CN117535565B - High-conductivity die-casting aluminum alloy based on dispersion strengthening and preparation method and application thereof - Google Patents
High-conductivity die-casting aluminum alloy based on dispersion strengthening and preparation method and application thereof Download PDFInfo
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- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 64
- 238000004512 die casting Methods 0.000 title claims abstract description 57
- 238000002360 preparation method Methods 0.000 title claims abstract description 12
- 239000006185 dispersion Substances 0.000 title claims description 12
- 238000005728 strengthening Methods 0.000 title claims description 10
- 239000000956 alloy Substances 0.000 claims abstract description 46
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 45
- 239000012535 impurity Substances 0.000 claims abstract description 16
- 229910052782 aluminium Inorganic materials 0.000 claims description 39
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims description 39
- 238000001816 cooling Methods 0.000 claims description 21
- 239000007788 liquid Substances 0.000 claims description 21
- 239000000843 powder Substances 0.000 claims description 21
- 238000010438 heat treatment Methods 0.000 claims description 18
- 229910052742 iron Inorganic materials 0.000 claims description 18
- 229910052759 nickel Inorganic materials 0.000 claims description 15
- 238000002347 injection Methods 0.000 claims description 12
- 239000007924 injection Substances 0.000 claims description 12
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 12
- 229910052691 Erbium Inorganic materials 0.000 claims description 10
- 239000002994 raw material Substances 0.000 claims description 8
- 238000004519 manufacturing process Methods 0.000 claims description 7
- 229910052726 zirconium Inorganic materials 0.000 claims description 7
- XKRFYHLGVUSROY-UHFFFAOYSA-N Argon Chemical compound [Ar] XKRFYHLGVUSROY-UHFFFAOYSA-N 0.000 claims description 6
- 238000009826 distribution Methods 0.000 claims description 6
- 239000007789 gas Substances 0.000 claims description 6
- 229910052746 lanthanum Inorganic materials 0.000 claims description 6
- 229910002555 FeNi Inorganic materials 0.000 claims description 5
- 239000000498 cooling water Substances 0.000 claims description 5
- 230000005496 eutectics Effects 0.000 claims description 5
- 239000011261 inert gas Substances 0.000 claims description 5
- 238000001556 precipitation Methods 0.000 claims description 5
- 229910018084 Al-Fe Inorganic materials 0.000 claims description 4
- 229910018192 Al—Fe Inorganic materials 0.000 claims description 4
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 claims description 4
- 238000001856 aerosol method Methods 0.000 claims description 4
- 238000004458 analytical method Methods 0.000 claims description 4
- 239000002826 coolant Substances 0.000 claims description 4
- 238000007670 refining Methods 0.000 claims description 4
- 229910018580 Al—Zr Inorganic materials 0.000 claims description 3
- 229910052786 argon Inorganic materials 0.000 claims description 3
- 238000007872 degassing Methods 0.000 claims description 3
- 238000007723 die pressing method Methods 0.000 claims description 3
- 230000003116 impacting effect Effects 0.000 claims description 3
- 229910001338 liquidmetal Inorganic materials 0.000 claims description 3
- 239000000155 melt Substances 0.000 claims description 3
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- 238000000034 method Methods 0.000 description 11
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- 239000002184 metal Substances 0.000 description 3
- 230000004048 modification Effects 0.000 description 3
- 238000012986 modification Methods 0.000 description 3
- 229910000510 noble metal Inorganic materials 0.000 description 3
- 229910052761 rare earth metal Inorganic materials 0.000 description 3
- 230000005540 biological transmission Effects 0.000 description 2
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- 150000002910 rare earth metals Chemical class 0.000 description 2
- 239000007787 solid Substances 0.000 description 2
- 239000000243 solution Substances 0.000 description 2
- 235000014347 soups Nutrition 0.000 description 2
- 229910052720 vanadium Inorganic materials 0.000 description 2
- 229910052684 Cerium Inorganic materials 0.000 description 1
- 229910000990 Ni alloy Inorganic materials 0.000 description 1
- 229910001093 Zr alloy Inorganic materials 0.000 description 1
- 230000002238 attenuated effect Effects 0.000 description 1
- 238000000498 ball milling Methods 0.000 description 1
- 230000000903 blocking effect Effects 0.000 description 1
- 229910052793 cadmium Inorganic materials 0.000 description 1
- 229910052799 carbon Inorganic materials 0.000 description 1
- 239000000969 carrier Substances 0.000 description 1
- 229910052804 chromium Inorganic materials 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 238000012864 cross contamination Methods 0.000 description 1
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Classifications
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
-
- 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
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22F—WORKING METALLIC POWDER; MANUFACTURE OF ARTICLES FROM METALLIC POWDER; MAKING METALLIC POWDER; APPARATUS OR DEVICES SPECIALLY ADAPTED FOR METALLIC POWDER
- B22F9/00—Making metallic powder or suspensions thereof
- B22F9/02—Making metallic powder or suspensions thereof using physical processes
- B22F9/06—Making metallic powder or suspensions thereof using physical processes starting from liquid material
- B22F9/08—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying
- B22F9/082—Making metallic powder or suspensions thereof using physical processes starting from liquid material by casting, e.g. through sieves or in water, by atomising or spraying atomising using a fluid
-
- 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
- C22C1/04—Making non-ferrous alloys by powder metallurgy
- C22C1/0408—Light metal alloys
- C22C1/0416—Aluminium-based alloys
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- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Materials Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Powder Metallurgy (AREA)
- Conductive Materials (AREA)
Abstract
The invention relates to a dispersion-reinforced high-conductivity die-casting aluminum alloy, a preparation method and application thereof, wherein the alloy comprises Fe：0.05-3.0wt％;Ni：0.05-2.5wt％;Zr：0.005-0.15wt%;Er：0.005-0.10wt％;La：0.005-0.10wt％;Er+La：≤0.1wt%;Si：≤0.15wt％;Mn：≤0.05wt％;B：0.01-0.1wt％;Ti+Cr+V≤0.05wt％; weight percent of the sum of the rest impurities, which is controlled below 0.5 weight percent, and the balance is Al; and the mass ratio of Fe to (Ni+Zr) is controlled to be 1-12:2. The die-casting aluminum alloy prepared by the invention has excellent conductivity, excellent elongation and good high-temperature mechanical property.
Description
Technical Field
The invention relates to the technical field of die-casting aluminum alloy, in particular to a high-conductivity die-casting aluminum alloy and a preparation method and application thereof.
Background
The aluminum alloy is not negligible in the modern industry and the technical field, and the light weight and high strength of the aluminum alloy make the aluminum alloy an ideal material widely applied to the aerospace, automobile manufacturing, building and electronic industries. The wide application of the aluminum alloy not only meets the requirements of the modern society on light weight, high strength and corrosion resistance, but also plays an important role in improving the product performance, saving energy and reducing emission, promoting technological progress and the like, and becomes one of the key materials indispensable in the industrial and technological fields at present.
In the field of new energy automobiles, aluminum is widely applied to the production of cast aluminum rotors, and at present, pure aluminum is used as a main material to be matched with a die casting process, so that better performance can be realized. However, due to the defects of low strength of pure aluminum materials and unavoidable die casting technology, the actual rotor parts have poor electric conductivity and low high-temperature strength, and the application of the rotor is limited. Although various other metal elements can be added into the aluminum liquid to improve the mechanical performance and the die casting performance of the aluminum rotor, according to the different added elements, the obvious deterioration of conductivity and extensibility and the increase of cost can be caused, and the requirements of low cost, high conductivity and high performance are difficult to meet simultaneously.
The alloy of an Al-Fe type motor rotor disclosed in patent CN114959368B and a preparation method and application thereof are characterized in that the composition of the alloy is 0.5-1.5wt% of Fe and the balance of Al. The patent increases the yield strength of the material by adding a single Fe element, but the addition form of Fe is single, and it is known that the addition of Fe element in aluminum deteriorates the elongation and conductivity of the material, and although the patent is improved by a multi-stage heat treatment process, the risk of defects such as bubbles and bulges is certainly increased in the actual heat treatment process, the yield is reduced, and the cost is increased.
Patent application CN112567059a discloses a cast aluminum alloy comprising 4wt% to 6wt% Ni, from 0.2wt% to 0.8wt% Fe,0.01wt% to 0.1wt% Ti, less than 1.0wt% impurities, the remainder being Al. According to the invention, the hardness and yield strength of the material are improved through the addition of high Ni, the die casting performance of the material is improved through the Fe content, and the grain refinement is realized through the addition of Ti. The material of the invention ensures the mechanical property of the material through high content of Ni, and Ni belongs to an expensive element, and has the advantages of huge raw material cost and high price, thus being difficult to obtain economic benefit for enterprises.
Patent application CN116904805A discloses a high-conductivity high-voltage die-casting aluminum alloy and a preparation method thereof, wherein the high-conductivity high-voltage die-casting aluminum alloy comprises (1-7)% Ni; (0.1-5.5)% Fe; (0.01-1.5)% Cd; (0.1-0.8)% Mn; (0.1-1.2)% B, and one or more of the following unavoidable control elements, the weight percentages being: zr is less than or equal to 0.15 percent; ti is less than or equal to 0.15%; v is less than or equal to 0.15 percent; cr is less than or equal to 0.15%; RE is less than or equal to 0.15 percent, and the balance is aluminum. According to the invention, through the combined addition of Ni and Fe, the mechanical property of the material is improved, the Fe phase is changed into a block shape from a needle shape, the elongation is improved, the corrosion resistance is improved by Cd element, the problem of die sticking is solved by Mn, and B is used for refining grains. However, the invention contains 0.1-0.8wt% of Cd, and the Cd element is a definitely specified harmful element in Rohs2.0, which does not meet the requirements of various manufacturers at the present stage and does not meet the environmental standards, and the popularization in the market is very limited. Secondly, the addition of Mn in the invention can improve the die casting performance, but the addition of Mn can greatly deteriorate the conductivity of the material, which is not beneficial to the improvement of the conductivity. Meanwhile, the Ni in the components is excessively high in proportion, the cost is high, and the economic benefit of the material is low.
Patent application CN116463529A discloses a high-conductivity high-heat-resistance die-casting aluminum alloy for new energy automobiles and a preparation method thereof, wherein the die-casting aluminum alloy comprises the following raw materials in percentage by weight: fe is less than or equal to 0.25wt percent, si is less than or equal to 0.2wt percent, the weight ratio of Fe to Si is 0.5～2;Ni：2.0～5.0wt％,Zr：0.05～0.5wt％,B：0.05～0.2wt％,Mg≤0.2wt％,Cu≤0.2wt％,Er：0.005～0.1wt％,Ce：0.005～0.1wt％;, the balance is Al and unavoidable impurities, and the sum of the weight percentages of the impurities is controlled below 0.1wt percent; compared with the traditional adding mode, the amorphous powder is added more uniformly, so that defects introduced during adding are reduced, slag inclusion or undissolved particle phases are not easy to generate, the purity of the aluminum liquid is improved, impurity elements are reduced to be dissolved in an aluminum matrix in a solid mode, and the electrical conductivity and the thermal conductivity of the material are improved; reducing the adverse factors of the electrical conductivity and mechanical property of the alloy. The main component of the invention is high Ni noble metal, the alloy has obvious limitation on the content of Fe element, which means that the alloy cannot be reinforced by Fe, and the Fe element is more favorable for improving the high-temperature strength, especially the yield strength, compared with the Ni element, in order to meet the high-temperature mechanical property requirement, the invention needs to additionally add high-content noble metal Ni to meet the property requirement, the higher the property requirement is, the higher the content of noble metal Ni is, the production cost is huge, the economic benefit is low, the enterprise burden is heavy, and the application of the technology is restricted.
Disclosure of Invention
In view of the above problems, an object of the present invention is to provide a die-casting aluminum alloy material suitable for highly conductive products, which overcomes the above-mentioned drawbacks of the prior art.
The aim of the invention can be achieved by the following technical scheme: a die-casting aluminum alloy based on dispersion strengthening and high conductivity comprises Fe：0.05-3.0wt％;Ni：0.05-2.5wt％;Zr：0.005-0.15wt%;Er：0.005-0.10wt％;La：0.005-0.10wt％;Er+La：≤0.1wt%;Si：≤0.15wt％;Mn：≤0.05wt％;B：0.01-0.1wt％;Ti+Cr+V≤0.05wt％; weight percent of the sum of the rest impurities controlled below 0.5 weight percent, and the balance of Al; and the mass ratio of Fe to (Ni+Zr) is controlled to be 1-12:2.
Preferably, the alloy comprises the following components ： Fe：0.10-2.3wt％;Ni：0.1-1.5wt％;Zr：0.005-0.10wt%;Er：0.005-0.08wt％;La：0.005-0.05％;Er+La：≤0.1wt%;Si：0.06-0.12wt％;Mn：0.005-0.05wt％; B：0.01wt％-0.05wt％;Ti+Cr+V≤0.03wt％; in percentage by mass, the sum of the weight percentages of the rest impurities is controlled below 0.5 weight percent, and the balance is Al; and the mass ratio of Fe to (Ni+Zr) is controlled to be 1.8-6:1.
Further, the mass ratio of B to (Ti+Cr+V+Mn) is controlled to be 1-10:2.
Further, the Er and La are added in a mode of Al-Er-La nanocrystalline, and the Al-Er-La nanocrystalline is prepared by a cryogenic aerosol method. The specific preparation method of the Al-Er-La nanocrystalline comprises the following steps:
step 1: mixing the commercial Al-Er and Al-La intermediate powder alloy according to a proportion;
Step 2: heating the alloy powder with specific components at 850-1100 ℃ to enable the alloy powder to be in a molten state, taking inert gas as a protecting and cooling medium, forming tiny liquid drops after impacting the molten liquid flow through air flow and cooling, and forming nanocrystalline powder after cooling, wherein the prepared alloy powder mainly comprises nanocrystalline;
Step 3: and (3) carrying out press-bonding on the collected alloy powder to obtain the blocky Al-Er-La nanocrystalline alloy.
The inert gas in the step2 is one of argon or nitrogen, and the gas flow pressure is 0.7-3.5MPa.
The invention also provides a preparation method of the high-conductivity die-casting aluminum alloy based on dispersion strengthening, which comprises the following steps:
Step S1: weighing pure aluminum raw materials, al-Fe, al-Ni, al-Zr, al-B intermediate alloy and Al-Er-La nanocrystalline alloy according to mass ratio; because the materials inevitably contain Si, mn, ti, cr, V and other impurities, the Si in the alloy is realized by the material selection control: less than or equal to 0.15 weight percent, mn: less than or equal to 0.05wt percent; the sum of the weight percentages of the rest impurities is controlled below 0.5 weight percent;
step S2: putting pure aluminum raw materials into a heating furnace, heating to 680 ℃ to obtain molten aluminum liquid, and standing and preserving heat for 20-30min after the aluminum liquid metal is completely melted;
step S3: heating to 780 ℃, and adding Al-Fe, al-Ni, al-B and Al-Zr into the aluminum liquid according to a proportion until the aluminum liquid is completely dissolved;
step S4: cooling to 750 ℃, adding Al-Er-La nanocrystalline, and preserving heat for 20-30 min;
Step S5: cooling to 720 ℃, preserving heat for 15-20min, and then degassing and refining;
Step S6: and (3) pouring the small sample for component analysis, and sending the melt into forming equipment for forming after the small sample is qualified to obtain the high-conductivity die-casting aluminum alloy.
The invention also provides an application of the dispersion-reinforced high-conductivity die-casting aluminum alloy, which carries out high-pressure die-casting molding on the obtained die-casting aluminum alloy to obtain a die-casting aluminum alloy product, and specifically comprises the following steps:
Melting the aluminum alloy casting again at 720-740 ℃, preserving heat, introducing protective gas to isolate the casting from air during heat preservation, injecting injection into a die casting mold, vacuumizing, and performing vacuum die pressing to obtain the die casting aluminum alloy product.
Further, the injection adopts a filling mode of firstly low speed and then high speed, the injection low speed is controlled to be 0.10-0.25 m/s, the temperature of the die casting die is controlled by an oil temperature machine, a water temperature machine and a water cooling machine in a co-operation mode, wherein the oil temperature machine is set to be 210-250 ℃, the water temperature machine is set to be 100-140 ℃, the cooling water is kept at a constant temperature of 15-30 ℃, the point cooling water passes through a die core point cooling pipeline under the water pressure of 0.8-1 MPa, and the pressure is maintained for 5-10 seconds after the injection is finished;
Further, the die-cast aluminum alloy product has a die-cast state property including an electrical conductivity of at least 31Ms/m, an elongation of 20% and a yield strength of not less than 50Mpa at 180 ℃.
Compared with the prior art, the invention has the following beneficial effects:
1) The aluminum alloy plays a main role in mechanical strengthening through the combined addition of Fe, ni and Zr. The addition of Fe element can obviously improve the room temperature and high temperature yield strength of the material and improve the die casting capability, but the addition of Fe is easy to generate an Al 3 Fe phase in a needle shape in the solidification process, and the extensibility and the conductivity of the material are reduced, so that the modification and neutralization effects on the morphology of Fe element are achieved through the combined addition of Ni and Zr, the deposition probability of Fe atoms can be obviously reduced through the solid solution of Ni on Al 3 Fe and the deposition on the surface of the Fe phase, the diffusion of Fe atoms is hindered, the growth of the Al 3 Fe phase is limited, the distribution form of the Fe phase is changed, the Fe phase is changed into a short rod shape from a long needle shape, and the adverse influence on the conductivity and the extensibility of Fe is greatly reduced. If the proportion of Ni to the Fe phase is too small, the Fe phase is insufficient, the conductivity is not improved and the cost is improved due to too much Ni, zr plays a role in supplementing and modifying the morphology of the Fe phase, and the inventor verifies that the proportion of Fe to Ni+Zr is in a reasonable component range of 1-12:2, and the cost and the performance are considered;
2) The invention introduces B element in specific proportion, and aims at purifying aluminum liquid. Some elements with side effects on conductivity, such as Mn, V, ti, cr and the like, are inevitably present in the aluminum liquid, and are dissolved in an aluminum matrix to deteriorate the conductivity of the material, while the B has high affinity with the elements at high temperature, is extremely easy to react with the impurity elements to generate boride, and has the effects of purifying the aluminum liquid and improving the conductivity. Through practical verification and consideration of the actual components of industrial aluminum, the B element is controlled to be in a proper range of 0.01-0.1 wt%, and excessive B addition can increase lattice distortion of an aluminum matrix and increase grain boundaries, increase electron scattering probability and cause conductivity reduction;
3) The invention takes Fe as the main component, the Fe element has low cost, compared with the high Ni conductive aluminum alloy on the market, the alloy can greatly reduce the use of expensive element Ni element, obviously reduce the production cost, and the product prepared by the invention can meet the demands of the market on the mechanical property and the conductivity of the conductive aluminum alloy without an additional heat treatment process, has extremely high economic value and also meets the current low-carbon requirement;
4) The alloy disclosed by the invention is used for carrying out dispersion refinement on Fe base through the modification effect of Al-Er-La. The Er and La have extremely strong deterioration effect on the morphology of Fe phases, under the element proportion of the application, the Fe-based phases can be effectively dispersed and distributed in an aluminum matrix by combining the preparation process provided by the invention, and the produced rare earth precipitated phases containing La and Er are combined, so that the mechanical properties of the material can be effectively improved, compared with long needle-shaped and large granular precipitated phases, the precipitated phases in a dispersed form can obviously reduce the adverse effect on the conductivity, and meanwhile, er and La belong to rare earth elements, so that the gas and impurities in aluminum liquid are effectively removed, the aluminum liquid is supplemented and refined, and the conductivity and comprehensive mechanical properties of the material are further improved;
5) The die-casting product made of the conductive aluminum alloy can further improve the performance of the material through low-temperature baking, and the application range of the material is improved. The Ni and Zr alloy added in the invention can separate out submicron Al 3 Ni and Al 3 Zr phases in alpha-Al after baking, and the phases are high temperature resistant phases and are dispersed, thus being beneficial to pinning dislocation and improving the sliding difficulty of the alloy, so that the material has better yield strength and rigidity even at high temperature;
6) The alloy structure of the die-casting aluminum alloy prepared by the method comprises alpha-Al and eutectic structures; wherein the eutectic structure comprises an alpha-Al phase, an Al 3 Fe phase, an Al 3 (Fe, ni) phase, an Al 9 FeNi phase, an Al 3 Ni phase and an Al 3 (Fe, re) phase; the Al 3Fe、Al3 (Fe, ni) phase, the Al 9 FeNi phase, the Al 3 Ni phase and the Al 3 (Fe, re) phase are 0.5-5um in size and are mainly distributed in a dispersing way, and the dispersing distribution phase accounts for more than 90% of the precipitation area of the total precipitation phase; in the eutectic structure, al 3Fe、Al3 (Fe, ni) phase, al 9 FeNi phase, al 3 Ni phase and Al 3 (Fe, re) phase which are distributed in a dispersive particle way are formed, and the morphology comprises short rod shapes, spherical shapes and blocky shapes. The precipitated phases are uniformly dispersed, fine in size and round in shape, so that stress concentration between phases and a matrix can be effectively improved, and meanwhile, the precipitated phases have high-temperature tolerance, so that the mechanical properties of the product can be greatly improved on the basis of ensuring the conductivity;
7) According to the Al-Er-La nanocrystalline disclosed by the invention, the alloy powder is not contacted with other metals in the process from a molten state to solid cooling by a cryogenic aerosol method, so that cross contamination between the alloy powder and a cooling medium can be effectively avoided. Common cryogenic technology at the present stage, such as a mechanical ball milling method, a single-roller extreme cooling method or a quenching block cooling method, cannot avoid the mutual contact between materials and media by taking metal media as carriers, elements with adverse conductivity such as Cr, mn, cu and the like exist in the metal media more or less, the impurity content in the prepared alloy is improved due to the element diffusion phenomenon in the contact process, the purity of the aluminum soup is finally influenced, the impurity content of the aluminum soup is increased, and the conductivity is attenuated.
Drawings
FIG. 1 shows the microscopic metallographic phase (1000 times) of the die-casting aluminum alloy of comparative example 4 of the present invention.
FIG. 2 shows the microscopic metallographic phase (1000 times) of the die-cast aluminum alloy according to example 4 of the present invention.
FIG. 3 shows the microscopic metallographic phase (1000 times) of the die-casting aluminum alloy of comparative example 5 of the present invention.
FIG. 4 shows the microscopic metallographic phase (1000 times) of the die-cast aluminum alloy according to example 6 of the present invention.
Fig. 5 is a schematic diagram of the morphology of the precipitated phases in the die-casting aluminum alloy against the electron movement obstruction.
Fig. 6 is a schematic diagram of the morphology of the precipitated phases in the die-cast aluminum alloy versus the electron motion inhibition.
Detailed Description
The following describes in detail the examples of the present invention, which are implemented on the premise of the technical solution of the present invention, and detailed embodiments and specific operation procedures are given, but the scope of protection of the present invention is not limited to the following examples.
Examples 1 to 9 and comparative examples 1 to 10
A high-conductivity die-casting aluminum alloy based on dispersion strengthening comprises the following components ：Si：≤0.15wt％;Fe：0.05-3.0wt％;Ni：0.05-2.5wt％;Zr：0.005-0.15wt%;Er：0.005-0.10wt％;La：0.005-0.10wt％;Er+La：≤0.1wt%;Mn：≤0.05wt％;B：0.01-0.1wt％;Ti+Cr+V≤0.05wt％; in percentage by weight, the sum of the weight percentages of the rest impurities is controlled below 0.5 weight percent, and the balance is Al; and the mass ratio of Fe to (Ni+Zr) is controlled to be 1-12:2.
The specific examples and comparative examples are detailed in Table 1
Table 1 shows the aluminum alloy content tables of examples and comparative examples
The common commercial alloy is selected as the raw material if the elements are not specifically described,
The Al-Er-La nanocrystalline is prepared by a deep-cooling aerosol method, and the specific preparation method comprises the following steps:
step 1: adding commercial Al-10Er and Al-10La intermediate powder alloy to mix according to a proportion;
step 2: heating alloy powder of a specific component to 900 ℃ to enable the alloy powder to be in a molten state, taking inert gas (argon is selected here) as a protecting and cooling medium, forming tiny liquid drops by impacting the molten liquid flow through airflow (airflow pressure is 1.5 MPa), and cooling to form nanocrystalline powder, wherein the prepared alloy powder mainly comprises nanocrystalline;
Step 3: the collected alloy powder is pressed and bonded to prepare blocky Al-Er-La nanocrystalline alloy;
The high-conductivity die-casting aluminum alloy based on dispersion strengthening is prepared by the following steps:
Step S1: firstly, weighing pure aluminum raw materials, al-Fe, al-Ni, al-Zr, al-B intermediate alloy and Al-Er-La nanocrystalline alloy according to mass ratio;
Step S2: firstly, putting pure aluminum element into a heating furnace, heating to 680 ℃ to obtain molten aluminum liquid, and standing and preserving heat for 20-30min after the aluminum liquid metal is completely melted;
Step S3: heating to 780 ℃, and adding Al-Fe, al-Ni, al-B and Al-Zr alloys to the aluminum liquid according to a proportion until the alloys are completely dissolved;
step S4: cooling to 750 ℃, adding Al-Er-La nanocrystalline, and preserving heat for 20-30 min;
Step S5: cooling to 720 ℃, preserving heat for 15-20min, and then degassing and refining;
Step S6: pouring the small sample for component analysis, and sending the melt into forming equipment for forming after the small sample is qualified to obtain the high-conductivity die-casting aluminum alloy;
Step S7: melting the obtained high-conductivity die-casting aluminum alloy again at 720-740 ℃, preserving heat, introducing protective gas to isolate the heat from air, injecting injection into a die-casting die, vacuumizing, and performing vacuum die pressing to obtain a die-casting aluminum alloy product; the injection adopts a filling mode of firstly low speed and then high speed, the injection low speed is controlled at 0.15m/s, the temperature of the die casting die is controlled by an oil temperature machine, a water temperature machine and a water cooling machine in a co-operation mode, wherein the oil temperature machine is set at 220 ℃, the water temperature machine is 120 ℃, point cooling water passes through a die core point cooling pipeline under the water pressure of 1MPa, and the pressure is maintained for 5 seconds after the injection is finished, and the specific performance is shown in Table 2 in detail.
The die cast state in the example of table 2 refers to: the alloy is in a state of not being subjected to any heat treatment after being subjected to high-pressure die casting; the low temperature heat treatment state refers to: the state after 300 ℃/1-3h heat treatment is adopted, the process client can adjust according to the self demand, and the P value refers to: mass ratio of Fe to (ni+zr); the high temperature yield strength at 180 ℃ means: the yield strength obtained by mechanical property detection of the sample at 180 ℃; conductivity refers to: the conductivity of the material was measured at room temperature (20 ℃).
In the invention, the detection of tensile strength, yield strength and elongation is carried out according to national standard GB/T228.1-2010; the conductivity was carried out according to GB/T12966-2008.
TABLE 2 highly conductive aluminum alloy Properties of examples 1-9 and comparative examples 1-10
Analysis from the specific results in table 2 above:
Example 1 is compared with comparative example 1, example 2 is compared with comparative example 2, example 3 is compared with comparative example 3, and the difference is that the examples control the ratio P value of the sum of the dosages of Fe, ni and Zr to be 1-12:2, so that the morphology of the phases is modified, the original long needle-shaped and blocky Fe-based phases are modified and refined, and the conductivity and mechanical properties of the materials obtained in examples 1-3 are obviously higher than those of comparative examples 1-3 as can be seen from the results of the table.
Examples 4 and 5 are different from comparative example 4 in that examples 6,7 and 8 are higher in Fe/(Ni+Zr) ratio than comparative example 5 in comparative examples 4 and 5, and are far larger than the P value range, and examples 4,5 and 6,7 and 8 are in the P value range, and as a result, the performance of examples is superior to that of comparative examples, and the material properties of examples are mainly because the deterioration of Fe-based phase by too little Ni, zr content is not completely reflected.
Example 9 is compared with comparative example 6, comparative example 7, comparative example 8, comparative example 9 and comparative example 10, except that no additional Er, la and B (excessively low content) are added in comparative example 6, no additional Er and La rare earth are added in comparative example 7, comparative example 8 does not add element B, comparative example 9 uses Ni as a main component, and the result shows that the electrical conductivity and mechanical properties of example 9 modified by the inclusion of Er, la and B are optimal, the electrical conductivity advantage is insignificant, and the mechanical properties thereof are relatively low, the specific content of element B in comparative example 10 is 0.29wt%, and the excessive B causes lattice distortion of aluminum matrix after removing impurities again, but causes decrease in electrical conductivity beyond the upper limit of the mass ratio of element B to (ti+cr+v+mn) specified in the present invention.
From the data, the high-conductivity die-casting aluminum alloy in the embodiments 1-9 has excellent mechanical properties and conductivity, is very suitable for producing products such as motor rotors and the like with high requirements on conductivity and high-temperature performance, and has low production cost, and good economic benefit and application range for various production enterprises.
FIG. 1 is a microscopic metallographic (1000 times) drawing of the die-cast aluminum alloy of comparative example 4 according to the present invention, from which it can be seen that: under the proportion of Fe with medium and high content and low Ni+Zr, the appearance of the precipitated phase is needle-shaped, the morphology is irregular, the size is larger, and the proportion is unfavorable for improving the conductivity and the mechanical property.
Fig. 2 shows the microscopic metallography (1000 times) of the die-cast aluminum alloy according to example 4 of the present invention, and it can be seen from the figure: the Fe/Ni ratio in a reasonable range can effectively improve the distribution form and the particle size of a precipitated phase, the overall shape is round and regular, and the distribution form can effectively improve the conductivity and the mechanical property of the material.
FIG. 3 is a microscopic metallographic (1000 times) view of the die-cast aluminum alloy of comparative example 5 of the present invention, as can be seen from the drawing: under the high-content Fe proportion, the size of a precipitated phase is obviously increased, the morphology is long-strip-shaped, and the morphology is irregular, so that the conductivity and the mechanical property are not improved.
Fig. 4 shows the microscopic metallography (1000 times) of the die-cast aluminum alloy according to example 6 of the present invention, and it can be seen from the figure: the Fe/Ni+Zr ratio in a reasonable range is changed into a disperse phase, the shape is round and regular, and the distribution shape can effectively improve the conductivity and mechanical property of the material.
Fig. 5 is a schematic diagram of the appearance of a precipitated phase in a die-casting aluminum alloy against electron movement obstruction, and can be seen from the figure: the precipitation in large particles and long needles has obvious blocking effect relative to the electron transmission path, and the conductivity of the material is reduced.
Fig. 6 is a schematic diagram of the appearance of the precipitated phase in the die-casting aluminum alloy against the electron movement obstruction, and can be seen from the figure: the precipitated phase is dispersed after modification, the particles are fine, the obstruction of the precipitated phase to electrons on a transmission path is reduced, and good conductivity can be obtained.
The foregoing is a preferred embodiment of the present invention, but the scope of the present invention is not limited to the above implementation, and all technical solutions belonging to the concept of the present invention belong to the scope of the present invention.
Claims (8)
1. A high-conductivity die-casting aluminum alloy based on dispersion strengthening is characterized in that the alloy comprises Fe：0.10-2.0wt％;Ni：0.1-1.5wt％;Zr：0.005-0.10wt%;Er：0.005-0.08wt％;La：0.005-0.05％;Er+La：≤0.1wt%;Si：0.06-0.12wt％;Mn：0.005-0.05wt％; B：0.01wt％-0.05wt％;Ti+Cr+V≤0.03wt％; weight percent of the sum of the rest impurities, which is controlled below 0.5 weight percent, and the balance of Al; the mass ratio of Fe to (Ni+Zr) is controlled to be 1-12:2, and the mass ratio of B to (Ti+Cr+V+Mn) is controlled to be 1-10:2; the alloy structure of the die-casting aluminum alloy comprises alpha-Al and eutectic structures; wherein the eutectic structure comprises an alpha-Al phase, an Al 3 Fe phase, an Al 3 (Fe, ni) phase, an Al 9 FeNi phase, an Al 3 Ni phase and an Al 3 (Fe, re) phase; the Al 3Fe、Al3 (Fe, ni) phase, the Al 9 FeNi phase, the Al 3 Ni phase and the Al 3 (Fe, re) phase are 0.5-5um in size and are mainly distributed in a dispersing way, and the dispersing distribution phase accounts for more than 90% of the precipitation area of the total precipitation phase.
2. The high-conductivity die-casting aluminum alloy based on dispersion strengthening according to claim 1, wherein the Er and La are added in the form of Al-Er-La nanocrystalline, and the Al-Er-La nanocrystalline is prepared by a cryogenic aerosol method.
3. The die-casting aluminum alloy based on dispersion strengthening and high conductivity according to claim 2, wherein the specific preparation method of the Al-Er-La nanocrystalline is as follows:
step 1: mixing the commercial Al-Er and Al-La intermediate powder alloy according to a proportion;
Step 2: heating the mixed alloy powder to 850-1100 ℃ to enable the alloy powder to be in a molten state, taking inert gas as a protecting and cooling medium, forming tiny liquid drops after impacting the molten liquid flow through air flow and cooling, and forming nanocrystalline powder after cooling, wherein the prepared alloy powder mainly comprises nanocrystalline;
Step 3: and (3) carrying out press-bonding on the collected alloy powder to obtain the blocky Al-Er-La nanocrystalline alloy.
4. A dispersion-strengthened high-conductivity die-casting aluminum alloy according to claim 3, wherein the inert gas in step 2 is one of argon or nitrogen, and the gas flow pressure is 0.7-3.5MPa.
5. A method for producing a dispersion-strengthened high-conductivity die-cast aluminum alloy according to any one of claims 1 to 4, comprising the steps of:
step S1: weighing pure aluminum raw materials, al-Fe, al-Ni, al-Zr, al-B intermediate alloy and Al-Er-La nanocrystalline alloy according to mass ratio;
step S2: putting pure aluminum raw materials into a heating furnace, heating to 680 ℃ to obtain molten aluminum liquid, standing and preserving heat for 20-30min after aluminum liquid metal is completely melted;
step S3: heating to 780 ℃, and adding Al-Fe, al-Ni, al-B and Al-Zr into the aluminum liquid according to a proportion until the aluminum liquid is completely dissolved;
step S4: cooling to 750 ℃, adding Al-Er-La nanocrystalline, and preserving heat for 20-30 min;
Step S5: cooling to 720 ℃, preserving heat for 15-20min, and then degassing and refining;
Step S6: and (3) pouring the small sample for component analysis, and sending the melt into forming equipment for forming after the small sample is qualified to obtain the high-conductivity die-casting aluminum alloy.
6. An application of a high-conductivity die-casting aluminum alloy based on dispersion reinforcement, which is characterized in that the high-conductivity die-casting aluminum alloy obtained in the claim 5 is subjected to high-pressure die-casting molding, and specifically comprises the following steps:
and melting the high-conductivity die-casting aluminum alloy again at 720-740 ℃, preserving heat, introducing protective gas to isolate the heat from air, injecting injection into a die-casting die, vacuumizing, and performing vacuum die pressing to obtain a die-casting aluminum alloy product.
7. The application of the dispersion-reinforced high-conductivity die-casting aluminum alloy according to claim 6, wherein the injection adopts a filling mode of firstly low speed and then high speed, the injection low speed is controlled to be 0.10-0.25 m/s, the temperature of the die-casting die is controlled by an oil temperature machine, a water temperature machine and a water cooling machine in a co-operation mode, wherein the oil temperature machine is set to be 210-250 ℃, the water temperature machine is set to be 100-140 ℃, the cooling water is kept at 15-30 ℃, the point cooling water passes through a die core point cooling pipeline under the water pressure of 0.8-1 MPa, and the pressure is maintained for 5-10 seconds after the injection is finished.
8. The use of a dispersion strengthened, high conductivity die cast aluminum alloy as claimed in claim 6, wherein the die cast properties of the resulting die cast aluminum alloy product, without further treatment, comprise an electrical conductivity of at least 31Ms/m, an elongation of 20% and a yield strength of not less than 50Mpa at 180 ℃.
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