatment is a discontinuous aging process, which comprises the following steps: performing primary low-temperature aging treatment at 100-150deg.C for 1-50h; performing secondary natural aging treatment at 20-60deg.C for 10-24 hr; performing three-stage high-temperature aging treatment at 160-350deg.C for 0.1-150 hr; or (b)
The aging treatment is a discontinuous aging process, and the discontinuous aging process comprises the following steps: performing primary low-temperature aging treatment at 100-150deg.C for 1-50h; performing secondary natural aging treatment at 20-60deg.C for 10-24 hr; performing three-stage high-temperature aging treatment at 160-250deg.C for 0.1-100h; four-stage high-temperature aging treatment is carried out at 250-350 ℃ for 0.1-50h.
The invention also provides a heat-resistant cable which comprises a wire core and an insulating layer coating the wire core, wherein the wire core is made of the Al-Mg-Si-Sn-RE rare earth aluminum alloy.
In the technical scheme of the invention, the Al-Mg-Si-Sn-RE aluminum alloy contains 0.1-1.3% by mass of Mg, 0.01-0.2% by mass of Cu, 0.1-0.7% by mass of Si, 0.01-0.3% by mass of Sn, 0.001-0.2% by mass of RE, 0-0.2% by mass of Zn, 0-0.15% by mass of B, 0-0.3% by mass of Nb and 0-0.3% by mass of Ge. When the elements are independently added into an aluminum matrix, the improvement of the electric conductivity and the mechanical property of aluminum is limited, and even the electric conductivity and the mechanical property of aluminum are negatively affected. And when the elements are added independently and the content is small, the performance of the aluminum alloy is difficult to be effectively improved; the addition of these elements alone and in relatively high amounts may have a negative effect on certain properties of the aluminum alloy. The invention adds the elements with the content into the aluminum matrix together, the interaction of the elements is mutually influenced, the solid solubility of the elements in the aluminum matrix can be reduced, the volume fraction of the precipitated phase is increased, the adverse effect of certain elements on the conductivity is reduced, the comprehensive performance is improved, and the comprehensive performance of the aluminum alloy can be greatly improved even if the content of one or more elements is lower or higher. Specifically, the content of at least one of the above elements is set to be larger than that in the prior art, and the elements can interact mutually to promote the desolventizing and precipitation of the elements so as to reduce the solid solubility of the elements in the aluminum matrix and promote the volume fraction of the precipitated phase, thereby improving the comprehensive performance of the aluminum alloy, and coarser second phase and the precipitated phase (such as Al 3 RE、Al 3 Fe、Mg 2 Si、Mg 2 Equal Sn) are refined in the matrix and the grain boundary or the grain boundary under the combined action of large deformation stress and special heat treatment process, thereby reducing the content of the elementsAdverse effect on aluminum alloy properties at high, mg 2 Si、Mg 2 The precipitation kinetics of various precipitation phases such as Sn can be mutually influenced, so that the size of the precipitation phases is not easy to grow, the volume fraction of the precipitation phases is improved, in addition, alloy elements can be mutually dissolved into proper second phases, and the comprehensive performance of the aluminum alloy can be improved, so that the content of at least one element in the elements is set to be larger than that in the prior art, on one hand, the elements are utilized to improve the performance of the aluminum alloy, and the elements, particularly the elements with higher content, can be reacted with other elements to generate the second phases as much as possible, so that adverse effects on the performance of the aluminum alloy caused by excessive solid solution of the elements, particularly the elements with higher content, are avoided, and the source range of raw materials is enlarged. Moreover, the effects of at least part of the elements are overlapped, for example, the elements can basically improve the mechanical property of the aluminum alloy, some elements can improve the electric conductivity, elongation and heat resistance of the aluminum alloy, even if the content of one or more of the elements is low, the effect of effectively improving the aluminum alloy performance is not required to be worried about when the content of one or more of the elements is low, and a plurality of elements with the same effect are added simultaneously, so that the use amount of the alloy elements can be greatly reduced, the effect is improved, namely, a small amount of a plurality of elements are used for replacing a large amount of single elements, and the mechanical property and the electric conductivity are greatly improved. In addition, the addition amount of the element which is low in cost can be set larger without worrying about the adverse effect of excessive addition on the performance of the aluminum alloy, for example, the addition amount of Si, cu, sn, zn can be set larger without worrying about the adverse effect of a large amount of Si, cu, sn, zn on the performance of the aluminum alloy. The aluminum alloy can adopt Cu, sn, zn and the like with higher content range, so that the invention can adopt common aluminum ingots or regenerated aluminum with low price as raw materials, and the cost is further reduced. In summary, mg, cu, si, sn, RE, zn, B, nb and Ge are added into an aluminum matrix together, and the elements interact as a whole to influence each other, so that the comprehensive performance of the aluminum alloy can be greatly improved even if the content of one or more elements is low or high. Specifically, the Al-Mg-Si-Sn-RE rare earth aluminum alloy has tensile strength The tensile strength of the medium strength aluminum alloy with the brand of LHA4 in the row mark is larger (the tensile strength of the medium strength aluminum alloy with the LHA4 is 255-290 MPa), the elongation and the electrical conductivity are larger than those of the medium strength aluminum alloy with the brand of LHA3 in the row mark (the elongation of the medium strength aluminum alloy with the LHA3 is larger than 3.5 percent and the electrical conductivity is 58.5 percent). Therefore, the Al-Mg-Si-Sn-RE rare earth aluminum alloy has better comprehensive performance, and can prevent the defects of increased cost, complex process, blind performance adjustment and the like caused by adding excessive impurity elements into an aluminum matrix.
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.
An embodiment of the present invention provides an Al-Mg-Si-Sn-RE rare earth aluminum alloy, which contains 0.1 to 1.3% by mass of Mg, 0.01 to 0.2% by mass of Cu, 0.1 to 0.7% by mass of Si, 0.01 to 0.3% by mass of Sn, 0.001 to 0.2% by mass of RE, 0 to 0.2% by mass of Zn, 0 to 0.15% by mass of B, 0 to 0.3% by mass of Nb, 0 to 0.3% by mass of Ge, al and unavoidable impurities.
In one embodiment, the Al-Mg-Si-Sn-RE rare earth aluminum alloy contains 0.2-1% by mass of Mg, 0.05-0.1% by mass of Cu, 0.2-0.5% by mass of Si, 0.01-0.1% by mass of Sn, 0.01-0.1% by mass of RE, 0.001-0.1% by mass of Zn, 0.01-0.08% by mass of B, 0.001-0.2% by mass of Nb, and 0.001-0.1% by mass of Ge.
The Al-Mg-Si-Sn-RE rare earth aluminum alloy can also contain 0-0.3% of Bi, 0-0.2% of Sr, 0-0.2% of Mo, 0-0.15% of Be, 0-0.2% of Ag, 0-0.3% of Co, 0-0.2% of In, 0-0.2% of Te and 0-0.3% of Fe.
In one embodiment, the Al-Mg-Si-Sn-RE rare earth aluminum alloy contains 0.2-1% by mass of Mg, 0.05-0.1% by mass of Cu, 0.2-0.5% by mass of Si, 0.01-0.1% by mass of Sn, 0.01-0.1% by mass of RE, 0.001-0.1% by mass of Zn, 0.01-0.08% by mass of B, 0.001-0.2% by mass of Nb, 0.001-0.1% by mass of Ge, 0.001-0.2% by mass of Bi, 0.001-0.1% by mass of Sr, 0.001-0.1% by mass of Mo, 0.001-0.08% by mass of Be, 0.001-0.1% by mass of Ag, 0.001-0.2% by mass of In, 0.001-0.1% by mass of Fe, 0.001-0.2% by mass of Te.
In one embodiment, the Mg may be 0.1%, 0.2%, 0.3%, 0.4%, 0.5%, 0.6%, 0.7%, 0.8%, 0.9%, 1%, 1.1%, 1.2%, or 1.3% by mass. When the mass percentage content of Mg is 0.1-1.3%, the mechanical property, the electric conductivity, the heat resistance and the fatigue resistance of the aluminum alloy can be improved; mg can react with Al, fe, si, cu, zn, sn, bi and the like to generate Mg 2 SiZn、Mg 2 Si、Mg 2 Zn、Mg 2 Sn、Mg 3 Bi 2 An equal second phase in which Mg is solid-dissolved in CuAl 2 Phase and AlFeSi phase, forming (CuMg) Al 2 The phase and AlFeSiMg phase, so that the content of Mg can be set to be larger than that of Mg (not larger than 1 percent) in the prior art, on the one hand, the performance of the aluminum alloy is improved by using the Mg, and on the other hand, the Mg is reacted with other elements as much as possible to generate the first elementThe two phases are used for avoiding the adverse effect on the performance of the aluminum alloy caused by excessive solid solution of Mg in the aluminum matrix; the effect of Mg is overlapped with the effect of other elements, and even if the content of Mg is low, the problem that the performance of the aluminum alloy is difficult to be effectively improved due to the addition of the small content is avoided.
In an embodiment, the Cu may be 0.01%, 0.02%, 0.03%, 0.04%, 0.05%, 0.06%, 0.07%, 0.08%, 0.09%, 0.1%, 0.11%, 0.12%, 0.13%, 0.14%, 0.15%, 0.16%, 0.17%, 0.18%, 0.19%, or 0.2% by mass. When the Cu content is 0.01-0.2% by mass, the mechanical property, heat resistance, elongation and fatigue resistance of the aluminum alloy can be improved; cu can react with Al, fe, si, RE, mg, in, zn to form CuAl 2 、CuIn、AlFeSiCu、Al 2 CuZn、(CuMg)Al 2 The second phase is equal, so that the content of Cu is set to be larger than the content of Cu (not larger than 0.1 percent) in the prior art, on one hand, the performance of the aluminum alloy is improved by utilizing Cu, and on the other hand, the Cu reacts with other elements as much as possible to generate the second phase so as to avoid the adverse effect on the performance of the aluminum alloy caused by excessive solid solution of Cu in an aluminum matrix; the effect of Cu is overlapped with that of other elements, and even if the content of Cu is low, the problem that the performance of the aluminum alloy is difficult to be effectively improved due to the addition of the small content is avoided. In addition, cu can promote Mg 2 The precipitation of Si and the like improves the volume fraction and the dispersion degree of the Si and the like so as to reduce the solid solubility of the elements in an aluminum matrix.
In one embodiment, the mass percentage of Si may be 0.1%, 0.11%, 0.12%, 0.13%, 0.14%, 0.15%, 0.2%, 0.25%, 0.3%, 035%, 0.4%, 0.45%, 0.5%, 0.55%, 0.6%, 0.65%, or 0.7%. When the mass percentage of Si is 0.1-0.7%, mg can be formed by solid solution and Mg element in the alloy 2 The Si phase can improve the mechanical property and the electric conductivity of the aluminum alloy; si can react with Al, fe, mg, cu, B, be to generate AlFeSi, alFeSiCu, alFeMgSi, alFeSiB, be-Fe (Al 8 Fe 2 SiBe) and the like, so that the Si content can be set to be larger than in the prior artSi content and ratio (Si content is generally less than 0.5%, mg is excessive) 2 The Si phase causes coarsening of the second phase, and the mechanical property and the electrical conductivity of the alloy are reduced; furthermore, mg: si=1.73, and Si is slightly remained, if Mg dissolved in the matrix remains, the conductivity of the alloy is greatly reduced, on the one hand, si is utilized to promote the performance of the aluminum alloy, and on the other hand, si reacts with other elements as much as possible to generate a second phase so as to avoid adverse effect on the performance of the aluminum alloy caused by excessive solid solution of Si in the aluminum matrix; the effect of Si is overlapped with the effect of other elements, and even if the content of Si is high, the aluminum alloy performance is not reduced by adding more Si; si can refine grains and further improve the mechanical property of the aluminum alloy.
In one embodiment, the mass percentage of RE may be specifically 0.001%, 0.005%, 0.01%, 0.02%, 0.03%, 0.04%, 0.05%, 0.06%, 0.07%, 0.08%, 0.09%, 0.1%, 0.11%, 0.12%, 0.13%, 0.14%, 0.15%, 0.16%, 0.17%, 0.18%, 0.19%, or 0.2%. When the mass percentage content of RE is 0.001-0.2%, the elongation, mechanical property, conductivity and heat resistance of the aluminum alloy can be improved; RE can refine alloy structure to improve mechanical property of aluminum alloy, RE can form rare earth active film on surface of iron-containing phase or combine with Al, fe, ti and other atoms to form rare earth compound, effectively reduce solid solution of harmful element in aluminum matrix to improve conductivity and mechanical property of aluminum alloy, RE can convert long-strip beta-Fe phase into spherical alpha-Fe phase and deteriorate simple substance Si, RE can promote disperse phase such as CuAl 2 、(CuMg)Al 2 Etc., further improving the conductivity and mechanical properties of the aluminum alloy, RE can refine the grains, the second phase and the precipitated phase (e.g., al can refine 3 RE、Al 3 Fe、Mg 2 Si、Mg 2 Sn phase), further improving the mechanical properties of the aluminum alloy.
In one embodiment, the mass percentage of Zn is 0.001%, 0.005%, 0.01%, 0.02%, 0.03%, 0.04%, 0.05%, 0.06%, 0.07%, 0.08%, 0.09%, 0.1%, 0.11%, 0.12%, 0.13%, 0.14%0.15%, 0.16%, 0.17%, 0.18%, 0.19%, or 0.2%. When the mass percentage content of Zn is not more than 0.2%, the elongation and mechanical property of the aluminum alloy can be improved; zn can react with Mg and the like to generate MgZn 2 The second phase is equal, so that the Zn content is set to be larger than the Zn content (not larger than 0.04 percent) in the prior art, on one hand, the performance of the aluminum alloy is improved by Zn, and on the other hand, the Zn reacts with other elements as much as possible to generate the second phase so as to avoid the adverse effect on the performance of the aluminum alloy caused by excessive solid solution of Zn in an aluminum matrix; the effect of Zn is overlapped with the effect of other elements, and even if the content of Zn is low, the problem that the performance of the aluminum alloy is difficult to be effectively improved due to the addition of the small content is avoided. In addition, zn can eliminate simple substance Si to reduce the influence of Si on the performance of the aluminum alloy and promote Mg 2 Si、Al 2 Precipitation of Cu and the like to form Mg 2 SiZn、Al 2 The CuZn phase reduces the solid solubility of the above elements in the aluminum matrix.
In one embodiment, the mass percentage of B may be specifically 0.001%, 0.005%, 0.01%, 0.02%, 0.03%, 0.04%, 0.05%, 0.06%, 0.07%, 0.08%, 0.09%, 0.1%, 0.11%, 0.12%, 0.13%, 0.14%, or 0.15%. When the mass percentage content of the B is not more than 0.15%, the elongation, the mechanical property and the electric conductivity of the aluminum alloy can be improved; b can react with Al, fe, si and the like to generate second phases such as AlFeSiB and the like, so that the content of B can be set to be larger than the content of B (not larger than 0.08%) in the prior art, on one hand, the performance of the aluminum alloy is improved by utilizing B, and on the other hand, the B is reacted with other elements as much as possible to generate the second phases so as to avoid the adverse effect on the performance of the aluminum alloy caused by excessive solid solution of B in an aluminum matrix; the effect of B is overlapped with the effect of other elements, and even if the content of B is low, the problem that the performance of the aluminum alloy is difficult to be effectively improved due to the addition of less content is avoided; b can be subjected to a boration reaction with transition metal impurities to reduce the adverse effect of the transition metal impurities on the performance (such as conductivity) of the aluminum alloy, eliminate simple substance Si to reduce the effect of Si on the performance of the aluminum alloy, and convert needle-shaped Fe phases into small-short-sheet-shaped, polyhedral-shaped or Chinese character-shaped Fe phases to reduce or eliminate the adverse effect of Fe on the performance (such as conductivity and elongation) of the aluminum alloy; and B, the grains can be refined, and the mechanical property of the aluminum alloy is further improved.
In one embodiment, the Sn may be 0.01%, 0.02%, 0.03%, 0.04%, 0.05%, 0.06%, 0.07%, 0.08%, 0.09%, 0.1%, 0.11%, 0.12%, 0.13%, 0.14%, 0.15%, 0.16%, 0.17%, 0.18%, 0.19%, 0.2%, 0.21%, 0.22%, 0.23%, 0.24%, 0.25%, 0.26%, 0.27%, 0.28%, 0.29%, or 0.3% by mass. When the mass percentage content of Sn is not more than 0.3%, the mechanical property, the electric conductivity and the corrosion resistance of the aluminum alloy can be improved; sn can react with Al, mg and the like to generate Al 9 Sn 7 、Al 6 Sn 5 、Al 5 Sn 2 、Al 3 Sn 4 、Mg 2 The second phase such as Sn, the content of Sn can be set to be larger than the content of Sn (not larger than 0.08%) in the prior art, on one hand, the performance of the aluminum alloy is improved by utilizing Sn, and on the other hand, the Sn reacts with other elements as much as possible to generate the second phase so as to avoid the adverse effect on the performance of the aluminum alloy caused by excessive solid solution of Sn in an aluminum matrix; the action of Sn is overlapped with the action of other elements, and even when the content of Sn is low, there is no concern that the addition of a small content is difficult to effectively improve the performance of the aluminum alloy. In addition, sn can promote Mg 2 The precipitation of the Si phase reduces the solid solubility of the above elements in the aluminum matrix.
In one embodiment, the Nb may be 0.001%, 0.005%, 0.01%, 0.02%, 0.03%, 0.04%, 0.05%, 0.06%, 0.07%, 0.08%, 0.09%, 0.1%, 0.11%, 0.12%, 0.13%, 0.14%, 0.15%, 0.16%, 0.17%, 0.18%, 0.19%, 0.2%, 0.25%, or 0.3% by mass. When the mass percentage content of Zr is not more than 0.3%, the high-temperature strength, toughness and high-temperature creep property of the aluminum alloy can be improved; nb can be used for refining grains and can form AlNb in a melt 3 、AlNb、Al 3 Nb and other high temperature reinforced metal compounds, part of Nb may be dispersed in matrix grain boundary to raise the performance of the alloyThe high-temperature strength, toughness, high-temperature creep property and the like of the aluminum alloy are improved; nb, ti and Al can also form TiAl-Nb phase, so that the high-temperature creep resistance of the aluminum alloy is further improved.
In an embodiment, the Ge may specifically be 0.001%, 0.005%, 0.01%, 0.02%, 0.03%, 0.04%, 0.05%, 0.06%, 0.07%, 0.08%, 0.09%, 0.1%, 0.11%, 0.12%, 0.13%, 0.14%, 0.15%, 0.16%, 0.17%, 0.18%, 0.19%, 0.2%, 0.21%, 0.22%, 0.23%, 0.24%, 0.25%, 0.26%, 0.27%, 0.28%, 0.29%, or 0.3% by mass. When the content of the Ge in percentage by mass is not more than 0.3%, the mechanical property, the electric conduction property and the heat resistance of the aluminum alloy can be improved; ge can react with Al, si and the like to generate Al 9 Ge 7 、Al 6 Ge 5 、Al 5 Ge 2 、Al 3 Ge 4 The content of Ge is set to be larger than the content of Ge (not larger than 0.1 percent) in the prior art, on one hand, the performance of the aluminum alloy is improved by using Ge, and on the other hand, ge is reacted with other elements as much as possible to generate a second phase so as to avoid adverse effects on the performance of the aluminum alloy caused by excessive solid solution of Ge in an aluminum matrix, and the conductivity and heat resistance of the aluminum alloy are further improved; the effect of Ge is overlapped with the effect of other elements, and even if the content of Ge is low, the problem that the performance of the aluminum alloy is difficult to effectively improve due to the addition of the small content is avoided. In addition, ge can promote Mg 2 Si、CuAl 2 Precipitation of the second phase is performed to reduce the solid solubility of the above elements in the aluminum matrix.
The mass ratio of Mg, si and Cu is 1-100:1-60:1, preferably 2-80:2-40:1, more preferably 5 to 50:5-20:1, again preferably 10-30:10-15:1. in the range of the mass ratio, the aluminum alloy has better conductive performance, and the conductive performance is gradually improved along with the increase of the mass ratio. Specifically, the mass ratio of Mg, si, and Cu is 1:1: 1. 1:10: 1. 1:20: 1. 1:30: 1. 1:40: 1. 1:50: 1. 1:60: 1. 10:1: 1. 10:10: 1. 10:20: 1. 10:30: 1. 10:40: 1. 10:50: 1. 10:60: 1. 50:1: 1. 50:10: 1. 50:20: 1. 50:30: 1. 50:40: 1. 50:50: 1. 50:60: 1. 100:1: 1. 100:10: 1. 100:20: 1. 100:30: 1. 100:40: 1. 100:50: 1. or 100:60:1.
The mass ratio of Mg, si and Zn is 1-100:1-40:1, preferably 2-80:2-30:1, more preferably 10 to 50:5-20:1. in the range of the mass ratio, the aluminum alloy has better conductive performance, and the conductive performance is gradually improved along with the increase of the mass ratio. Specifically, the mass ratio of Mg, si, and Zn is 1:1: 1. 1:10: 1. 1:20: 1. 1:30: 1. 1:40: 1. 10:1: 1. 10:10: 1. 10:20: 1. 10:30: 1. 10:40: 1. 50:1: 1. 50:10: 1. 50:20: 1. 50:30: 1. 50:40: 1. 100:1: 1. 100:10: 1. 100:20: 1. 100:30: 1. or 100:40:1.
the mass ratio of Mg, si and Sn is 1-500:1-300:1, preferably 5-400:5-200:1, more preferably 10 to 300:10-100:1, again preferably 200-300:60-100:1. in the range of the mass ratio, the aluminum alloy has better conductive performance, and the conductive performance is gradually improved along with the increase of the mass ratio. Specifically, the mass ratio of Mg, si, and Sn is 1:1: 1. 1:10: 1. 1:50: 1. 1:100: 1. 1:200: 1. 1:300: 1. 10:1: 1. 10:10: 1. 10:50: 1. 10:100: 1. 10:200: 1. 10:300: 1. 100:1: 1. 100:10: 1. 100:50: 1. 100:100: 1. 100:200: 1. 100:300: 1. 200:1: 1. 200:10: 1. 200:50: 1. 200:100: 1. 200:200: 1. 200:300: 1. 300:1: 1. 300:10: 1. 300:50: 1. 300:100: 1. 300:200: 1. 300:300: 1. 400:1: 1. 400:10: 1. 400:50: 1. 400:100: 1. 400:200: 1. 400:300: 1. 500:1: 1. 500:10: 1. 500:50: 1. 500:100: 1. 500:200: 1. or 500:300:1.
The mass ratio of Si to Ge is 1-100:1, preferably 5-80:1, more preferably 10 to 50:1, again preferably 15-25:1. in the range of the mass ratio, the aluminum alloy has better mechanical property, and the tensile property is gradually improved along with the increase of the mass ratio. Specifically, the mass ratio of Si to Ge is 1: 1. 5:1. 10: 1. 15: 1. 20: 1. 25:1. 30:1. 35: 1. 40: 1. 45: 1. 50:1. 55: 1. 60: 1. 65: 1. 70: 1. 75: 1. 80: 1. 85: 1. 90: 1. 95: 1. or 100:1.
the mass ratio of Si to Nb is 1-150:1, preferably 5-100:1, more preferably 10 to 80:1, again preferably 20-30:1. in the range of the mass ratio, the aluminum alloy has better mechanical property and heat resistance, and the mechanical property and the heat resistance are gradually improved along with the increase of the mass ratio. Specifically, the mass ratio of Si to Nb is 1: 1. 5:1. 10: 1. 15: 1. 20: 1. 25:1. 30:1. 35: 1. 40: 1. 45: 1. 50:1. 55: 1. 60: 1. 65: 1. 70: 1. 75: 1. 80: 1. 85: 1. 90: 1. 95: 1. 100:1. 110: 1. 120: 1. 130: 1. 140:1 or 150:1.
RE is at least one of La, ce, pr, nd, er, sm, Y and Gd.
When RE is Ce, sm and Er, the mass ratio of Ce, sm and Er is 1-2:0.5-1.5:1, preferably 1-2:1-1.5:1, specifically, may be 1:0.5: 1. 1:1: 1. 1:1.5: 1. 1.5:0.5: 1. 1.5:1: 1. 1.5:1.5: 1. 2:0.5: 1. 2:1: 1. or 2:1.5:1. at this time, the effect of improving the electrical conductivity of the aluminum alloy by the mixture of Ce, sm, and Er was improved by 1 IACS value as compared to when La was added alone.
When RE is La, Y and Er, the mass ratio of La, Y and Er is 0.5-3:0.5-2:1, preferably 1-2:1-2:1, specifically, may be 0.5:0.5: 1. 0.5:1: 1. 0.5:1.5: 1. 0.5:2: 1. 1:0.5: 1. 1:1: 1. 1:1.5: 1. 1:2: 1. 1.5:0.5: 1. 1.5:1: 1. 1.5:1.5: 1. 1.5:2: 1. 2:0.5: 1. 2:1: 1. 2:1.5:1. 2:2: 1. 2.5:0.5: 1. 2.5:1: 1. 2.5:1.5: 1. 2.5:2: 1. 3:0.5: 1. 3:1: 1. 3:1.5: 1. or 3:2:1. at this time, the effect of improving the electrical conductivity of the aluminum alloy by the mixture of La, Y, and Er was improved by 1.5 IACS values as compared to when La was added alone.
When RE is Pr, nd and Gd, the mass ratio of Pr, nd and Gd is 1-2:0.1-2.5:1, preferably 1-2:1-2:1, specifically, may be 1:0.1: 1. 1:0.5: 1. 1:1: 1. 1:1.5: 1. 1:2: 1. 1:2.5: 1. 1.5:0.1: 1. 1.5:0.5: 1. 1.5:1: 1. 1.5:1.5: 1. 1.5:2: 1. 1.5:2.5: 1. 2:0.1: 1. 2:0.5: 1. 2:1: 1. 2:1.5:1. 2:2: 1. or 2:2.5:1. at this time, the effect of improving the electric conductivity of the aluminum alloy by the mixture of Pr, nd, and Gd was improved by 1.2 IACS values as compared with the case of adding La alone.
When RE is La and Ce, the mass ratio of La to Ce is 0.5-2:1, preferably 1-2:1, specifically, may be 0.5: 1. 1: 1. 1.5: 1. or 2:1. at this time, the effect of the mixture of La and Ce to improve the electric conductivity of the aluminum alloy is improved by 1.1 IACS values as compared to when La is added alone.
The mass percentage content of the impurities is not more than 0.15%, wherein the mass percentage content of the single impurities is less than 0.05%.
In one embodiment, the Bi may be specifically 0.001%, 0.005%, 0.01%, 0.02%, 0.03%, 0.04%, 0.05%, 0.06%, 0.07%, 0.08%, 0.09%, 0.1%, 0.11%, 0.12%, 0.13%, 0.14%, 0.15%, 0.16%, 0.17%, 0.18%, 0.19%, 0.2%, 0.21%, 0.22%, 0.23%, 0.24%, 0.25%, 0.26%, 0.27%, 0.28%, 0.29%, or 0.3% by mass. When the mass percentage content of Bi is not more than 0.3%, the mechanical property of the aluminum alloy can be improved; bi can react with Mg and the like to generate Mg 3 Bi 2 The second phase is equal, so that the Bi content is set to be larger than the Bi content (not larger than 0.1 percent) in the prior art, on one hand, the Bi is utilized to promote the performance of the aluminum alloy, and on the other hand, the Bi reacts with other elements as much as possible to generate the second phase so as to avoid the adverse effect on the performance of the aluminum alloy caused by excessive solid solution of the Bi in the aluminum matrix; the effect of Bi is overlapped with the effect of other elements, and even if the content of Bi is low, the problem that the performance of the aluminum alloy is difficult to be effectively improved due to the addition of the small content is avoided.
In one embodiment, the Sr may be 0.001%, 0.005%, 0.01%, 0.02%, 0.03%, 0.04%, 0.05%, 0.06%, 0.07%, 0.08%, 0.09%, 0.1%, 0.11%, 0.12%, 0.13%0.14%, 0.15%, 0.16%, 0.17%, 0.18%, 0.19%, or 0.2%. When the mass percentage content of Sr is not more than 0.2%, the mechanical property and the elongation of the aluminum alloy can be improved; sr is taken as an modifier, can be adsorbed on the surface of Si phase, inhibits the growth of the Si phase, enables beta-AlFeSi phase change Cheng Han-shaped alpha-AlFeSi phase in an ingot to improve the mechanical property of the aluminum alloy, and can be preferentially combined with elements such as Fe, cu, si and the like to form dispersion strengthening, so that the solid solubility of the elements in the alloy is reduced to improve the electric conductivity and the elongation, therefore, the Sr content can be set to be larger than the Sr content (not more than 0.1 percent) in the prior art, on one hand, the Sr is utilized to improve the property of the aluminum alloy, and on the other hand, the Sr is reacted with other elements to generate a second phase as much as possible to avoid the phenomenon that the Sr is excessively dissolved in an aluminum matrix to bring adverse effect on the property of the aluminum alloy; the effect of Sr is overlapped with the effect of other elements, even if the content of Sr is low, the problem that the performance of the aluminum alloy is difficult to be effectively improved due to the addition of less content is avoided; sr also promotes CuAl 2 、Mg 2 Si、Mg 2 Sn、Mg 2 Precipitation of Si and the like to reduce the solid solubility of the above elements in the aluminum matrix.
In one embodiment, the mass percentage of Mo may be specifically 0.001%, 0.005%, 0.01%, 0.02%, 0.03%, 0.04%, 0.05%, 0.06%, 0.07%, 0.08%, 0.09%, 0.1%, 0.11%, 0.12%, 0.13%, 0.14%, 0.15%, 0.16%, 0.17%, 0.18%, 0.19%, or 0.2%. When the mass percentage content of Mo is not more than 0.2%, the conductivity and fatigue resistance of the aluminum alloy can be improved; mo can react with Al, si, fe and the like to generate AlMo, alSiMo, alSiFeMo and other second phases, and is distributed on the grain boundary of the aluminum matrix in a disperse phase, so that the effects of improving the mechanical property, the corrosion resistance and the fatigue resistance of the aluminum alloy can be achieved; mo can refine grains, improve the morphology of Fe-containing intermetallic compounds and further improve the mechanical properties of the aluminum alloy.
In an embodiment, the content of Be by mass may Be specifically 0.001%, 0.005%, 0.01%, 0.02%, 0.03%, 0.04%, 0.05%, 0.06%, 0.07%, 0.08%, 0.09%, 0.1%, 0.11%, 0.12%, 0.13%, 0.14%, or 0.15%. When the mass percentage content of Be is not more than 0.15%, the mechanical property and the elongation of the aluminum alloy can Be improved; be can react with Al, fe, si and the like to generate Be-Fe (Al 8 Fe 2 SiBe) 2 The second phase is equal, so that the content of Be can Be set to Be larger than that of Be (not larger than 0.05%) in the prior art, on one hand, the performance of the aluminum alloy is improved by using Be, and on the other hand, the Be reacts with other elements as much as possible to generate the second phase so as to avoid the adverse effect on the performance of the aluminum alloy caused by excessive solid solution of the Be in an aluminum matrix; the action of Be coincides with the action of other elements, and even if the content of Be is low, the problem that the performance of the aluminum alloy is difficult to effectively improve due to the addition of less content is avoided; be can change the eutectic Si phase from flaky phase to fine phase to refine the Si phase, reduce or eliminate adverse effect of Si on the performance of aluminum alloy, and change the platy beta intermediate phase into relatively harmless Chinese character-like Be-Fe (Al) 8 Fe 2 SiBe) phase to reduce or eliminate adverse effect of Fe on aluminum alloy performance and promote Mg 2 Si, and Mg 3 Bi 2 And the like to reduce the solid solubility of the above elements in the aluminum matrix.
In one embodiment, the mass percentage of Ag may be specifically 0.001%, 0.005%, 0.01%, 0.02%, 0.03%, 0.04%, 0.05%, 0.06%, 0.07%, 0.08%, 0.09%, 0.1%, 0.11%, 0.12%, 0.13%, 0.14%, 0.15%, 0.16%, 0.17%, 0.18%, 0.19%, or 0.2%. Ag promotes the second phase (e.g. Al 2 Cu、Mg 2 Si、Mg 3 Sb 2 And Mg 3 Bi 2 Etc.), refining the precipitated phase and improving the density of the precipitated phase, and improving the precipitation strengthening effect of the aluminum alloy, thereby improving the mechanical property of the aluminum alloy.
In one embodiment, the mass percentage of Co may be 0.001%, 0.005%, 0.01%, 0.02%, 0.03%, 0.04%, 0.05%, 0.06%, 0.07%, 0.08%, 0.09%, 0.1%, 0.11%, 0.12%, 0.13%, 0.14%, 0.15%, 0.16%, 0.17%, 0.18%, 0.19%, 0.2%, 0.21%, 0.22%, 0.23%, 0.24%, 0.25%, 0.26%, 0.27%, 028%, 0.29%, or 0.3%. When the mass percentage content of Co is not more than 0.2%, the heat resistance, mechanical property and elongation of the aluminum alloy can be improved; co can react with Al, fe, si and the like to generate Al 15 (Fe,Co) 3 Si 2 、Al 3 The content of Co is set to be larger than the content of Co (not larger than 0.04 percent) in the prior art, on one hand, the performance of the aluminum alloy is improved by using Co, and on the other hand, co reacts with other elements as much as possible to generate a second phase so as to avoid the adverse effect on the performance of the aluminum alloy caused by excessive solid solution of Co in an aluminum matrix; the effect of Co is overlapped with the effect of other elements, even if the content of Co is low, the problem that the performance of the aluminum alloy is difficult to be effectively improved due to the addition of less Co is avoided; co to Al 3 The Fe phase has refining effect, and can also be used for preparing Al 3 Transformation of Fe phase into alpha-Al 15 (Fe,Co) 3 Si 2 (the shape of the alloy can be granular, small flower-shaped or fine strip-shaped), co can refine grains, and the mechanical property of the aluminum alloy is further improved.
In one embodiment, the In content may be 0.001%, 0.005%, 0.01%, 0.02%, 0.03%, 0.04%, 0.05%, 0.06%, 0.07%, 0.08%, 0.09%, 0.1%, 0.11%, 0.12%, 0.13%, 0.14%, 0.15%, 0.16%, 0.17%, 0.18%, 0.19%, or 0.2% by mass. When the mass percentage content of In is not more than 0.2%, the mechanical property of the aluminum alloy can be improved; in can react with Al and Cu to generate second phases such as AlIn and CuIn, so that the content of In can be set to be larger than that of In (not larger than 0.1 percent) In the prior art, on one hand, the performance of the aluminum alloy is improved by utilizing In, and on the other hand, in is reacted with other elements as much as possible to generate the second phases so as to avoid the adverse effect on the performance of the aluminum alloy caused by excessive solid solution of In an aluminum matrix; the effect of In is overlapped with the effect of other elements, and even if the content of In is low, the problem that the performance of the aluminum alloy is difficult to be effectively improved due to the addition of the small content is avoided; in can refine grains and further improve the mechanical property of the aluminum alloy.
In one embodiment, the Te may be specifically 0.001%, 0.005%, 0.01%, 0.02%, 0.03%, 0.04%, 0.05%, 0.06%, 0.07%, 0.08%, 0.09%, 0.1%, 0.11%, 0.12%, 0.13%, 0.14%, 0.15%, 0.16%, 0.17%, 0.18%, 0.19%, or 0.2% by mass. When the mass percentage content of Te is not more than 0.2%, the elongation, tensile strength and conductivity of the aluminum alloy can be improved; when Sb and Te are added in a compounding way, the solidification temperature interval of the aluminum alloy can be reduced, fine petal shapes rather than dendritic primary crystals are formed, and microscopic shrinkage porosity is reduced or eliminated, so that the comprehensive performance of the aluminum alloy, in particular the tensile strength, the elongation and the electrical conductivity, is improved.
In one embodiment, the Fe may be 0.001%, 0.005%, 0.01%, 0.02%, 0.03%, 0.04%, 0.05%, 0.06%, 0.07%, 0.08%, 0.09%, 0.1%, 0.11%, 0.12%, 0.13%, 0.14%, 0.15%, 0.16%, 0.17%, 0.18%, 0.19%, 0.2%, 0.21%, 0.22%, 0.23%, 0.24%, 0.25%, 0.26%, 0.27%, 0.28%, 0.29%, or 0.3% by mass. Fe can improve the elongation, mechanical property and heat resistance of the aluminum alloy; when the mass percentage of Fe is not more than 0.3%, the Fe can react with Al, RE, si, mg, B, cu, be to generate Al 3 Fe、AlFeRE、AlFeSi、AlFeMgSi、AlFeSiB、AlFeSiCu、Be-Fe(Al 8 Fe 2 SiBe) and the like, so that the content of Fe can be set to be larger than that of Fe in the prior art, the performance of the aluminum alloy is improved by utilizing Fe, and Fe can be reacted with other elements as much as possible to generate a second phase so as to avoid the adverse effect on the performance of the aluminum alloy caused by excessive solid solution of Fe in an aluminum matrix; the effect of Fe element is overlapped with the effect of other elements, and when the content of Fe is set to be low, the worry that the performance of the aluminum alloy is difficult to be effectively improved due to the addition of the small content is not needed.
The mass ratio of Mg to Bi is 1-500:1, preferably 5-400:1, more preferably 50 to 300:1, further preferably 100-200:1. in the range of the mass ratio, the electric conductivity of the aluminum alloy is gradually improved. Specifically, the mass ratio of Mg to Bi is 1: 1. 2: 1. 5: 1. 10: 1. 15: 1. 20:1. 25: 1. 30: 1. 40:1. 45: 1. 50: 1. 100: 1. 150: 1. 200:1. 250: 1. 300: 1. 350: 1. 400: 1. 450: 1. or 500:1.
the mass ratio of Cu to Bi is 1-40:1, preferably 2-30:1, more preferably 5 to 25:1, further preferably 10 to 20:1. within this mass ratio range, the tensile strength of the aluminum alloy gradually increases. Specifically, the mass ratio of Cu to Sb is 1: 1. 2: 1. 3: 1. 4: 1. 5: 1. 6: 1. 7: 1. 8: 1. 9: 1. 10: 1. 11: 1. 12: 1. 13: 1. 14: 1. 15: 1. 20:1. 25: 1. 30: 1. 35: 1. or 40:1.
Fe. The mass ratio of Cu to Sr is 0.5-20:0.2-10:1, preferably 1-15:0.5-10:1, more preferably 5 to 10:1-5:1, more preferably 5 to 8:2-3:1. in the range of the mass ratio, the tensile strength and heat resistance of the aluminum alloy are gradually improved. Specifically, the mass ratio of Fe, cu and Sr is 0.5:0.2: 1. 0.5:1: 1. 0.5:5: 1. 0.5:10: 1. 1:0.2: 1. 1:1: 1. 1:5: 1. 1:10: 1. 5:0.2: 1. 5:1: 1. 5:5: 1. 5:10: 1. 10:0.2: 1. 10:1: 1. 10:5: 1. 10:10: 1. 15:0.2: 1. 15:1: 1. 15:5: 1. 15:10: 1. 20:0.2: 1. 20:1: 1. 20:5: 1. or 20:10:1.
be. The mass ratio of Co to Fe is 0.5-20:0.5-10:1. preferably 1-15:1-8:1, more preferably 5 to 10:2-5:1, more preferably 5 to 6:2-3:1. in the range of the mass ratio, the mechanical property and the heat resistance of the aluminum alloy are gradually improved. Specifically, the mass ratio of Be, co and Fe is 0.5:0.5: 1. 0.5:1: 1. 0.5:5: 1. 0.5:10: 1. 1:0.5: 1. 1:1: 1. 1:5: 1. 1:10: 1. 5:0.5: 1. 5:1: 1. 5:5: 1. 5:10: 1. 10:0.5: 1. 10:1: 1. 10:5: 1. 10:10: 1. 15:0.5: 1. 15:1: 1. 15:5: 1. 15:10: 1. 20:0.5: 1. 20:1: 1. 120:5: 1. or 20:10:1.
The mass ratio of Si, fe and Sr is 1-200:0.5-10:1, preferably 5-150:1-5:1, more preferably 10 to 100:1-5:1, further preferably 20 to 30:2-5:1. within this mass ratio range, the tensile strength of the aluminum alloy gradually increases. Specifically, the mass ratio of Si, fe and Sr is 1:0.5: 1. 1:1: 1. 1:5: 1. 1:10: 1. 5:0.5: 1. 5:1: 1. 5:5: 1. 5:10:1. 10:0.5: 1. 10:1: 1. 10:5: 1. 10:10: 1. 50:0.5: 1. 50:1: 1. 50:5: 1. 50:10: 1. 100:0.5: 1. 100:1: 1. 100:5: 1. 100:10: 1. 150:0.5: 1. 150:1: 1. 150:5: 1. 150:10: 1. 200:0.5: 1. 200:1: 1. 200:5: 1. or 200:10:1.
fe. The mass ratio of RE to Sr is 0.5-15:0.5-10:1. preferably 0.5-12:0.5-8:1, more preferably 1 to 10:1-8:1, more preferably 2-8:2-6:1. within this mass ratio range, the heat resistance of the aluminum alloy gradually improves. Specifically, the mass ratio of Fe, RE, and Sr is 0.5:0.5: 1. 0.5:1: 1. 0.5:2: 1. 0.5:3: 1. 0.5:4: 1. 0.5:5: 1. 0.5:6: 1. 0.5:7: 1. 0.5:8: 1. 0.5:9: 1. 0.5:10: 1. 1:0.5: 1. 1:1: 1. 1:2: 1. 1:3: 1. 1:4: 1. 1:5: 1. 1:6: 1. 1:7: 1. 1:8: 1. 1:9: 1. 1:10: 1. 2:0.5: 1. 2:1: 1. 2:2: 1. 2:3: 1. 2:4: 1. 2:5: 1. 2:6: 1. 2:7: 1. 2:8: 1. 2:9: 1. 2:10: 1. 5:0.5: 1. 5:1: 1. 5:2: 1. 5:3: 1. 5:4: 1. 5:5: 1. 5:6: 1. 5:7: 1. 5:8: 1. 5:9: 1. 5:10:1. 10:0.5: 1. 10:1: 1. 10:2: 1. 10:3: 1. 10:4: 1. 10:5: 1. 10:6: 1. 10:7: 1. 10:8: 1. 10:9: 1. 10:10: 1. 15:0.5: 1. 15:1: 1. 15:2: 1. 15:3: 1. 15:4: 1. 15:5: 1. 15:6: 1. 15:7: 1. 15:8: 1. 15:9: 1. or 15:10:1.
Fe. The mass ratio of Co to Sr is 0.5-10:0.5-10:1. preferably 0.5 to 5:1-8:1, more preferably 1-5:2-5:1, more preferably 2-3:2-3:1. within this mass ratio range, the heat resistance of the aluminum alloy gradually improves. Specifically, the mass ratio of Fe, co and Sr is 0.5:0.5: 1. 0.5:1: 1. 0.5:2: 1. 0.5:3: 1. 0.5:4: 1. 0.5:5: 1. 0.5:6: 1. 0.5:7: 1. 0.5:8: 1. 0.5:9: 1. 0.5:10: 1. 1:0.5: 1. 1:1: 1. 1:2: 1. 1:3: 1. 1:4: 1. 1:5: 1. 1:6: 1. 1:7: 1. 1:8: 1. 1:9: 1. 1:10: 1. 2:0.5: 1. 2:1: 1. 2:2: 1. 2:3: 1. 2:4: 1. 2:5: 1. 2:6: 1. 2:7: 1. 2:8: 1. 2:9: 1. 2:10: 1. 5:0.5: 1. 5:1: 1. 5:2: 1. 5:3: 1. 5:4: 1. 5:5: 1. 5:6: 1. 5:7: 1. 5:8: 1. 5:9: 1. 5:10: 1. 10:0.5: 1. 10:1: 1. 10:2: 1. 10:3: 1. 10:4: 1. 10:5: 1. 10:6: 1. 10:7: 1. 10:8: 1. 10:9: 1. or 10:10:1.
the mass ratio of RE, B and Be is 0.5-20:0.1-10:1, preferably 1-20:0.5-10:1, more preferably 2 to 20:1-10:1, more preferably 5 to 20:2-10:1. in the range of the mass ratio, the electric conductivity, the tensile strength and the heat resistance of the aluminum alloy are gradually improved. Specifically, the mass ratio of RE, B and Be is 0.5:0.1: 1. 0.5:0.5: 1. 0.5:1: 1. 0.5:2: 1. 0.5:5: 1. 0.5:10: 1. 1:0.1: 1. 1:0.5: 1. 1:1: 1. 1:2: 1. 1:5: 1. 1:10: 1. 2:0.1: 1. 2:0.5: 1. 2:1: 1. 2:2: 1. 2:5: 1. 2:10: 1. 5:0.1: 1. 5:0.5: 1. 5:1: 1. 5:2: 1. 5:5: 1. 5:10: 1. 10:0.1: 1. 10:0.5: 1. 10:1: 1. 10:2: 1. 10:5: 1. 10:10:1. 15:0.1: 1. 15:0.5: 1. 15:1: 1. 15:2: 1. 15:5: 1. 15:10: 1. 20:0.1: 1. 20:0.5: 1. 20:1: 1. 20:2: 1. 20:5: 1. or 20:10:1.
Fe. The mass ratio of RE to B is 1-15:0.1-10:1. preferably 1-12:0.5-10:1, more preferably 2 to 10:1-10:1, more preferably 2-8:2-8:1. in the range of the mass ratio, the tensile strength and heat resistance of the aluminum alloy are gradually improved. Specifically, the mass ratio of Fe, RE and B is 1:0.1: 1. 1:0.5: 1. 1:1: 1. 1:2: 1. 1:3: 1. 1:4: 1. 1:5: 1. 1:6: 1. 1:7: 1. 1:8: 1. 1:9: 1. 1:10: 1. 2:0.1: 1. 2:0.5: 1. 2:1: 1. 2:2: 1. 2:3: 1. 2:4: 1. 2:5: 1. 2:6: 1. 2:7: 1. 2:8: 1. 2:9: 1. 2:10: 1. 3:0.1: 1. 3:0.5: 1. 3:1: 1. 3:2: 1. 3:3: 1. 3:4: 1. 3:5: 1. 3:6: 1. 3:7: 1. 3:8: 1. 3:9: 1. 3:10: 1. 4:0.1: 1. 4:0.5: 1. 4:1: 1. 4:2: 1. 4:3: 1. 4:4: 1. 4:5: 1. 4:6: 1. 4:7: 1. 4:8: 1. 4:9: 1. 4:10: 1. 5:0.1: 1. 5:0.5: 1. 5:1: 1. 5:2: 1. 5:3: 1. 5:4: 1. 5:5: 1. 5:6: 1. 5:7: 1. 5:8: 1. 5:9: 1. 5:10:1. 10:0.1: 1. 10:0.5: 1. 10:1: 1. 10:2: 1. 10:3: 1. 10:4: 1. 10:5: 1. 10:6: 1. 10:7: 1. 10:8: 1. 10:9: 1. 10:10: 1. 15:0.1: 1. 15:0.5: 1. 15:1: 1. 15:2: 1. 15:3: 1. 15:4: 1. 15:5: 1. 15:6: 1. 15:7: 1. 15:8: 1. 15:9: 1. or 15:10:1.
The mass ratio of Si to Mo is 1-100:1, preferably 10-50:1, more preferably 10 to 30:1, further preferably 10 to 20:1. in the range of the mass ratio, the tensile strength and heat resistance of the aluminum alloy are gradually improved. Specifically, the mass ratio of Si to Mo is 1:1. 2: 1. 3:1. 4: 1. 5: 1. 6: 1. 7: 1. 8: 1. 9: 1. 10:1. 20:1. 30: 1. 40: 1. 50: 1. 60: 1. 70: 1. 80: 1. 90: 1. or 100:1.
the mass ratio of Te to Sn is 0.01-10:1, preferably 0.05-8:1, more preferably 0.1 to 5:1, further preferably 2-3:1. in the range of the mass ratio, the tensile strength and the electric conductivity of the aluminum alloy are gradually improved. Specifically, the mass ratio of Te to Sn is 0.01: 1. 0.02: 1. 0.03: 1. 0.04: 1. 0.05: 1. 0.06: 1. 0.07: 1. 0.08: 1. 0.09: 1. 0.1:1. 0.2: 1. 0.3: 1. 0.4: 1. 0.5: 1. 0.6: 1. 0.7: 1. 0.8: 1. 0.9: 1. 1:1. 2: 1. 3:1. 4: 1. 5: 1. 6: 1. 7: 1. 8: 1. 9: 1. or 10:1.
the mass ratio of Te to Si is 0.001-1:1, preferably 0.005-1:1, more preferably 0.01 to 0.5:1, more preferably 0.05 to 0.1:1. in the range of the mass ratio, the tensile strength and heat resistance of the aluminum alloy are gradually improved. Specifically, the mass ratio of Te to Si is 0.001: 1. 0.002: 1. 0.003: 1. 0.004: 1. 0.005: 1. 0.01: 1. 0.05: 1. 0.1:1. 0.2: 1. 0.3: 1. 0.4: 1. 0.5: 1. or 1:1.
The mass ratio of Mg to Ag is 2-500:1, preferably 2-400:1, more preferably 5 to 300:1, further preferably 10 to 200:1. in the range of the mass ratio, the mechanical property of the aluminum alloy is gradually improved. Specifically, the mass ratio of Mg to Ag is 2: 1. 3: 1. 4: 1. 5: 1. 10: 1. 15: 1. 20: 1. 25: 1. 30:1. 35: 1. 40: 1. 45: 1. 50: 1. 60: 1. 70: 1. 80:1. 90: 1. 100: 1. 150: 1. 200:1. 250: 1. 300: 1. 350: 1. 400: 1. 450: 1. or 500:1.
the mass ratio of Cu to Ag is 1-80:1, preferably 10-60:1, more preferably 20 to 50:1, further preferably 20 to 30:1. in the range of the mass ratio, the tensile strength and heat resistance of the aluminum alloy are gradually improved. Specifically, the mass ratio of Cu to Ag is 1: 1. 2: 1. 3: 1. 4: 1. 5: 1. 6: 1. 7: 1. 8: 1. 9: 1. 10: 1. 11: 1. 12: 1. 13: 1. 14: 1. 15: 1. 16: 1. 17: 1. 18: 1. 19: 1. 20: 1. 21: 1. 22: 1. 23: 1. 24: 1. 25: 1. 26: 1. 27: 1. 28: 1. 29: 1. 30:1. 31: 1. 32: 1. 33: 1. 34: 1. 35: 1. 36: 1. 37: 1. 38: 1. 39: 1. 40: 1. 50: 1. 60: 1. 70: 1. or 80:1.
The mass ratio of Mg to In is 2-600:1. preferably 2-500:1, more preferably 5 to 400:1, further preferably 100-300:1. in the range of the mass ratio, the electric conductivity of the aluminum alloy is gradually improved. Specifically, the mass ratio of Mg to In is 2: 1. 3: 1. 4: 1. 5:1. 10:1. 15:1. 20: 1. 25: 1. 30: 1. 35: 1. 40:1. 45: 1. 50: 1. 60: 1. 70: 1. 80:1. 90: 1. 100: 1. 150: 1. 200: 1. 250: 1. 300:1. 350: 1. 400: 1. 450: 1. 500: 1. 550). 1. Or 600:1.
the mass ratio of Cu to In is 0.2-80:1. preferably 0.5 to 70:1, more preferably 10 to 60:1, further preferably 15-40:1. in the range of the mass ratio, the tensile strength and heat resistance of the aluminum alloy are gradually improved. Specifically, the mass ratio of Cu to In is 0.2: 1. 0.3: 1. 0.4: 1. 0.5: 1. 0.6: 1. 0.7: 1. 0.8: 1. 0.9: 1. 1: 1. 2: 1. 3: 1. 4: 1. 5:1. 6: 1. 7: 1. 8: 1. 9: 1. 10:1. 15:1. 20: 1. 25: 1. 30: 1. 35: 1. 40:1. 45: 1. 50: 1. 55: 1. 60: 1. 65: 1. 70: 1. 75: 1. or 80:1.
the mass ratio of In to B is 0.1-15:1. preferably 0.5-15:1, more preferably 1-12:1, further preferably 2 to 10:1. in the range of the mass ratio, the tensile strength and heat resistance of the aluminum alloy are gradually improved. Specifically, the mass ratio of In to B is 0.1: 1. 0.2: 1. 0.3: 1. 0.4: 1. 0.5: 1. 0.6: 1. 0.7: 1. 0.8: 1. 0.9: 1. 1: 1. 2: 1. 3: 1. 4: 1. 5:1. 6: 1. 7: 1. 8: 1. 9: 1. 10:1. 11: 1. 12: 1. 13: 1. 14: 1. or 15:1.
In the technical scheme of the invention, the Al-Mg-Si-Sn-RE aluminum alloy contains 0.1-1.3% by mass of Mg, 0.01-0.2% by mass of Cu, 0.1-0.7% by mass of Si, 0.01-0.3% by mass of Sn, 0.001-0.2% by mass of RE, 0-0.2% by mass of Zn, 0-0.15% by mass of B, 0-0.3% by mass of Nb and 0-0.3% by mass of Ge. The alloy also comprises 0-0.3% of Bi, 0-0.2% of Sr, 0-0.2% of Mo, 0-0.15% of Be, 0-0.2% of Ag, 0-0.3% of Co, 0-0.2% of In, 0-0.2% of Te and 0-0.3% of Fe. When the elements are independently added into an aluminum matrix, the improvement of the electric conductivity and the mechanical property of aluminum is limited, and even the electric conductivity and the mechanical property of aluminum are negatively affected. And when the elements are added independently and the content is small, the performance of the aluminum alloy is difficult to be effectively improved; the addition of these elements alone and in relatively high amounts may have a negative effect on certain properties of the aluminum alloy. The invention adds the elements with the content into the aluminum matrix, and the interaction of the elements can reduce the interaction The solid solubility in the aluminum matrix is improved, the volume fraction of the precipitated phase is increased, the adverse effect of certain elements on conductivity is reduced, and the comprehensive performance is improved, and even if the content of one or more elements is lower or higher, the comprehensive performance of the aluminum alloy can be greatly improved. Specifically, the content of at least one of the above elements is set to be larger than that in the prior art, and the elements can interact mutually to promote the desolventizing and precipitation of the elements so as to reduce the solid solubility of the elements in the aluminum matrix and promote the volume fraction of the precipitated phase, thereby improving the comprehensive performance of the aluminum alloy, and coarser second phase and the precipitated phase (such as Al 3 RE、Al 3 Fe、Mg 2 Si、Mg 2 Equal Sn) are refined in the matrix and the grain boundary or the grain boundary under the combined action of large deformation stress and special heat treatment process, thereby reducing the adverse effect of the elements on the performance of the aluminum alloy when the content is higher, mg 2 Si、Mg 2 The precipitation kinetics of various precipitation phases such as Sn can be mutually influenced, so that the size of the precipitation phases is not easy to grow, the volume fraction of the precipitation phases is improved, in addition, alloy elements can be mutually dissolved into proper second phases, and the comprehensive performance of the aluminum alloy can be improved, so that the content of at least one element in the elements is set to be larger than that in the prior art, on one hand, the elements are utilized to improve the performance of the aluminum alloy, and the elements, particularly the elements with higher content, can be reacted with other elements to generate the second phases as much as possible, so that adverse effects on the performance of the aluminum alloy caused by excessive solid solution of the elements, particularly the elements with higher content, are avoided, and the source range of raw materials is enlarged. Moreover, the effects of at least part of the elements are coincident, for example, the elements can basically improve the mechanical property of the aluminum alloy, some elements can improve the electric conductivity, the elongation and the heat resistance of the aluminum alloy, even if the content of one or more of the elements is low, the effect of effectively improving the aluminum alloy is not required to be worried about when the content of one or more of the elements is low, and a plurality of elements with the same effect are added simultaneously, so that the use amount of the alloy elements can be greatly reduced, the effect is improved, namely, a small amount of a plurality of elements are used for replacing a large amount of single elements, and the effect is greatly improved And the mechanical property and the electric conductivity are improved. In addition, the addition amount of the element which is low in cost can be set larger without worrying about the adverse effect of excessive addition on the performance of the aluminum alloy, for example, the addition amount of Si, cu, sn, zn can be set larger without worrying about the adverse effect of a large amount of Si, cu, sn, zn on the performance of the aluminum alloy. The aluminum alloy can adopt Cu, sn, zn and the like with higher content range, so that the invention can adopt common aluminum ingots or regenerated aluminum with low price as raw materials, and the cost is further reduced. In summary, mg, cu, si, sn, RE, zn, B, nb and Ge are added into an aluminum matrix together, or Mg, cu, si, sn, RE, zn, B, nb, ge, bi, sr, mo, be, ag, co, in, te and Fe are added into an aluminum matrix together, and the elements interact and influence each other as a whole, so that the comprehensive performance of the aluminum alloy can be greatly improved even if the content of one or more elements is low or high. Specifically, the tensile strength of the Al-Mg-Si-Sn-RE rare earth aluminum alloy is larger than that of a medium-strength aluminum alloy with the brand name LHA4 in a row mark (the tensile strength of the medium-strength aluminum alloy with the LHA4 is 255-290 MPa), and the elongation and the conductivity are larger than those of the medium-strength aluminum alloy with the brand name LHA3 in the row mark (the elongation of the medium-strength aluminum alloy with the LHA3 is larger than 3.5 percent and the conductivity is 58.5 percent). Therefore, the Al-Mg-Si-Sn-RE rare earth aluminum alloy has better comprehensive performance, and can prevent the defects of increased cost, complex process, blind performance adjustment and the like caused by adding excessive impurity elements into an aluminum matrix.
The Al-Mg-Si-Sn-RE rare earth aluminum alloy also contains 0-0.1% by mass of C. The content of C may be specifically 0.001%, 0.005%, 0.01%, 0.02%, 0.03%, 0.04%, 0.05%, 0.06%, 0.07%, 0.08%, 0.09%, or 0.1% by mass. C is used as a high-efficiency modifier, can react with Fe, cu, mg and the like to generate carbide so as to improve the mechanical property of the aluminum alloy, and can also be used as a refiner so as to improve the elongation of the aluminum alloy. C. The mass ratio of Fe, cu and Mg is 1:1-500:0.5-300:0.5 to 400, preferably 1:300-400:100-200:100-300. In the range of the ratio, the mechanical property and the elongation of the aluminum alloy can be effectively improved by the C.
The Al-Mg-Si-Sn-RE rare earth aluminum alloy also contains Na with the mass percentage content of 0-0.1 percent. The Na content may be specifically 0.001%, 0.005%, 0.01%, 0.02%, 0.03%, 0.04%, 0.05%, 0.06%, 0.07%, 0.08%, 0.09%, or 0.1% by mass. Na can react with Al and Si to generate Al 2 Na 3 、AlNa 2 、AlNa 5 The NaAlSi and other compounds react with Fe, mg, RE to produce NaRE, naMgFeRE and other compounds, which are dispersed in aluminum alloy, and Na can refine grains to raise the mechanical performance, fatigue resistance and elongation of the aluminum alloy. The mass ratio of Na, fe, mg and RE is 1:1-600:0.5-500:0.5 to 300, preferably 1:100-400:100-300:100-200. In the ratio range, the mechanical property, fatigue resistance and elongation of the aluminum alloy can be effectively improved.
The Al-Mg-Si-Sn-RE rare earth aluminum alloy also contains 0-0.1% of K by mass percent. The content of K may be specifically 0.001%, 0.005%, 0.01%, 0.02%, 0.03%, 0.04%, 0.05%, 0.06%, 0.07%, 0.08%, 0.09%, or 0.1% by mass. K can react with Al to generate Al 5 K 7 、Al 3 K 4 、Al 2 K 3 、AlK 2 The equal-high-temperature strengthening phase can improve the heat resistance and mechanical property of the aluminum alloy.
The Al-Mg-Si-Sn-RE rare earth aluminum alloy also contains 0-0.1% of Hf by mass percent. The content of Hf may be specifically 0.001%, 0.005%, 0.01%, 0.02%, 0.03%, 0.04%, 0.05%, 0.06%, 0.07%, 0.08%, 0.09%, or 0.1% by mass. Hf can react with Fe, cu, al and the like to generate various second phases, and can improve the fatigue resistance, heat resistance, wear resistance and mechanical property of the aluminum alloy. Hf. The mass ratio of Fe to Cu is 1:1-400:0.5 to 300, preferably 1:200-300:100-200. In the range of the ratio, the fatigue resistance, heat resistance, wear resistance and mechanical property of the aluminum alloy can be effectively improved.
The Al-Mg-Si-Sn-RE rare earth aluminum alloy also contains 0 to 0.1 percent by mass percentIs not shown). The Ir content may be specifically 0.001%, 0.005%, 0.01%, 0.02%, 0.03%, 0.04%, 0.05%, 0.06%, 0.07%, 0.08%, 0.09%, or 0.1% by mass. Ir can react with Fe and Al to generate Al 5 Ir 3 、Al 3 Ir 2 、AlIr 2 、Al 4 The strengthening phase such as (IrFe) can improve the fatigue resistance and heat resistance of the aluminum alloy. The mass ratio of Ir to Fe is 1:5-420, preferably 1:100-300. In the range of the ratio, the fatigue resistance and heat resistance of the aluminum alloy can be effectively improved.
The Al-Mg-Si-Sn-RE rare earth aluminum alloy also contains 0-0.1% of Rh by mass percent. The Rh may be specifically 0.001%, 0.005%, 0.01%, 0.02%, 0.03%, 0.04%, 0.05%, 0.06%, 0.07%, 0.08%, 0.09%, or 0.1% by mass. Rh can react with Fe and Al to generate Al 5 Rh 2 、Al 3 Rh 2 、AlRh 2 、Al 4 And (RhFe) and other strengthening phases, and can improve the fatigue resistance and heat resistance of the aluminum alloy. The mass ratio of Rh to Fe is 1:1-450, preferably 1:200-300. In the range of the ratio, the fatigue resistance and heat resistance of the aluminum alloy can be effectively improved.
The Al-Mg-Si-Sn-RE rare earth aluminum alloy also contains Ru with the mass percentage content of 0-0.1%. The Ru content may be specifically 0.001%, 0.005%, 0.01%, 0.02%, 0.03%, 0.04%, 0.05%, 0.06%, 0.07%, 0.08%, 0.09%, or 0.1% by mass. Ru can react with Al to generate RuAl 4 The high-temperature strengthening phase can improve the mechanical property and heat resistance of the aluminum alloy, ru can inhibit the recrystallization coarsening effect, promote the solid solution strengthening of the second phase and further improve the mechanical property of the aluminum alloy.
The Al-Mg-Si-Sn-RE rare earth aluminum alloy also contains Rb with the mass percentage content of 0-0.1%. The Rb content may be specifically 0.001%, 0.005%, 0.01%, 0.02%, 0.03%, 0.04%, 0.05%, 0.06%, 0.07%, 0.08%, 0.09%, or 0.1% by mass. Rb can react with Al to form Al 7 Rb 9 、Al 5 Rb 3 、AlRb 2 、AlRb 4 Equal strengthAnd the phase is changed, so that the tensile strength of the aluminum alloy can be improved.
The Al-Mg-Si-Sn-RE rare earth aluminum alloy also contains 0-0.1% of Pd by mass percent. The content of Pd may be specifically 0.001%, 0.005%, 0.01%, 0.02%, 0.03%, 0.04%, 0.05%, 0.06%, 0.07%, 0.08%, 0.09%, or 0.1% by mass. Pd can react with Al to generate AlPd 2 、Al 3 Pd、Al 2 Pd and other high temperature strengthening phases, and can refine Fe phase to improve the mechanical property of the aluminum alloy.
The Al-Mg-Si-Sn-RE rare earth aluminum alloy also contains 0-0.1% of Au by mass percent. The content of Au may be specifically 0.001%, 0.005%, 0.01%, 0.02%, 0.03%, 0.04%, 0.05%, 0.06%, 0.07%, 0.08%, 0.09%, or 0.1% by mass. After a small amount of Au is added into the aluminum alloy, the formation of an aging transition phase can be promoted, the stability of the transition phase is improved, the aging hardening characteristic of the alloy is improved, and the mechanical property of the alloy is greatly improved.
The Al-Mg-Si-Sn-RE rare earth aluminum alloy also contains 0-0.1% of Ba by mass percent. The content of Ba may be specifically 0.001%, 0.005%, 0.01%, 0.02%, 0.03%, 0.04%, 0.05%, 0.06%, 0.07%, 0.08%, 0.09%, or 0.1% by mass. Ba can react with Al to generate Al 14 Ba 13 、Al 10 Ba 12 、Al 7 Ba 8 、AlBa 5 And the like, can improve the mechanical property and heat resistance of the aluminum alloy.
The Al-Mg-Si-Sn-RE rare earth aluminum alloy also contains 0-0.1% of Li by mass percent. The content of Li by mass may be specifically 0.001%, 0.005%, 0.01%, 0.02%, 0.03%, 0.04%, 0.05%, 0.06%, 0.07%, 0.08%, 0.09%, or 0.1%. Li can react with Al to generate Al 2 Li 3 、AlLi 2 And AlLi 5 The equal high temperature strengthening phase can improve the mechanical property of the aluminum alloy.
The Al-Mg-Si-Sn-RE rare earth aluminum alloy also contains 0-0.1% of Pt by mass percent. The mass percentage of Pt can be 0.001%, 0.005%, 0.01%, 0.02%, 0.03%, 0.04%, 0.05%, 0.06%, 0.07%, 0.08%, 0.09%, or 0.1%. Pt can react with Al to generate AlPt 2 、Al 3 Pt 2 、Al 5 Pt 3 And the like, and can improve the mechanical properties of the aluminum alloy.
The Al-Mg-Si-Sn-RE rare earth aluminum alloy also contains Ta with the mass percentage content of 0-0.1%. The content of Ta may be specifically 0.001%, 0.005%, 0.01%, 0.02%, 0.03%, 0.04%, 0.05%, 0.06%, 0.07%, 0.08%, 0.09%, or 0.1% by mass. Ta forms Al in aluminum alloys 7 Ta 9 、Al 7 Ta 5 、Al 3 Ta 4 、Al 2 Ta 3 、AlTa 2 And the mechanical properties of the aluminum alloy are improved by the equal-high-temperature strengthening phase.
The invention also provides a preparation method of the Al-Mg-Si-Sn-RE rare earth aluminum alloy, which comprises the following steps:
smelting: heating an aluminum source (such as an aluminum ingot) to 720-780 ℃ to obtain an aluminum liquid, adding Mg, cu, si, sn, RE, zn, B, nb and Ge into the aluminum liquid for heating and smelting, uniformly stirring, refining, degassing and deslagging, standing at 700-750 ℃ for 10-30min to obtain an alloy liquid, and then standing at a constant temperature to detect components and content;
continuous casting and rolling: after the components and the content are detected to be qualified, carrying out continuous casting and rolling treatment and quenching treatment on the alloy liquid subjected to the degassing and slag removing treatment to obtain an aluminum alloy rod;
and (3) drawing: drawing the quenched aluminum alloy rod to obtain an aluminum alloy wire with the diameter smaller than 5 mm; and
Aging treatment: aging the aluminum alloy wire, and cooling to obtain an Al-Mg-Si-Sn-RE rare earth aluminum alloy, wherein the Al-Mg-Si-Sn-RE rare earth aluminum alloy contains Al, 0.1-1.3% of Mg, 0.01-0.2% of Cu, 0.1-0.7% of Si, 0.01-0.3% of Sn, 0.001-0.2% of RE, 0-0.2% of Zn, 0-0.15% of B, 0-0.3% of Nb, 0-0.3% of Ge, al and unavoidable impurities;
It can be understood that when the content of each component in the alloy liquid after the degassing and slag skimming treatment is detected to reach the standard, the subsequent treatment such as continuous casting and rolling is performed. Wherein the aluminum alloy contains 0.1 to 1.3% by mass of Mg, 0.01 to 0.2% by mass of Cu, 0.1 to 0.7% by mass of Si, 0.01 to 0.3% by mass of Sn, 0.001 to 0.2% by mass of RE, 0 to 0.2% by mass of Zn, 0 to 0.15% by mass of B, 0 to 0.3% by mass of Nb, 0 to 0.3% by mass of Ge, al and unavoidable impurities. The mass percentage content of the impurities is not more than 0.15%, wherein the mass percentage content of the single impurities is less than 0.05%. When the detection of the components and the content is not qualified, corresponding elements can be added for adjustment until the detection of the components and the content is qualified.
In an embodiment, the quenching treatment may be an in-line water quenching treatment.
In one embodiment, the aluminum alloy may be further subjected to a twisting process. The stranding treatment is as follows: and stranding the aluminum alloy wire and the high-elastic wire.
In one embodiment, at least one of Bi, sr, mo, be, ag, co, in, te, fe, C, na, K, hf, ir, rh, ru, rb, pd, au, ba, li, pt, ta may also be added to the aluminum liquid.
In one embodiment, mg, cu, si, sn, RE, zn, B, nb, ge, bi, sr, mo, be, ag, co, in, te, fe, C, na, K, hf, ir, rh, ru, rb, pd, au, ba, li, pt, ta is added as a simple substance and/or as an aluminum master alloy.
In one embodiment, the casting temperature is 680-750deg.C and the rolling temperature is 450-550deg.C.
In an embodiment, the drawing process may be cold drawing. During cold drawing, the aluminum alloy rod is drawn into aluminum alloy wires with the preset diameter range, the elongation coefficient of each cold drawing is controlled to be 0.5-2, the temperature is raised to 250-350 ℃ after each cold drawing, the heat is preserved for 5-20h, and secondary heat treatment is carried out, so that the aluminum alloy wires are obtained.
In one embodiment, the aging treatment is a discontinuous aging process, and the Al-Mg-Si-Sn-RE rare earth aluminum alloy is a medium strength semi-heat treatment semi-work hardening Al-Mg-Si-Sn-RE rare earth aluminum alloy. The intermittent aging process comprises the following steps: the intermittent aging process comprises the following steps: performing primary low-temperature aging treatment at 100-150deg.C for 1-50h; performing secondary natural aging treatment at 20-60deg.C for 10-24 hr; performing three-stage high temperature aging treatment at 160-350deg.C for 0.1-150 hr. The primary low temperature aging treatment may be at a temperature of 100deg.C, 110deg.C, 120deg.C, 130deg.C, 140deg.C, or 150deg.C for 1h, 5h, 10h, 15h, 20h, 25h, 30h, 35h, 40h, 45h, or 50h. The temperature of the secondary natural aging treatment can be 20 ℃, 30 ℃, 40 ℃, 50 ℃ or 60 ℃ for 10 hours, 15 hours, 20 hours or 24 hours. The temperature of the three-stage high temperature aging treatment can be 160 ℃, 170 ℃, 180 ℃, 190 ℃, 200 ℃, 250 ℃, 300 ℃ or 350 ℃ for 0.1h, 1h, 5h, 10h, 50h, 100h or 150h. The ratio of the temperature of the three-stage high-temperature aging treatment to the temperature of the one-stage low-temperature aging treatment can be 2.5-17.5:1, preferably 5-10:1. when the primary low-temperature aging treatment is carried out, the primary low-temperature aging treatment and the internal stress of the aluminum alloy act together (namely, the internal stress and the thermal stress act together), so that the formation of GP zones is obviously improved, the range of the GP zones is enlarged, and no phase size and type transformation exists; when the secondary natural aging treatment is carried out, the aluminum alloy is still in a high oversaturation state, the high oversaturation state can lead the aluminum alloy to continuously form a large number of GP zones during the secondary natural aging treatment, the size of the GP zone formed by the aluminum alloy during the primary low-temperature aging treatment is not obviously changed and cannot be converted into beta' phase due to lower temperature, two GP zone nuclei (it can be understood that the two GP zone nuclei can be connected into a whole or can be arranged at intervals) of the aluminum alloy during the primary low-temperature aging treatment and the secondary natural aging treatment can lead the GP zone density of the aluminum alloy to be obviously increased, and the aluminum alloy is subjected to the tertiary high-temperature aging treatment The gradual transition of the GP zone to the beta "phase, the precipitation of beta" provides a number of nucleation sites at which the size and volume fraction of the precipitated phases in the alloy (e.g., mg 2 Si、Mg 2 Equal Sn), the conductivity is gradually increased, the strength is first increased and then decreased, and the trend of the change of the elongation and the heat resistance is opposite to the strength. Therefore, the intermittent aging process not only can greatly improve the mechanical properties of the alloy, but also can greatly improve the conductivity, the elongation and the heat resistance of the aluminum alloy. Due to Al 3 RE、Al 3 And the second phase with good stability such as Fe is pinned to grain boundary and matrix, alloy grains are thinned and stretched along the deformation direction under the action of large deformation stress in continuous casting and rolling and drawing treatment, the second phase is crushed and thinned, no precipitation band between crystals is narrowed, and the conductivity, the tensile strength and the elongation along the drawing direction are improved. Compared with the second phase subjected to common aging treatment, the precipitated phase (such as Mg 2 Si、Mg 2 Sn equal) is smaller.
In another embodiment, the aging treatment is a discontinuous aging process, and the Al-Mg-Si-Sn-RE-based rare earth aluminum alloy is a medium strength semi-heat treated semi-work hardened Al-Mg-Si-Sn-RE-based rare earth aluminum alloy. The intermittent aging process comprises the following steps: performing primary low-temperature aging treatment at 100-150deg.C for 1-50h; performing secondary natural aging treatment at 20-60deg.C for 10-24 hr; performing three-stage high-temperature aging treatment at 160-250deg.C for 0.1-100h; four-stage high-temperature aging treatment is carried out at 250-350 ℃ for 0.1-50h. The primary low temperature aging treatment may be at a temperature of 100deg.C, 110deg.C, 120deg.C, 130deg.C, 140deg.C, or 150deg.C for 1h, 5h, 10h, 15h, 20h, 25h, 30h, 35h, 40h, 45h, or 50h. The temperature of the secondary natural aging treatment can be 20 ℃, 30 ℃, 40 ℃, 50 ℃ or 60 ℃ for 10 hours, 15 hours, 20 hours or 24 hours. The temperature of the three-stage high temperature aging treatment can be 160 ℃, 170 ℃, 180 ℃, 190 ℃, 200 ℃, or 250 ℃ for 0.1h, 1h, 5h, 10h, 50h, or 100h. The four levels are high The temperature of the warm aging treatment may be 250 ℃, 260 ℃, 270 ℃, 280 ℃, 290 ℃, 300 ℃, 310 ℃, 320 ℃, 330 ℃, 340 ℃, or 350 ℃ for 0.1h, 1h, 5h, 10h, 20h, 30h, 40h, or 50h. The ratio of the temperature of the three-stage high-temperature aging treatment to the temperature of the one-stage low-temperature aging treatment can be 1.1-2.5:1, preferably 1.5-2:1. the ratio of the temperature of the four-stage high-temperature aging treatment to the temperature of the one-stage low-temperature aging treatment can be 1.5-35:1, preferably 10-20:1. when the primary low-temperature aging treatment is carried out, the primary low-temperature aging treatment and the internal stress of the aluminum alloy act together (namely, the internal stress and the thermal stress act together), so that the formation of GP zones is obviously improved, the range of the GP zones is enlarged, and no phase size and type transformation exists; when the secondary natural aging treatment is carried out, the aluminum alloy is still in a high oversaturation state, the high oversaturation state can lead the aluminum alloy to continuously form a large number of GP zones during the secondary natural aging treatment, the size of the GP zone formed by the aluminum alloy during the primary low-temperature aging treatment is not obviously changed and cannot be converted into beta ', two GP zone nucleation (it is understood that the two GP zone nucleation can be connected into a whole or can be arranged at intervals) of the aluminum alloy during the primary low-temperature aging treatment and the secondary natural aging treatment can lead the GP zone density of the aluminum alloy to be obviously increased, the three-stage high-temperature aging treatment is carried out, the GP zone is gradually converted into beta ', the precipitation of beta ', and a plurality of nucleation sites are provided, and the size and the volume fraction (such as Mg) of the precipitated phase in the alloy 2 Si、Mg 2 Sn is equal), the strength, the conductivity and the heat resistance are gradually improved, the elongation is gradually reduced, and finally, the fourth-stage high-temperature aging treatment can enable elements dissolved in the matrix to be continuously precipitated and grown, the strength is reduced, and the conductivity, the heat resistance and the elongation are improved. Therefore, the intermittent aging process not only can greatly improve the mechanical properties of the alloy, but also can greatly improve the conductivity, the elongation and the heat resistance of the aluminum alloy. Due to Al 3 RE、Al 3 A second phase pinning grain boundary and a matrix with good stability such as Fe, wherein alloy grains are thinned and stretched along a deformation direction under the action of large deformation stress in continuous casting and rolling and drawing processes, and a second phase pinning grain boundary and a matrix with good stability such as FeThe phase is crushed and thinned, and the band without precipitation among crystals is narrowed, so that the conductivity, the tensile strength and the elongation in the wire drawing direction are improved. Compared with the second phase subjected to common aging treatment, the precipitated phase (such as Mg 2 Si、Mg 2 Sn equal) is smaller.
In one embodiment, the refining treatment is performed at a temperature of 690-750 ℃ for a period of 10-20 minutes. The refining agent for refining treatment can comprise the following raw materials in parts by weight: 60-70 parts of KF, 50-60 parts of NaC1, 40-60 parts of LiCl, 20-25 parts of cryolite and AIF 3 10-25 parts of CaF 2 10-15 parts of light calcium carbonate 5-10 parts of graphite powder 15-20 parts of talcum powder 10-20 parts of MgCl 2 20-30 parts of rare earth acid salt and 10-30 parts of rare earth acid salt. The rare earth acid salt can be one of chloride, fluoride and nitric acid compound of light rare earth and more than one compound. The rare earth acid salt can be one or more of chlorides, fluorides and nitric acid compounds of heavy rare earth and is compounded by the heavy rare earth. The mass ratio of the refining agent to the alloy liquid is 0.0013-0.0018:1.
according to the technical scheme, mg, cu, si, sn, RE, zn, B, nb and Ge are added into aluminum liquid, and after heating and smelting, continuous casting and rolling, drawing treatment, stranding treatment and time-efficient treatment are carried out to obtain the Al-Mg-Si-Sn-RE rare earth aluminum alloy. The Al-Mg-Si-Sn-RE rare earth aluminum alloy contains 0.1-1.3% by mass of Mg, 0.01-0.2% by mass of Cu, 0.1-0.7% by mass of Si, 0.01-0.3% by mass of Sn, 0.001-0.2% by mass of RE, 0-0.2% by mass of Zn, 0-0.15% by mass of B, 0-0.3% by mass of Nb and 0-0.3% by mass of Ge. When the elements are independently added into an aluminum matrix, the improvement of the electric conductivity and the mechanical property of aluminum is limited, and even the electric conductivity and the mechanical property of aluminum are negatively affected. And when the elements are added independently and the content is small, the performance of the aluminum alloy is difficult to be effectively improved; the addition of the above elements alone and in high amounts may be specific to the aluminum alloy Can have negative effects. The invention adds the elements with the content into the aluminum matrix together, the interaction of the elements is mutually influenced, the solid solubility of the elements in the aluminum matrix can be reduced, the volume fraction of the precipitated phase is increased, the adverse effect of certain elements on the conductivity is reduced, the comprehensive performance is improved, and the comprehensive performance of the aluminum alloy can be greatly improved even if the content of one or more elements is lower or higher. Specifically, the content of at least one of the above elements is set to be larger than that in the prior art, and the elements can interact mutually to promote the desolventizing and precipitation of the elements so as to reduce the solid solubility of the elements in the aluminum matrix and promote the volume fraction of the precipitated phase, thereby improving the comprehensive performance of the aluminum alloy, and coarser second phase and the precipitated phase (such as Al 3 RE、Al 3 Fe、Mg 2 Si、Mg 2 Equal Sn) are refined in the matrix and the grain boundary or the grain boundary under the combined action of large deformation stress and special heat treatment process, thereby reducing the adverse effect of the elements on the performance of the aluminum alloy when the content is higher, mg 2 Si、Mg 2 The precipitation kinetics of various precipitation phases such as Sn can be mutually influenced, so that the size of the precipitation phases is not easy to grow, the volume fraction of the precipitation phases is improved, in addition, alloy elements can be mutually dissolved into proper second phases, and the comprehensive performance of the aluminum alloy can be improved, so that the content of at least one element in the elements is set to be larger than that in the prior art, on one hand, the elements are utilized to improve the performance of the aluminum alloy, and the elements, particularly the elements with higher content, can be reacted with other elements to generate the second phases as much as possible, so that adverse effects on the performance of the aluminum alloy caused by excessive solid solution of the elements, particularly the elements with higher content, are avoided, and the source range of raw materials is enlarged. Moreover, the effects of at least part of the elements are coincident, for example, the elements can basically improve the mechanical property of the aluminum alloy, some elements can improve the electric conductivity, the elongation and the heat resistance of the aluminum alloy, even if the content of one or more of the elements is low, the elements are not required to be added in a small amount, the aluminum alloy performance is difficult to be effectively improved, and a plurality of elements with the same effects are the same When the alloy is added, the use amount of alloy elements can be greatly reduced, and the action effect is improved, namely, a small amount of multiple elements are used for replacing a large amount of single elements, so that the mechanical property and the electric conductivity are greatly improved. In addition, the addition amount of the element which is low in cost can be set larger without worrying about the adverse effect of excessive addition on the performance of the aluminum alloy, for example, the addition amount of Si, cu, sn, zn can be set larger without worrying about the adverse effect of a large amount of Si, cu, sn, zn on the performance of the aluminum alloy. The aluminum alloy can adopt Cu, sn, zn and the like with higher content range, so that the invention can adopt common aluminum ingots or regenerated aluminum with low price as raw materials, and the cost is further reduced. In summary, mg, cu, si, sn, RE, zn, B, nb and Ge are added into an aluminum matrix together, and the elements interact as a whole to influence each other, so that the comprehensive performance of the aluminum alloy can be greatly improved even if the content of one or more elements is low or high. Specifically, the tensile strength of the Al-Mg-Si-Sn-RE rare earth aluminum alloy is larger than that of a medium-strength aluminum alloy with the brand name LHA4 in a row mark (the tensile strength of the medium-strength aluminum alloy with the LHA4 is 255-290 MPa), and the elongation and the conductivity are larger than those of the medium-strength aluminum alloy with the brand name LHA3 in the row mark (the elongation of the medium-strength aluminum alloy with the LHA3 is larger than 3.5 percent and the conductivity is 58.5 percent). Therefore, the Al-Mg-Si-Sn-RE rare earth aluminum alloy has better comprehensive performance, and can prevent the defects of increased cost, complex process, blind performance adjustment and the like caused by adding excessive impurity elements into an aluminum matrix.
It will be appreciated that when using recycled aluminum as the aluminum source, the composition and content of the recycled aluminum may be detected, and the elements and content to be added to the recycled aluminum liquid may be designed based on the detected composition and content.
The invention also provides a heat-resistant cable which comprises a wire core and an insulating layer coating the wire core, wherein the wire core is made of the Al-Mg-Si-Sn-RE rare earth aluminum alloy, and can be a stranded body of the Al-Mg-Si-Sn-RE rare earth aluminum alloy and a high-elastic wire. The heat resistant cable may further include other elements, and in one embodiment, the heat resistant cable may further include an inner shielding layer disposed between the core and the insulating layer, an outer shielding layer covering the insulating layer, and a protective layer covering the core and the outer shielding layer, etc.
Because the heat-resistant cable adopts all the technical schemes of all the embodiments, the heat-resistant cable has at least all the beneficial effects brought by the technical schemes of the embodiments, and the description is omitted herein.
Examples and comparative examples
The compositions and contents of the aluminum alloys of examples one to seven and comparative examples one to four are shown in Table 1, and the results of the performance tests are shown in Table 2.
TABLE 1 Components and contents of aluminum alloys of examples one to seven and comparative examples one to four
For simplicity of description, the comparative examples and examples do not show the contents of trace elements such as impurities.
According to the test requirements of GB/T3048.2 electric wire and cable performance test method, the electric conductivity of the aluminum alloys of examples one to seven and comparative examples one to four is tested by adopting a digital direct current bridge instrument with the model number QJ57 manufactured by Shanghai brand electric technology Co., ltd. The specification of the test sample is phi 2.5mm multiplied by 1000mm, the temperature is controlled to be 20+/-0.1 ℃ in the test process, and three test samples are tested in the same state and averaged.
The mechanical properties of the aluminum alloys of examples one to seven and comparative examples one to four were tested at room temperature using a domestic CSS-44100 electronic universal stretcher according to the test requirements of GB/T4909.3 "bare wire tensile test". Wherein, the tensile force of the electronic universal stretcher is 2kN, the tensile speed is 2mm/min, three samples are tested in the same state, and the average value is taken.
The heat resistance (strength remaining rate) of the aluminum alloys of examples one to seven and comparative examples one to four was tested using a domestic JCT-1 type electrothermal high temperature drying oven with a temperature fluctuation of ±1℃. Wherein, the annealing temperature is 230 ℃, the heat preservation time is 1h, three samples are tested under the same state, and the average value is taken.
Table 2 results of performance test of aluminum alloys of examples one to seven and comparative examples one to four
The tensile strength, elongation, electrical conductivity and heat resistance of the Al-Mg-Si-Sn-RE rare earth aluminum alloys of examples one to seven were significantly greater than those of the Al-Mg-Si-Sn-RE rare earth aluminum alloys of comparative examples one to four. The following is indicated: the Al-Mg-Si-Sn-RE rare earth aluminum alloy has better performances.
The foregoing description is only of the preferred embodiments of the present invention and is not intended to limit the scope of the invention, and all equivalent structural changes made by the content of the present invention under the inventive concept of the present invention, or direct/indirect application in other related technical fields are included in the scope of the present invention.
Claims (11)
1. An Al-Mg-Si-Sn-RE rare earth aluminum alloy containing Al, characterized in that: the Al-Mg-Si-Sn-RE rare earth aluminum alloy also contains 0.1-1.3% by mass of Mg, 0.01-0.2% by mass of Cu, 0.1-0.7% by mass of Si, 0.01-0.3% by mass of Sn, 0.001-0.2% by mass of RE, 0-0.2% by mass of Zn, 0-0.15% by mass of B, 0-0.3% by mass of Nb and 0-0.3% by mass of Ge.
2. The Al-Mg-Si-Sn-RE-based rare earth aluminum alloy according to claim 1, wherein: at least one of the following conditions is satisfied:
the mass ratio of Mg, si and Cu is 1-100:1-60:1, a step of;
the mass ratio of Mg, si and Zn is 1-100:1-40:1, a step of;
the mass ratio of Mg, si and Sn is 1-500:1-300:1, a step of;
the mass ratio of Si to Ge is 1-100:1, a step of;
the mass ratio of Si to Nb is 1-150:1.
3. the Al-Mg-Si-Sn-RE-based rare earth aluminum alloy according to claim 1, wherein: RE is at least one of La, ce, pr, nd, er, sm, Y and Gd, wherein,
when RE is Ce, sm and Er, the mass ratio of Ce, sm and Er is 1-2:0.5-1.5:1, a step of;
when RE is La, Y and Er, the mass ratio of La, Y and Er is 0.5-3:0.5-2:1, a step of;
when RE is Pr, nd and Gd, the mass ratio of Pr, nd and Gd is 1-2:0.1-2.5:1, a step of;
when RE is La and Ce, the mass ratio of La to Ce is 0.5-2:1.
4. the Al-Mg-Si-Sn-RE-based rare earth aluminum alloy according to claim 1, wherein: the Al-Mg-Si-Sn-RE rare earth aluminum alloy contains 0.2-1% by mass of Mg, 0.05-0.1% by mass of Cu, 0.2-0.5% by mass of Si, 0.01-0.1% by mass of Sn, 0.01-0.1% by mass of RE, 0.001-0.1% by mass of Zn, 0.01-0.08% by mass of B, 0.001-0.2% by mass of Nb and 0.001-0.1% by mass of Ge.
5. The Al-Mg-Si-Sn-RE-based rare earth aluminum alloy according to any one of claims 1 to 4, wherein: at least one of the following conditions is satisfied:
the Al-Mg-Si-Sn-RE rare earth aluminum alloy also contains Bi with the mass percent content of 0-0.3 percent;
the Al-Mg-Si-Sn-RE rare earth aluminum alloy also contains 0-0.2% of Sr by mass percent;
the Al-Mg-Si-Sn-RE rare earth aluminum alloy also contains 0-0.2% of Mo by mass percent;
the Al-Mg-Si-Sn-RE rare earth aluminum alloy also contains Be with the mass percent content of 0-0.15 percent;
the Al-Mg-Si-Sn-RE rare earth aluminum alloy also contains 0-0.2 mass percent of Ag;
the Al-Mg-Si-Sn-RE rare earth aluminum alloy also contains Co with the mass percentage content of 0-0.3 percent;
the Al-Mg-Si-Sn-RE rare earth aluminum alloy also contains In with the mass percentage content of 0-0.2 percent;
the Al-Mg-Si-Sn-RE rare earth aluminum alloy also contains Te with the mass percentage content of 0-0.2 percent;
the Al-Mg-Si-Sn-RE rare earth aluminum alloy also contains 0-0.3% of Fe by mass percent.
6. The Al-Mg-Si-Sn-RE-based rare earth aluminum alloy according to claim 5, wherein: at least one of the following conditions is satisfied:
When the Al-Mg-Si-Sn-RE rare earth aluminum alloy contains Bi, the mass ratio of Mg to Bi is 1-500:1, the mass ratio of Cu to Bi is 1-40:1, a step of;
when the Al-Mg-Si-Sn-RE rare earth aluminum alloy contains Sr, co, be and Fe, the mass ratio of Fe, cu and Sr is 0.5-20:0.2-10:1, si, fe and Sr with the mass ratio of 1-200:0.5-10:1, the mass ratio of Fe, RE and Sr is 0.5-15:0.5-10:1, the mass ratio of Fe, co and Sr is 0.5-10:0.5-10:1, the mass ratio of Be, co and Fe is 0.5-20:0.5-10:1, RE, B and Be in a mass ratio of 0.5-20:0.1-10:1, the mass ratio of Fe, RE and B is 1-15:0.1-10:1, a step of;
when the Al-Mg-Si-Sn-RE rare earth aluminum alloy contains Mo, the mass ratio of Si to Mo is 1-100:1, a step of;
when the Al-Mg-Si-Sn-RE rare earth aluminum alloy contains Te, the mass ratio of Te to Sn is 0.01-10:1, the mass ratio of Te to Si is 0.001-1:1, a step of;
when the Al-Mg-Si-Sn-RE rare earth aluminum alloy contains Ag, the mass ratio of Mg to Ag is 2-500:1, the mass ratio of Cu to Ag is 1-80:1, a step of;
when the Al-Mg-Si-Sn-RE rare earth aluminum alloy contains In, the mass ratio of Mg to In is 2-600:1, the mass ratio of Cu to In is 0.2-80:1, the mass ratio of in to B is 0.1-15:1.
7. The Al-Mg-Si-Sn-RE-based rare earth aluminum alloy according to claim 5, wherein: the Al-Mg-Si-Sn-RE rare earth aluminum alloy contains 0.2-1% by mass of Mg, 0.05-0.1% by mass of Cu, 0.2-0.5% by mass of Si, 0.01-0.1% by mass of Sn, 0.01-0.1% by mass of RE, 0.001-0.1% by mass of Zn, 0.01-0.08% by mass of B, 0.001-0.2% by mass of Nb, 0.001-0.1% by mass of Ge, 0.001-0.2% by mass of Bi, 0.001-0.1% by mass of Sr, 0.001-0.1% by mass of Mo, 0.001-0.08% by mass of Be, 0.001-0.1% by mass of Ag, 0.001-0.2% by mass of In, 0.001-0.1% by mass of Te, 0.001-0.1% by mass of Fe, 0.001-0.1% by mass of 0.001-0.2% by mass of Te.
8. A method for producing an Al-Mg-Si-Sn-RE-based rare earth aluminum alloy as claimed in any one of claims 1 to 7, comprising the steps of:
Carrying out primary heating treatment on an aluminum source to obtain aluminum liquid;
adding Mg, cu, si, sn, RE, zn, B, nb and Ge into the aluminum liquid, and performing a second heating treatment to obtain an alloy liquid;
refining and slag skimming are carried out on the alloy liquid, and component and content detection is carried out;
after the components and the content are detected to be qualified, carrying out continuous casting and rolling treatment and quenching treatment on the alloy liquid subjected to the refining treatment and the slag skimming treatment to obtain an aluminum alloy rod;
drawing the quenched aluminum alloy rod to obtain an aluminum alloy wire with the diameter smaller than 5 mm;
and aging the aluminum alloy wire to obtain an Al-Mg-Si-Sn-RE rare earth aluminum alloy, wherein the Al-Mg-Si-Sn-RE rare earth aluminum alloy contains Al, 0.1-1.3% of Mg, 0.01-0.2% of Cu, 0.1-0.7% of Si, 0.01-0.3% of Sn, 0.001-0.2% of RE, 0-0.2% of Zn, 0-0.15% of B, 0-0.3% of Nb and 0-0.3% of Ge.
9. The method for producing an Al-Mg-Si-Sn-RE-based rare earth aluminum alloy according to claim 8, wherein: the method for producing an Al-Mg-Si-Sn-RE rare earth aluminum alloy further comprises a step of adding at least one of Bi, sr, mo, be, ag, co, in, te and Fe to the aluminum liquid.
10. The method for producing an Al-Mg-Si-Sn-RE-based rare earth aluminum alloy according to claim 8, wherein:
the aging treatment is a discontinuous aging process, and the discontinuous aging process comprises the following steps: performing primary low-temperature aging treatment at 100-150deg.C for 1-50h; performing secondary natural aging treatment at 20-60deg.C for 10-24 hr; performing three-stage high-temperature aging treatment at 160-350deg.C for 0.1-150 hr; or (b)
The aging treatment is a discontinuous aging process, and the discontinuous aging process comprises the following steps: performing primary low-temperature aging treatment at 100-150deg.C for 1-50h; performing secondary natural aging treatment at 20-60deg.C for 10-24 hr; performing three-stage high-temperature aging treatment at 160-250deg.C for 0.1-100h; four-stage high-temperature aging treatment is carried out at 250-350 ℃ for 0.1-50h.
11. A heat resistant cable, characterized by: the cable comprises a cable core and an insulating layer coating the cable core, wherein the cable core is made of the Al-Mg-Si-Sn-RE rare earth aluminum alloy as claimed in any one of claims 1-7.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202311540220.9A CN117305668A (en) | 2023-11-17 | 2023-11-17 | Al-Mg-Si-Sn-RE rare earth aluminum alloy, preparation method thereof and heat-resistant cable |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202311540220.9A CN117305668A (en) | 2023-11-17 | 2023-11-17 | Al-Mg-Si-Sn-RE rare earth aluminum alloy, preparation method thereof and heat-resistant cable |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN117305668A true CN117305668A (en) | 2023-12-29 |
Family
ID=89250073
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202311540220.9A Pending CN117305668A (en) | 2023-11-17 | 2023-11-17 | Al-Mg-Si-Sn-RE rare earth aluminum alloy, preparation method thereof and heat-resistant cable |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN117305668A (en) |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN118028666A (en) * | 2024-02-05 | 2024-05-14 | 广东辉煌金属制品有限公司 | Al-Si aluminum alloy, preparation method thereof and heat dissipation structure |
-
2023
- 2023-11-17 CN CN202311540220.9A patent/CN117305668A/en active Pending
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN118028666A (en) * | 2024-02-05 | 2024-05-14 | 广东辉煌金属制品有限公司 | Al-Si aluminum alloy, preparation method thereof and heat dissipation structure |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| JP6691612B2 (en) | High electrical conductivity and heat resistant iron-containing light aluminum wire and its manufacturing process | |
| CN117305668A (en) | Al-Mg-Si-Sn-RE rare earth aluminum alloy, preparation method thereof and heat-resistant cable | |
| CN105734353A (en) | Light high-conductivity and heat-resistant aluminum conductor and preparation method thereof | |
| CN117721352A (en) | Al-Cu aluminum alloy, preparation method thereof and heat-resistant cable | |
| CN116419982A (en) | Aluminum-scandium alloy for bus bar | |
| CN117363932A (en) | Aluminum alloy conductor material, preparation method thereof and wire drawing method | |
| CN117568675A (en) | Al-Mg-Si-Zr-RE rare earth aluminum alloy, preparation method thereof and heat-resistant cable | |
| CN117604343A (en) | Al-Mg-Si-Sb-RE rare earth aluminum alloy, preparation method thereof and heat-resistant cable | |
| CN117448638A (en) | Al-Mg-Si-RE rare earth aluminum alloy, preparation method thereof and heat-resistant cable | |
| CN117568674A (en) | Al-Mg-Si-B-RE rare earth aluminum alloy, preparation method thereof and heat-resistant cable | |
| Srivatsan et al. | Microstructural characterization of two lithium-containing aluminium alloys | |
| CN112430765B (en) | High-conductivity heat-resistant creep-resistant aluminum alloy conductor material and preparation method and application thereof | |
| CN117778833A (en) | Al-Cu-RE rare earth aluminum alloy, preparation method thereof and heat-resistant cable | |
| CN117758115A (en) | Al-Cu aluminum alloy, preparation method thereof and heat-resistant cable | |
| CN117448640A (en) | Al-Cu-RE rare earth aluminum alloy, preparation method thereof and heat-resistant cable | |
| CN117701949A (en) | Al-Fe-Mg-Cu-In-RE rare earth aluminum alloy, preparation method thereof and heat-resistant cable | |
| CN117778834A (en) | Al-Cu aluminum alloy, preparation method thereof and heat-resistant cable | |
| CN112853173A (en) | Rhenium element-added heat-resistant aluminum alloy and preparation method and application thereof | |
| CN117535561A (en) | Al-Fe-Mg-Cu-Zr-RE rare earth aluminum alloy, preparation method thereof and heat-resistant cable | |
| CN117568665A (en) | Al-Fe-Mg-Cu-Co-RE rare earth aluminum alloy, preparation method thereof and heat-resistant cable | |
| CN117488142A (en) | Al-Fe-Mg-Cu-RE rare earth aluminum alloy, preparation method thereof and heat-resistant cable | |
| CN117403110A (en) | Al-Fe-Mg-Cu-Si-RE rare earth aluminum alloy, preparation method thereof and heat-resistant cable | |
| CN117431435A (en) | Al-Fe-Mg-Cu-Sn-RE rare earth aluminum alloy, preparation method thereof and heat-resistant cable | |
| CN117551915A (en) | Al-Fe-Mg-Cu-Zn-RE rare earth aluminum alloy, preparation method thereof and heat-resistant cable | |
| CN117737511A (en) | Al-Fe-Mg-Cu-B-RE rare earth aluminum alloy, preparation method thereof and heat-resistant cable |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination |