CN116904810B - High-strength and high-toughness heat-free aluminum alloy for vacuum integrated die casting and preparation method thereof - Google Patents
High-strength and high-toughness heat-free aluminum alloy for vacuum integrated die casting and preparation method thereof Download PDFInfo
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- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 80
- 238000004512 die casting Methods 0.000 title claims abstract description 22
- 238000002360 preparation method Methods 0.000 title abstract description 7
- 239000000956 alloy Substances 0.000 claims abstract description 70
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 48
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 46
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims abstract description 44
- 239000011701 zinc Substances 0.000 claims abstract description 37
- 239000012535 impurity Substances 0.000 claims abstract description 36
- 239000011777 magnesium Substances 0.000 claims abstract description 35
- 239000011572 manganese Substances 0.000 claims abstract description 27
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 claims abstract description 18
- 229910052725 zinc Inorganic materials 0.000 claims abstract description 18
- 229910052749 magnesium Inorganic materials 0.000 claims abstract description 17
- FYYHWMGAXLPEAU-UHFFFAOYSA-N Magnesium Chemical compound [Mg] FYYHWMGAXLPEAU-UHFFFAOYSA-N 0.000 claims abstract description 15
- 229910052742 iron Inorganic materials 0.000 claims abstract description 15
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 14
- 239000010703 silicon Substances 0.000 claims abstract description 14
- 239000011651 chromium Substances 0.000 claims abstract description 13
- 239000010949 copper Substances 0.000 claims abstract description 13
- 229910052802 copper Inorganic materials 0.000 claims abstract description 8
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 8
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 claims abstract description 7
- 229910052712 strontium Inorganic materials 0.000 claims abstract description 6
- CIOAGBVUUVVLOB-UHFFFAOYSA-N strontium atom Chemical compound [Sr] CIOAGBVUUVVLOB-UHFFFAOYSA-N 0.000 claims abstract description 6
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 claims abstract description 5
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 claims abstract description 5
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 5
- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 claims abstract description 5
- 229910045601 alloy Inorganic materials 0.000 claims description 60
- 238000000034 method Methods 0.000 claims description 28
- 238000005266 casting Methods 0.000 claims description 24
- 239000007788 liquid Substances 0.000 claims description 16
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims description 15
- 238000007872 degassing Methods 0.000 claims description 11
- 238000010438 heat treatment Methods 0.000 claims description 9
- 238000002844 melting Methods 0.000 claims description 7
- 230000008018 melting Effects 0.000 claims description 7
- 229910052757 nitrogen Inorganic materials 0.000 claims description 7
- 238000007670 refining Methods 0.000 claims description 6
- 239000003795 chemical substances by application Substances 0.000 claims description 5
- 238000004519 manufacturing process Methods 0.000 claims description 5
- 238000001914 filtration Methods 0.000 claims description 3
- 229910001873 dinitrogen Inorganic materials 0.000 claims 1
- 238000012360 testing method Methods 0.000 description 31
- 230000008569 process Effects 0.000 description 20
- 230000000052 comparative effect Effects 0.000 description 16
- 239000000463 material Substances 0.000 description 13
- 238000005728 strengthening Methods 0.000 description 12
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 10
- 238000005275 alloying Methods 0.000 description 10
- 230000000694 effects Effects 0.000 description 9
- 230000007797 corrosion Effects 0.000 description 7
- 238000005260 corrosion Methods 0.000 description 7
- 238000001816 cooling Methods 0.000 description 5
- 239000000155 melt Substances 0.000 description 5
- 238000011161 development Methods 0.000 description 4
- 230000018109 developmental process Effects 0.000 description 4
- 238000002347 injection Methods 0.000 description 4
- 239000007924 injection Substances 0.000 description 4
- 239000002994 raw material Substances 0.000 description 4
- 230000009467 reduction Effects 0.000 description 4
- 239000006104 solid solution Substances 0.000 description 4
- 229910052720 vanadium Inorganic materials 0.000 description 4
- 229910021364 Al-Si alloy Inorganic materials 0.000 description 3
- 229910052799 carbon Inorganic materials 0.000 description 3
- 239000007789 gas Substances 0.000 description 3
- 238000000746 purification Methods 0.000 description 3
- 230000035945 sensitivity Effects 0.000 description 3
- 239000010959 steel Substances 0.000 description 3
- LEONUFNNVUYDNQ-UHFFFAOYSA-N vanadium atom Chemical compound [V] LEONUFNNVUYDNQ-UHFFFAOYSA-N 0.000 description 3
- 239000002699 waste material Substances 0.000 description 3
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 description 2
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 2
- 229910000831 Steel Inorganic materials 0.000 description 2
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 2
- 230000032683 aging Effects 0.000 description 2
- 230000009286 beneficial effect Effects 0.000 description 2
- 230000007423 decrease Effects 0.000 description 2
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- 230000006866 deterioration Effects 0.000 description 2
- 238000005516 engineering process Methods 0.000 description 2
- 230000005496 eutectics Effects 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 230000004048 modification Effects 0.000 description 2
- 238000012986 modification Methods 0.000 description 2
- 229910000510 noble metal Inorganic materials 0.000 description 2
- 229910052761 rare earth metal Inorganic materials 0.000 description 2
- 150000002910 rare earth metals Chemical class 0.000 description 2
- 238000004064 recycling Methods 0.000 description 2
- 239000002893 slag Substances 0.000 description 2
- 239000010936 titanium Substances 0.000 description 2
- 229910052719 titanium Inorganic materials 0.000 description 2
- 229910018134 Al-Mg Inorganic materials 0.000 description 1
- 229910000851 Alloy steel Inorganic materials 0.000 description 1
- 229910018467 Al—Mg Inorganic materials 0.000 description 1
- 229920000049 Carbon (fiber) Polymers 0.000 description 1
- 229910001018 Cast iron Inorganic materials 0.000 description 1
- GYHNNYVSQQEPJS-UHFFFAOYSA-N Gallium Chemical compound [Ga] GYHNNYVSQQEPJS-UHFFFAOYSA-N 0.000 description 1
- 229910000861 Mg alloy Inorganic materials 0.000 description 1
- 229910016583 MnAl Inorganic materials 0.000 description 1
- 229910000676 Si alloy Inorganic materials 0.000 description 1
- 229910018594 Si-Cu Inorganic materials 0.000 description 1
- 229910008465 Si—Cu Inorganic materials 0.000 description 1
- 229910000797 Ultra-high-strength steel Inorganic materials 0.000 description 1
- QCWXUUIWCKQGHC-UHFFFAOYSA-N Zirconium Chemical compound [Zr] QCWXUUIWCKQGHC-UHFFFAOYSA-N 0.000 description 1
- 229910009369 Zn Mg Inorganic materials 0.000 description 1
- 229910007573 Zn-Mg Inorganic materials 0.000 description 1
- CSDREXVUYHZDNP-UHFFFAOYSA-N alumanylidynesilicon Chemical compound [Al].[Si] CSDREXVUYHZDNP-UHFFFAOYSA-N 0.000 description 1
- 229910052786 argon Inorganic materials 0.000 description 1
- 239000004917 carbon fiber Substances 0.000 description 1
- 238000012512 characterization method Methods 0.000 description 1
- 239000002131 composite material Substances 0.000 description 1
- 230000002950 deficient Effects 0.000 description 1
- 238000013461 design Methods 0.000 description 1
- 238000009792 diffusion process Methods 0.000 description 1
- 238000011049 filling Methods 0.000 description 1
- 229910052733 gallium Inorganic materials 0.000 description 1
- 230000017525 heat dissipation Effects 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- VNWKTOKETHGBQD-UHFFFAOYSA-N methane Chemical compound C VNWKTOKETHGBQD-UHFFFAOYSA-N 0.000 description 1
- 229910052750 molybdenum Inorganic materials 0.000 description 1
- 238000001556 precipitation Methods 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
- 238000003756 stirring Methods 0.000 description 1
- 230000001502 supplementing effect Effects 0.000 description 1
- 238000004227 thermal cracking Methods 0.000 description 1
- 239000013585 weight reducing agent Substances 0.000 description 1
- 229910052726 zirconium 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
- C22C21/02—Alloys based on aluminium with silicon as the next major constituent
- C22C21/04—Modified aluminium-silicon alloys
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22D—CASTING OF METALS; CASTING OF OTHER SUBSTANCES BY THE SAME PROCESSES OR DEVICES
- B22D17/00—Pressure die casting or injection die casting, i.e. casting in which the metal is forced into a mould under high pressure
- B22D17/14—Machines with evacuated die cavity
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
- C22C1/026—Alloys based on aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
- C22C1/03—Making non-ferrous alloys by melting using master alloys
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/06—Making non-ferrous alloys with the use of special agents for refining or deoxidising
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Manufacture And Refinement Of Metals (AREA)
Abstract
The invention belongs to the technical field of aluminum alloy materials, and relates to a high-strength and high-toughness heat-free aluminum alloy for vacuum integrated die casting and a preparation method thereof, wherein the aluminum alloy comprises the following components: 6.0 to 9.0 weight percent of silicon, 4.0 to 6.0 weight percent of zinc, 0.1 to 0.2 weight percent of magnesium, 0.2 to 0.3 weight percent of manganese, 0.2 to 0.42 weight percent of iron, 0.01 to 0.04 weight percent of strontium, 0.1 to 0.3 weight percent of chromium, less than or equal to 0.6 weight percent of copper, less than or equal to 0.05 weight percent of single element of trace impurities, less than or equal to 0.15 weight percent of the total amount of trace impurities, and the balance of aluminum and unavoidable impurities, wherein the weight ratio of manganese to iron is 0.5 to 1.0, and the weight ratio of zinc to magnesium is 20 to 60. The aluminum alloy can be produced by using regenerated aluminum with higher proportion, the tensile strength is more than or equal to 270MPa, the yield strength is more than or equal to 130MPa, and the elongation after breaking is more than or equal to 10%.
Description
Technical Field
The invention relates to the technical field of aluminum alloy materials, in particular to a high-strength and high-toughness heat-free aluminum alloy for vacuum integrated die casting and a preparation method thereof.
Background
Weight reduction is a major trend in the development of the automotive industry. The common light materials for the car body mainly comprise ultra-high strength steel, aluminum alloy, magnesium alloy, carbon fiber composite material, plastic and the like. The aluminum alloy has the advantages of relatively low cost, excellent performance, small density, corrosion resistance, excellent heat conduction performance, high specific strength and low melting point, and is a preferred material for light weight of automobiles.
At present, lightweight replacement of shells and heat dissipation is already finished by die-casting aluminum alloy, main materials of chassis parts are cast iron and stamping steel, and aluminum alloy is the most important lightweight replacement material. Aluminum alloy castings, particularly die castings, are increasingly developed towards the directions of large-scale, complex and integrated, and the integrated die casting is led by new energy vehicle enterprises such as Tesla and the like, so that development and application processes are increasingly accelerated. The Tesla integrated die-cast rear floor and the front cabin are applied to the Model Y in batches, and the development work of die-casting the lower car body and the whole white car body is also in planning and development.
The large-sized structural member of the automobile has new requirements on the performance of aluminum alloy materials, high strength can be obtained under the non-heat treatment condition, and the elongation of the materials is also higher due to the requirements of self-piercing riveting (SPF) and other connection technologies or the requirements of impact resistance. Conventional die-cast aluminum alloys, such as YL102, do not meet the requirements for toughness; YL101 and YL104 have adequate strength and cannot meet the requirements on toughness; YL112 and YL113 are Al-Si-Cu alloy, 2-4% of copper element is added, the strength is slightly insufficient, the toughness cannot meet the requirement, the material cost is greatly increased, and the alloy is mainly used for heat-resistant castings; YL302 is an Al-Mg series cast aluminum alloy, and the casting performance deviation cannot meet the trend of increasing the size, complicating the design and integrating the aluminum alloy die castings.
Furthermore, it should be noted in particular that: in general, in al—si alloys, cu, mg, and Mn are used as main alloying elements, and Zn is used as an impurity element, and this is because the strengthening effect is not remarkable when the Zn content is low, and the thermal cracking property of the alloy is increased and the corrosion resistance is lowered when the Zn content is too high.
The invention discloses a heat-treatment-free high-strength and toughness die-casting aluminum alloy, a preparation method and a product thereof, wherein the die-casting aluminum alloy comprises the following components in percentage by mass: 7.0 to 10.0wt.% silicon, not more than 0.05wt.% copper, not more than 0.4wt.% magnesium, 0.3 to 0.7wt.% manganese, not more than 0.2wt.% iron, not more than 0.07wt.% zinc, not more than 0.2wt.% titanium, 0.015 to 0.03wt.% strontium, 0.01 to 0.1wt.% vanadium, 0.01 to 0.1wt.% zirconium, the total of other unavoidable impurity elements being not more than 0.25wt.% individually, the remainder being aluminum. The tensile strength is 270-300 MPa, the yield strength is 120-150 MPa, and the elongation is 12-17%.
The low-carbon heat-treatment-free high-pressure casting aluminum alloy disclosed in CN116200635a includes: 6.0 to 7.5 weight percent silicon; 0.15 to 0.3wt% iron; 0.02 to 0.1 weight percent copper; 0.02 to 0.15wt% zinc; 0.4 to 0.6wt% manganese; 0.02 to 0.15% by weight of chromium; 0.1 to 0.4 weight percent magnesium; 0.02 to 0.1wt.% vanadium; 0.02 to 0.1 wt% titanium; 0.01 to 0.03 weight percent gallium; 0.01 to 0.03 weight percent strontium; 0.02 to 0.3 weight percent of rare earth single impurity element up to 0.03 weight percent, and the balance of aluminum.
Although the requirements of the integrated die-casting aluminum alloy on the elongation and strength can be met in the above patent, the upper limit of the iron content and the zinc content is lower, so that the regenerated waste with a smaller proportion cannot be or can be added, and the carbon reduction and emission reduction are not facilitated; the noble metal elements such as vanadium, rare earth and the like are added, so that the cost is high, and the recycling is not facilitated.
Disclosure of Invention
The invention aims to overcome the defects of the prior art, and provides a high-strength and high-toughness heat-free aluminum alloy for vacuum integrated die casting and a preparation method thereof, which solve the problems that the existing heat-free aluminum alloy cannot be added with high proportion of regenerated waste materials, and is not beneficial to carbon reduction and emission reduction; more noble metal elements are added, the cost is high, and the recycling is not facilitated.
Aiming at the characteristics of large size, complex structure, high strength and toughness requirement and difficult heat treatment of a large structural member of an automobile, the invention provides a high strength and toughness heat-free aluminum alloy for vacuum integrated die casting, which belongs to an Al-Si-Zn-Mg system and comprises the following components in percentage by mass:
6.0 to 9.0 weight percent of silicon, 4.0 to 6.0 weight percent of zinc, 0.1 to 0.2 weight percent of magnesium, 0.2 to 0.3 weight percent of manganese, 0.2 to 0.42 weight percent of iron, 0.01 to 0.04 weight percent of strontium, 0.1 to 0.3 weight percent of chromium, less than or equal to 0.6 weight percent of copper, and the balance of aluminum and unavoidable trace impurities, wherein the content of single elements of the trace impurities is less than or equal to 0.05 weight percent, and the total amount of the trace impurities is less than or equal to 0.15 weight percent.
According to the characteristics of the material and the casting and processing requirements, the invention reasonably controls the range of each element, strictly controls the proportion of main alloy elements, and particularly controls the Zn/Mg ratio and Mn/Fe ratio.
Si is the first main alloying element in the high-toughness heat-free aluminum alloy, the content is controlled to be 6.0-9.0wt%, and the toughness is considered while the good mold filling capability of the alloy is ensured. When the silicon content is lower than 6.0wt%, the alloy strength does not reach the peak area, and the alloy casting performance is deviated; when the silicon content is higher than 9.0wt%, the strength increases only a limited amount, and the toughness decreases at a rapid rate. Preferably, the silicon content is 6.4 to 8.2wt%, more preferably 6.4 to 7.5wt%.
In the invention, zn is used as a main alloying element of the Al-Si alloy, and the solid solution strengthening effect of the alloy can be ensured by controlling the reasonable adding proportion, and the negative effect of the alloy is controlled within a certain range.
Specifically, zn is the second main alloying element in the high-strength and high-toughness heat-free aluminum alloy, and the content is controlled to be 4.0-6.0wt%. The solid solubility of Zn in Al is high, and the solid solution strengthening effect is obvious; the Zn-containing alpha solid solution is stable and does not decompose in the casting cooling process; the Zn-containing aluminum alloy can further improve the performance through manual or self-heating aging; the compactness of the alloy is improved, and the demolding is facilitated. Zn and Mg can form MgZnX multi-element strengthening phase, wherein X is one or more than two of Al, si and Mn, the MgZnX multi-element strengthening phase can weaken the diffusion capacity of Mg and prevent Mg 2 The continuous precipitation of Si phase increases the strength of the material and improves the corrosion resistance of the material to a certain extent. Zn can improve the solubility of Cu, so that more Cu is dissolved in a-Al to form supersaturated solid solution, and the strength and plasticity of the material are improved. Preferably, the zinc content is 4.4 to 5.92wt%, preferably 4.89 to 5.80wt%
Mg is the third main alloying element in the high-strength and high-toughness heat-free aluminum alloy, and the content is controlled to be 0.1-0.2wt%. Mg forms Mg with Si 2 The Si strengthening phase can obviously improve the room temperature strength of the alloy, but can obviously reduce the toughness of the alloy; when the Zn/Mg ratio is proper, mg can also form MgZnX multi-element strengthening phase with Zn, and the MgZnX multi-element strengthening phase and Mg 2 The Si phase has better and more remarkable strengthening effect and has lower negative influence on toughness. In the invention, the characteristics of high cooling speed and less casting defects of vacuum integrated die casting are consideredThe cast Al-Si alloy containing Mg, in which the content of Mg is controlled in the range of 0.1 to 0.2wt% and the Zn/Mg ratio is controlled in the range of 20 to 60, preferably 27 to 54, has the potential to further improve the mechanical properties by heat treatment or natural aging.
Mn is the fourth main alloying element in the high-strength and high-toughness heat-free aluminum alloy, the content is controlled to be 0.2-0.3wt%, and the Mn has three main functions in the high-strength and high-toughness heat-free aluminum alloy, namely, the Mn dissolves impurity iron to form (Fe, mn) Al 6 Reducing the harmful influence of iron, preventing die sticking, prolonging the service life of the die, and forming MnAl with aluminum as a strengthening element 6 And fourthly, the corrosion resistance of the alloy is improved. In the high strength and toughness heat-free aluminum alloy of the invention, the Mn content range and Mn/Fe ratio B should be strictly controlled to be 0.5-1.5, preferably 0.6-0.9.
Fe is the fifth alloying element in the high-strength and high-toughness heat-free aluminum alloy, and the content is controlled to be 0.3-0.42wt%. The main function of Fe in the high-strength and high-toughness heat-free aluminum alloy is to prevent the die from sticking and prolong the service life of the die. Considering that Fe-containing has a large negative influence on the toughness of the alloy, the content range and Mn/Fe ratio should be strictly controlled to 0.5 to 1.0.
Sr is a sixth alloying element in the high-strength and high-toughness heat-free aluminum alloy, and the content is controlled to be 0.01-0.04wt%. The Sr has the main functions of modifying eutectic Si phase and Fe-containing phase in the high-strength and high-toughness heat-free aluminum alloy. In the present invention, considering the deterioration effect of the Fe-containing phase, the Sr content is controlled to be in a higher range than that of the ordinary cast aluminum-silicon alloy under the premise of preventing the eutectic Si phase from being excessively deteriorated.
Cr is a seventh alloying element of the high-strength and high-toughness aluminum alloy, and the content is controlled to be 0.1-0.3wt%. Cr has the main function of improving the corrosion resistance of the alloy in the high-strength and high-toughness heat-free aluminum alloy, and has the effect of supplementing and strengthening.
Cu is controlled as an impurity element in the high-strength and high-toughness heat-free aluminum alloy, and the content is less than or equal to 0.6wt%. Cu is used as an impurity element in the high-strength and high-toughness heat-free aluminum alloy, and the upper limit of the content range is obviously improved compared with other impurity elements, mainly because: 1) Within the content range, the existence of trace Cu can play a role in strengthening, improve corrosion resistance and have relatively small influence on toughness; 2) In the actual aluminum ingot production, the application range of selectable waste aluminum pieces is obviously increased.
The invention also provides a preparation method of the high-strength and high-toughness heat-free aluminum alloy for vacuum integrated die casting, which comprises the following steps of:
(1) Preparing raw materials for standby according to the proportion, comprising: aluminum ingots, industrial silicon, pure zinc ingots, pure magnesium ingots, alFe10 intermediate alloys, alMn10 intermediate alloys, alSr10 intermediate alloys, alCr5 intermediate alloys and the like for remelting.
(2) Proportionally adding an aluminum ingot for remelting, industrial silicon, an AlFe10 intermediate alloy, an AlMn10 intermediate alloy and an AlCr5 intermediate alloy into an aluminum melting furnace, controlling the furnace temperature to 770-780 ℃ and heating to fully melt to obtain a first alloy liquid;
(3) Adding pure zinc ingots, pure magnesium ingots and AlSr10 intermediate alloy into the first alloy liquid according to a proportion to obtain a second alloy liquid;
(4) And (3) carrying out on-line degassing, deslagging, filtering and casting on the second alloy liquid to obtain the high-strength and high-toughness heat-free aluminum alloy material.
Further, in the step (4), the temperature of the melting furnace is adjusted to 710-730 ℃ during deslagging, and 3 wt%o refining agent is added for purifying treatment.
Further, in step (4), the refining agent adopts the refining agent disclosed in CN109306412 a.
Further, in step (4), the deaeration is in-furnace deaeration; the furnace temperature is adjusted to 690-710 ℃ when the furnace is deaerated, and nitrogen is used for deaerating the furnace.
Further, in the step (4), the outlet pressure of nitrogen for degassing in the furnace is 0.4-0.6Mpa, and the degassing time is not less than 50min. Further, the rotational speed of the deaerator for online deaeration is 460-500rpm, and the nitrogen flow is 15-25LPM; before on-line degassing, the degassing tank is preheated at 350-450 ℃.
Further, in the step (4), the casting is casting, the casting temperature is 660-690 ℃, and the casting rate is 30-50Hz.
In the aspect of raw material selection, compared with the heat-free alloys such as aluminum C611, the high-strength and toughness heat-free aluminum alloy has the advantages that the upper limit of Fe, zn and Cu elements is improved, so that in the aspect of raw material selection, the higher addition proportion of the regenerated aluminum can be selected; compared with the heat-free alloy such as Rhin Phillips castsail-37, no noble alloying elements such as Mo, V, zr and the like are added. In consideration of the two points, compared with other heat-free aluminum alloys, the high-strength and high-toughness heat-free aluminum alloy has obvious cost advantages while ensuring the service performance.
In the aspect of purification treatment, the method ensures that the aluminum liquid has higher purity by efficiently removing nonmetallic inclusion, oxide and gas in the aluminum liquid, and avoids the generation of defective products in the later stage due to poor purification treatment effect of the gas content in the aluminum liquid.
In the aspect of casting technology, the invention provides proper casting temperature and casting parameters, and ensures that the alloy has uniform and compact grain structure.
The invention has the advantages and beneficial effects that:
the high-strength and high-toughness aluminum alloy material is mainly applied to the production of large-size, complex-structure and high-strength and difficult-to-heat-treat automobile large-size structural parts, and can meet the production requirements of the automobile structural parts with the tensile strength of more than or equal to 270Mpa, the yield strength of more than or equal to 130Mpa and the elongation of more than or equal to 10 percent under the condition of no need of heat treatment.
Drawings
FIG. 1 is a graph showing the MgZnX multi-component reinforced phase scanning characterization (test condition A) of the high-strength and high-toughness heat-free aluminum alloy ingot prepared in the embodiment 1 of the invention.
Detailed Description
The invention will now be described with reference to specific examples, which are intended to be illustrative only and not limiting in any way.
Example 1
The high-strength and high-toughness heat-free aluminum alloy cast ingot is prepared according to the following steps:
the raw materials and the addition proportion are as follows: aluminum ingot Al99.70 and 80.74wt percent for remelting; 3303 commercial silicon, 6.48wt%; pure zinc ingot, 4.91wt%; pure magnesium ingot Mg9995,0.19wt%; 2wt% of an AlFe10 intermediate alloy; 3.2wt% of AlMn10 master alloy; 0.3wt% of AlSr10 intermediate alloy, and 2.2wt% of AlCr5 intermediate alloy.
Proportionally adding aluminum ingots Al99.70 and 3303 industrial silicon, alFe10 intermediate alloy, alMn10 intermediate alloy and AlCr5 intermediate alloy for remelting into an aluminum melting furnace, controlling the furnace temperature to 770-780 ℃ and heating to fully melt to obtain a first alloy liquid; adding pure zinc ingots, pure magnesium ingots Mg9995 and AlSr10 intermediate alloy into the first alloy liquid according to a proportion to obtain a second alloy liquid; refining the second alloy liquid, degassing in a furnace, filtering and casting to obtain the high-strength and high-toughness heat-free aluminum alloy material, wherein the specific process comprises the following steps of: the furnace temperature is controlled at 720 ℃, and 3 wt%o refining agent is added for purification treatment; the outlet pressure of nitrogen for degassing in the furnace is 0.5Mpa, and the degassing time is 50min; the rotational speed of the deaerator for online deaeration is 480rpm, and the nitrogen flow is 15LPM; before on-line degassing, the degassing tank is preheated at 350 ℃. The casting temperature was 680℃and the casting rate was 40Hz.
The composition is as follows: si:6.48wt%; zn:4.91wt%; mg:0.18wt%; mn:0.32wt%; fe:0.30wt%; sr:0.022wt%; 0.11wt% of Cr and the balance of Al.
The high-strength and high-toughness heat-free alloy material prepared by the method is subjected to vacuum die casting according to the following method and process, and the mechanical properties are tested.
(1) Adding the high-strength and high-toughness heat-free alloy material into an aluminum melting furnace of a die casting machine, quickly heating to 700-720 ℃, preserving heat for 30min after the alloy is melted, introducing argon and continuously stirring the melt for 30min, and removing gas in the melt to homogenize the components; standing for 10min after slag skimming, and controlling the temperature of the aluminum liquid at 720 ℃.
(2) Vacuum die casting is carried out on the melt after slag skimming, the casting temperature of the melt is 720 ℃, the die temperature is 180 ℃, the die material is H13 die steel, the multistage low-speed injection speed is 0.15m/s-0.18m/s-0.2m/s, the high-speed injection speed is 3m/s, a Ai Jiaya vacuum machine is adopted for vacuumizing, and the vacuum degree of a die cavity is 1-3KPa under the vacuum condition.
Examples 2 to 5
A series of aluminum alloys were prepared using substantially the same procedure as in example 1, with specific compositions and contents shown in Table 1 (the balance being aluminum and unavoidable impurities, not shown). The prepared aluminum alloy was vacuum die-cast using the same process as in example 1, and the test bars were subjected to mechanical property test, and the results are shown in table 1.
TABLE 1
Examples 1-5 the mechanical properties of the prepared aluminum alloy test bars were tested by changing the content of each component, and the results show that when the content of each component, the Zn/Mg ratio and the Mn/Fe ratio were all within the control range, the tensile strength, the yield strength and the elongation after breaking of the prepared aluminum alloy test bars were all in the alloy strength peak area, and the comprehensive properties were excellent.
Comparative example 1
The difference from example 1 was only that the content of Fe was changed to 0.75wt%, the Mn/Fe ratio was 0.37, and other components and contents were shown in Table 2 (the balance being aluminum and unavoidable impurities, not shown), the aluminum alloy obtained was vacuum die-cast by the same process as in example 1, and the test bars were subjected to mechanical properties, and the results are shown in Table 2.
Comparative example 2
The difference from example 1 was only that the content of Fe was changed to 0.2wt%, the Mn/Fe ratio was 1.4, and other components and contents were shown in Table 2 (the balance being aluminum and unavoidable impurities, not shown), the aluminum alloy obtained was vacuum die-cast by the same process as in example 1, and the test bars were subjected to mechanical properties, and the results are shown in Table 2.
Comparative example 3
The difference from example 1 was only that the Mn content was changed to 0.12wt%, the Mn/Fe ratio was 0.4, and the other components and contents were shown in Table 2 (the balance being aluminum and unavoidable impurities, not shown), the aluminum alloy obtained was vacuum die-cast by the same process as in example 1, and the test bars were subjected to mechanical properties, and the results are shown in Table 2.
Comparative example 4
The difference from example 1 was only that the Mn content was changed to 0.55wt%, the Mn/Fe ratio was 1.83, and other components and contents were shown in Table 2 (the balance being aluminum and unavoidable impurities, not shown), the aluminum alloy obtained was vacuum die-cast by the same process as in example 1, and the test bars were subjected to mechanical properties, and the results are shown in Table 2.
Comparative example 5
The difference from example 1 was only that the Mn content was changed to 0.4wt%, the Mn/Fe ratio was 1.3, and other components and contents were shown in Table 2 (the balance being aluminum and unavoidable impurities, not shown), and the produced aluminum alloy was vacuum die-cast by the same process as in example 1, and the test bars were subjected to mechanical properties, and the results are shown in Table 2.
Comparative example 6
The difference from example 1 was only that the Mn content was changed to 0.22wt%, the Fe content was 0.5wt%, the Mn/Fe ratio was 0.44, and the other components and contents were as shown in Table 2 (the balance being aluminum and unavoidable impurities, not shown), and the produced aluminum alloy was vacuum die-cast by the same process as in example 1, and the test bars were subjected to mechanical properties, the results of which are shown in Table 2.
The aluminum alloy material with the elongation after break lower than 10% cannot be applied to the production of automobile structural parts with large size, complex structure and higher strength and toughness requirements, and the elongation after break is 12.61% and exceeds 10% when the Mn/Fe ratio B is 1.6, but the addition amount of Fe is 0.2wt%, the proportion of the renewable aluminum which can be added is low, and the material cost is increased.
Comparative example 7
The difference from example 1 was only that the Zn content was changed to 3.5wt%, the Zn/Mg ratio was 19.4, and the other components and contents were as shown in Table 2 (the balance being aluminum and unavoidable impurities, not shown), and the produced aluminum alloy was vacuum die-cast by the same process as in example 1, and the test bars were subjected to mechanical properties test, the results of which are shown in Table 2.
Comparative example 8
The difference from example 1 was only that the Zn content was changed to 6.5wt%, the Zn/Mg ratio was 36, and the other components and contents were as shown in Table 2 (the balance being aluminum and unavoidable impurities, not shown), the produced aluminum alloy was vacuum die-cast by the same process as in example 1, and the test bars were subjected to mechanical properties test, and the results are shown in Table 2.
Comparative example 9
The difference from example 1 was only that the content of Mg was changed to 0.05wt%, the Zn/Mg ratio was 98.2, and other components and contents were shown in table 2 (the balance of aluminum and unavoidable impurities, not shown), and the produced aluminum alloy was vacuum die-cast by the same process as in example 1, and the test bars were subjected to mechanical properties test, and the results are shown in table 2.
Comparative example 10
The difference from example 1 was only that the content of Mg was changed to 0.25wt%, the Zn/Mg ratio was 19.6, and other components and contents were shown in table 2 (the balance of aluminum and unavoidable impurities, not shown), and the produced aluminum alloy was vacuum die-cast by the same process as in example 1, and the test bars were subjected to mechanical properties test, and the results are shown in table 2.
Comparative example 11
The difference from example 1 was only that the Si content was changed to 5.8wt%, the other components and contents were as shown in Table 2 (the balance being aluminum and unavoidable impurities, not shown), the aluminum alloy obtained was vacuum die-cast by the same process as in example 1, and the test bars were subjected to mechanical properties, and the results are shown in Table 2. The influence of mechanical properties is small after the Si content is reduced, but the fluidity of the alloy is obviously reduced, and large-scale complex parts cannot be formed.
Comparative example 12
The difference from example 1 was only that the Si content was changed to 9.7wt%, the other components and contents were as shown in Table 2 (the balance being aluminum and unavoidable impurities, not shown), the aluminum alloy obtained was vacuum die-cast by the same process as in example 1, and the test bars were subjected to mechanical properties, and the results are shown in Table 2.
The invention strictly controls the Si content to be 6.0-9.0%, and compared with examples 11-12, the results of the mechanical property test of the aluminum alloy test bar prepared by changing the Si content show that when the Si content is lower than 6.0%, the mechanical property influence is not great, but the alloy fluidity is obviously reduced, and large-scale complex parts cannot be formed; if the Si content is more than 9.0%, the strength increases only a limited amount, and the toughness decreases at a rapid rate.
Comparative example 13
The difference from example 1 was only that the Sr content was changed to 0.008wt%, and the other components and contents are shown in Table 2 (the balance being aluminum and unavoidable impurities, not shown), and the produced aluminum alloy was vacuum die-cast by the same procedure as in example 1, and the test bars were subjected to mechanical properties, and the results are shown in Table 2. The reduced Sr content results in insufficient deterioration and reduced performance.
Comparative example 14
The difference from example 1 was only that the Sr content was changed to 0.045wt%, and the other components and contents are shown in Table 2 (the balance being aluminum and unavoidable impurities, not shown), and the produced aluminum alloy was vacuum die-cast by the same process as in example 1, and the test bars were subjected to mechanical properties, and the results are shown in Table 2. The Sr content is higher than 0.04%, which mainly leads to an increase in alloy cost.
Comparative example 15
The difference from example 1 was only that the Cr content was changed to 0.05wt%, the other components and contents were as shown in Table 2 (the balance being aluminum and unavoidable impurities, not shown), the aluminum alloy obtained was vacuum die-cast by the same process as in example 1, and the test bars were subjected to mechanical properties, and the results are shown in Table 2. Cr content less than 0.1% has less effect on the properties, but the corrosion resistance of the alloy is reduced.
Comparative example 16
The difference from example 1 was only that the Cr content was changed to 0.35wt%, the other components and contents were as shown in Table 2 (the balance being aluminum and unavoidable impurities, not shown), the aluminum alloy obtained was vacuum die-cast by the same process as in example 1, and the test bars were subjected to mechanical properties, and the results are shown in Table 2. The Cr content is higher than 0.3%, the elongation after break is 9.13%, and the Cr content is obviously reduced.
TABLE 2
For large complex structural members, the cooling speed is different because the thicknesses of different parts are different. If the cold speed sensitivity index is larger, the performance difference of different parts is larger. The present invention thus performs a cold rate sensitivity test under two conditions:
test condition a: and casting square bars by weight, wherein the preheating temperature of a die is 150 ℃ and the casting temperature is 700 ℃. The tensile bar was sampled from the center of the square bar at a cooling rate of about 5-10 c/sec.
Test condition B: and (3) vacuum die casting a test bar with the diameter of 6.3 mm. The casting temperature of the melt is 720 ℃, the mold temperature is 180 ℃, the mold material is H13 mold steel, the multistage low-speed injection speed is 0.15m/s-0.18m/s-0.2m/s, the high-speed injection speed is 3m/s, a Ai Jiaya vacuum machine is adopted for vacuumizing, and the vacuum degree of the mold cavity is 1-3Kpa under the vacuum condition. The cooling rate is about 30-40 deg.c/sec.
The results are shown in Table 3, compared with the aluminum C611 alloy most commonly used in the current integral die casting.
TABLE 3 Table 3
As can be seen from Table 3, the alloy of example 1 has a tensile strength and yield strength variation of 17.2% and 10.4%, respectively, which are much lower than 43.8% and 35.4% for the C611 aluminum alloy, compared to the low cold speed condition A and the high cold speed condition B. This shows that the alloy of example 1 has lower sensitivity to cold speed, and when the alloy is used for producing large complex structural members with different wall thicknesses, the uniformity of the performance of the parts at different positions is easier to ensure.
The foregoing describes only exemplary embodiments or examples of the present invention and is not intended to limit the present invention. The present invention is susceptible to various modifications and changes by those skilled in the art. Any modification, equivalent replacement, improvement, etc. that comes within the spirit and principle of the present invention are included in the scope of the claims of the present application.
Claims (9)
1. A high strength and toughness heat-free aluminum alloy for vacuum integrated die casting, characterized by comprising, relative to the total weight of the aluminum alloy: 6.0 to 9.0 weight percent of silicon, 4.4 to 6.0 weight percent of zinc, 0.1 to 0.2 weight percent of magnesium, 0.2 to 0.3 weight percent of manganese, 0.2 to 0.42 weight percent of iron, 0.01 to 0.04 weight percent of strontium, 0.1 to 0.3 weight percent of chromium, less than or equal to 0.6 weight percent of copper, less than or equal to 0.05 weight percent of single element of trace impurities, less than or equal to 0.15 weight percent of the total amount of trace impurities, and the balance of aluminum and unavoidable impurities, wherein the weight ratio of manganese to iron is 0.5 to 1.0, the weight ratio of zinc to magnesium is 20 to 60, and Mg to Zn form MgZnX multi-element reinforced phase, wherein X is one or more than two of Al, si and Mn.
2. The heat-free aluminum alloy according to claim 1, wherein the zinc is 4.89 to 5.92wt%.
3. The heat-free aluminum alloy according to claim 2, wherein the weight ratio of zinc to magnesium is 27-54.
4. A heat-free aluminium alloy according to claim 3, wherein the weight ratio of manganese to iron is 0.6-0.9.
5. The heat-free aluminum alloy of claim 1, comprising, relative to the total weight of the aluminum alloy: 6.40 to 7.34 weight percent of silicon, 4.89 to 5.92 weight percent of zinc, 0.11 to 0.18 weight percent of magnesium, 0.22 to 0.29 weight percent of manganese, 0.30 to 0.42 weight percent of iron, 0.021 to 0.030 weight percent of strontium, 0.11 to 0.12 weight percent of chromium, less than or equal to 0.6 weight percent of copper, less than or equal to 0.05 weight percent of single element of trace impurities, less than or equal to 0.15 weight percent of the total amount of trace impurities, and the balance of aluminum and unavoidable impurities, wherein the weight ratio of manganese to iron is 0.6 to 0.9, and the weight ratio of zinc to magnesium is 27 to 54.
6. A method for producing an aluminum alloy according to any one of claims 1 to 5, comprising the steps of:
proportionally adding an aluminum ingot for remelting, industrial silicon, an AlFe10 intermediate alloy, an AlMn10 intermediate alloy and an AlCr5 intermediate alloy into an aluminum melting furnace, controlling the furnace temperature to 770-780 ℃ and heating to fully melt to obtain a first alloy liquid;
adding pure zinc ingots, pure magnesium ingots and AlSr10 intermediate alloy into the first alloy liquid according to a proportion to obtain a second alloy liquid;
and (3) carrying out on-line degassing, deslagging, filtering and vacuum casting on the second alloy liquid to obtain the high-strength and high-toughness heat-free aluminum alloy material.
7. The method according to claim 6, wherein the temperature of the melting furnace is adjusted to 710-730 ℃ during deslagging, and 3wt% refining agent is added for purifying.
8. The method according to claim 6, wherein the furnace is deaerated by adjusting the temperature of the furnace to 690-710 ℃ and using nitrogen gas.
9. The method of claim 8, wherein the deaerated nitrogen outlet pressure is 0.4-0.6MPa and the nitrogen flow is 15-25LPM.
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| CN109468511A (en) * | 2018-12-29 | 2019-03-15 | 广州立中锦山合金有限公司 | A kind of aluminum alloy materials bored for deep-well |
| CN113755722A (en) * | 2021-09-22 | 2021-12-07 | 隆达铝业（顺平）有限公司 | High-strength and high-toughness heat-treatment-free aluminum alloy material and preparation method thereof |
| US20230052639A1 (en) * | 2020-01-21 | 2023-02-16 | Novelis Inc. | Aluminum alloys and coated aluminum alloys with high corrosion resistance and methods of making the same |
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| CN109468511A (en) * | 2018-12-29 | 2019-03-15 | 广州立中锦山合金有限公司 | A kind of aluminum alloy materials bored for deep-well |
| US20230052639A1 (en) * | 2020-01-21 | 2023-02-16 | Novelis Inc. | Aluminum alloys and coated aluminum alloys with high corrosion resistance and methods of making the same |
| CN113755722A (en) * | 2021-09-22 | 2021-12-07 | 隆达铝业（顺平）有限公司 | High-strength and high-toughness heat-treatment-free aluminum alloy material and preparation method thereof |
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