CN117127067A - High-performance cast aluminum alloy material and preparation method thereof - Google Patents
High-performance cast aluminum alloy material and preparation method thereof Download PDFInfo
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- 239000000956 alloy Substances 0.000 title claims abstract description 136
- 229910000838 Al alloy Inorganic materials 0.000 title claims abstract description 59
- 238000002360 preparation method Methods 0.000 title abstract description 13
- 238000005266 casting Methods 0.000 claims abstract description 37
- 229910052761 rare earth metal Inorganic materials 0.000 claims abstract description 10
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 claims abstract description 4
- 229910052782 aluminium Inorganic materials 0.000 claims abstract description 4
- 239000012535 impurity Substances 0.000 claims abstract description 3
- 229910045601 alloy Inorganic materials 0.000 claims description 102
- 230000032683 aging Effects 0.000 claims description 21
- 238000010438 heat treatment Methods 0.000 claims description 17
- 238000000034 method Methods 0.000 claims description 14
- 239000000243 solution Substances 0.000 claims description 14
- 239000006104 solid solution Substances 0.000 claims description 12
- 239000007788 liquid Substances 0.000 claims description 7
- 230000008018 melting Effects 0.000 claims description 7
- 238000002844 melting Methods 0.000 claims description 7
- 238000007670 refining Methods 0.000 claims description 7
- 238000005303 weighing Methods 0.000 claims description 7
- 238000003723 Smelting Methods 0.000 claims description 6
- 229910021421 monocrystalline silicon Inorganic materials 0.000 claims description 6
- 238000003756 stirring Methods 0.000 claims description 6
- 238000001816 cooling Methods 0.000 claims description 5
- 230000005484 gravity Effects 0.000 claims description 5
- 229910052710 silicon Inorganic materials 0.000 claims description 5
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 4
- 238000001035 drying Methods 0.000 claims description 3
- 229910052758 niobium Inorganic materials 0.000 claims description 3
- 238000010791 quenching Methods 0.000 claims description 3
- 230000000171 quenching effect Effects 0.000 claims description 3
- 238000004140 cleaning Methods 0.000 claims description 2
- 229910052720 vanadium Inorganic materials 0.000 claims description 2
- 229910052726 zirconium Inorganic materials 0.000 claims description 2
- 238000004519 manufacturing process Methods 0.000 claims 3
- 229910018182 Al—Cu Inorganic materials 0.000 abstract description 5
- 230000007547 defect Effects 0.000 abstract description 3
- 229910000676 Si alloy Inorganic materials 0.000 abstract description 2
- 238000005728 strengthening Methods 0.000 description 18
- 238000001556 precipitation Methods 0.000 description 16
- 230000008569 process Effects 0.000 description 10
- 239000011159 matrix material Substances 0.000 description 8
- 239000000203 mixture Substances 0.000 description 7
- 238000007711 solidification Methods 0.000 description 6
- 230000008023 solidification Effects 0.000 description 6
- 239000000126 substance Substances 0.000 description 6
- 229910017818 Cu—Mg Inorganic materials 0.000 description 5
- 230000000694 effects Effects 0.000 description 5
- 230000005496 eutectics Effects 0.000 description 5
- 239000004615 ingredient Substances 0.000 description 5
- 230000000052 comparative effect Effects 0.000 description 4
- 229910000521 B alloy Inorganic materials 0.000 description 3
- 230000015572 biosynthetic process Effects 0.000 description 3
- 230000007123 defense Effects 0.000 description 3
- 229910052719 titanium Inorganic materials 0.000 description 3
- 239000010936 titanium Substances 0.000 description 3
- 231100000331 toxic Toxicity 0.000 description 3
- 230000002588 toxic effect Effects 0.000 description 3
- 229910018125 Al-Si Inorganic materials 0.000 description 2
- 229910018520 Al—Si Inorganic materials 0.000 description 2
- UGACIEPFGXRWCH-UHFFFAOYSA-N [Si].[Ti] Chemical compound [Si].[Ti] UGACIEPFGXRWCH-UHFFFAOYSA-N 0.000 description 2
- 238000004364 calculation method Methods 0.000 description 2
- 238000005336 cracking Methods 0.000 description 2
- 239000000835 fiber Substances 0.000 description 2
- 239000000463 material Substances 0.000 description 2
- 239000010955 niobium Substances 0.000 description 2
- 231100000572 poisoning Toxicity 0.000 description 2
- 230000000607 poisoning effect Effects 0.000 description 2
- 150000002910 rare earth metals Chemical class 0.000 description 2
- 238000005204 segregation Methods 0.000 description 2
- 238000004088 simulation Methods 0.000 description 2
- 230000035882 stress Effects 0.000 description 2
- 238000005275 alloying Methods 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 239000013078 crystal Substances 0.000 description 1
- 238000010586 diagram Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000009776 industrial production Methods 0.000 description 1
- 230000003993 interaction Effects 0.000 description 1
- 238000012986 modification Methods 0.000 description 1
- 230000004048 modification Effects 0.000 description 1
- LIZIAPBBPRPPLV-UHFFFAOYSA-N niobium silicon Chemical compound [Si].[Nb] LIZIAPBBPRPPLV-UHFFFAOYSA-N 0.000 description 1
- 239000002893 slag Substances 0.000 description 1
- 239000007787 solid Substances 0.000 description 1
Classifications
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C21/00—Alloys based on aluminium
- C22C21/02—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
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
- C22C1/026—Alloys based on aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C1/00—Making non-ferrous alloys
- C22C1/02—Making non-ferrous alloys by melting
- C22C1/03—Making non-ferrous alloys by melting using master alloys
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/002—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
- 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
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Abstract
The invention provides a high-performance cast aluminum alloy material, which comprises the following elements in percentage by weight: si:7.0 to 10.0wt.%, cu:0.5 to 3.0wt.%, mg:0.10 to 0.75wt.%, rare earth element RE:0 to 0.50wt.%, ti:0.05 to 0.30wt.%, sr: 0.005-0.20 wt.%, B:0.01 to 0.20wt.%, total amount of impurity elements: less than 0.1wt.%, balance aluminum. The invention also relates to a preparation method of the high-performance cast aluminum alloy material. The high-performance cast aluminum alloy has excellent mechanical properties, far exceeds the performance standard of the conventional typical A1-Si alloy, achieves the performance level of Al-Cu high-strength aluminum alloy, has the tensile strength of 410-460 MPa at room temperature, the yield strength of 320-360 MPa and the elongation of 5.5-10.5 percent, and simultaneously has good fluidity, the casting process is not easy to generate defects such as shrinkage porosity and the like, and the whole casting process is good.
Description
Technical Field
The invention relates to the technical field of high-performance light-weight structural aluminum alloy materials and casting, in particular to an Al-Si-Cu-Mg series high-performance cast aluminum alloy material and a preparation method thereof.
Background
The aluminum alloy casting has the excellent characteristics of light weight, high specific strength, low expansion coefficient and the like, and is widely applied to the fields of automobile industry, aerospace and the like. At present, with the continuous demands of fields such as national defense equipment, aerospace and the like on casting with high strength, light weight and low cost, the market hopefully obtains a novel cast aluminum alloy material with high strength and excellent casting performance.
The strength of the Al-Cu series alloy widely applied in China at present is 400MPa, but the casting performance is poor, the Al-Si series alloy cannot be used for producing some high-quality complex castings, the casting performance is generally 300MPa, but the strength is lower, the Al-Si-Cu-Mg series casting alloy has the advantages of excellent casting performance of the Al-Si series alloy, high strength of the Al-Cu series alloy and the like, and the Al-Cu series casting alloy has wide application prospect in the fields of national defense equipment and aerospace, such as rocket shells, tail covers, engine cylinder blocks, cylinder heads and the like. However, the application of the alloy in China is still not as wide as that of alloys such as ZL114A, ZL A and ZL205A, especially on high-quality complex castings, and the main reason is that the mechanical properties of the alloy still cannot meet the engineering application requirements, and the high-performance cast aluminum alloy material becomes an urgent need in the field of novel high-end equipment in China.
Disclosure of Invention
The invention provides a high-performance cast aluminum alloy material and a preparation method thereof, and the A1-Si-Cu-Mg alloy obtained by the preparation method can obtain excellent strength and elongation matching and is far superior to the performance standard of the A1-Si alloy for the existing vehicles, aerospace and high-end equipment parts. So as to meet the requirements of the field of high-end equipment in China on high-performance casting aluminum alloy materials and improve the internal quality and the comprehensive mechanical properties of the new-generation high-end equipment aluminum alloy casting products in China.
The technical scheme of the invention is as follows:
a high performance cast aluminum alloy material, characterized by: the high-performance cast aluminum alloy material comprises the following elements in percentage by weight: si:7.0 to 10.0wt.%, cu:0.5 to 3.0wt.%, mg:0.10 to 0.75wt.%, rare earth element RE:0 to 0.50wt.%, ti:0.05 to 0.30wt.%, sr: 0.005-0.20 wt.%, B:0.01 to 0.20wt.%, total amount of impurity elements: less than 0.1wt.%, balance aluminum.
The function of Si is to form a large amount of eutectic Si phases which are dispersed and distributed, cu and Mg are main strengthening elements to form a large amount of theta and Q strengthening phases, the rare earth elements RE, ti and B can effectively refine grain structures, the Sr element has high-efficiency metamorphism function, the eutectic Si phases can be metamorphized from coarse plate shapes to fine fiber shapes, and the mechanical property of the alloy is improved.
The preferable technical scheme is as follows:
the rare earth RE is added in the form of Al-Ti-RE-B intermediate alloy. Further preferred is: the rare earth element RE is at least one of Nb, la, ce, eu or some combination thereof.
The aluminum alloy also contains at least one of the following elements in percentage by weight: mn:0 to 0.8wt.%, V:0 to 0.5wt.%, zr:0 to 0.7wt.%.
The mass ratio of Cu and Mg elements in the aluminum alloy material is limited to be between Cu/Mg=3.5 and 7.5.
According to the invention, the mass ratio of Cu and Mg elements in the alloy is limited between Cu/Mg=3.5 and 7.5 by adjusting the addition ratio of the Cu and Mg elements, so that the type, the size and the generation amount of each secondary phase (theta phase and Q phase are equal) in a structure are controlled, the secondary phases can be completely dissolved in a matrix under the solution treatment process, the simulation calculation result of related materials is shown in fig. 6, and a plurality of evenly distributed precipitation strengthening phases with theta phase and Q phase equal are formed in the aging treatment process, dislocation slip in the structure can be effectively prevented, a good precipitation strengthening effect is generated, and the mechanical property of the cast aluminum alloy is greatly improved. However, when the mass ratio of Cu to Mg is too large, the Cu element is seriously segregated in the solidification process, and the solidification is causedForming a large amount of eutectic theta-Al with low melting point in solid structure 2 The Cu phase is difficult to dissolve completely during heat treatment, and is extremely easy to generate an overburning structure, so that the mechanical property of the alloy is seriously affected; when the mass ratio of Cu and Mg elements is too small, a large number of thick plate-shaped Q phases are formed in the tissue, as shown in fig. 4, the large-size phases are difficult to dissolve completely in the heat treatment process, so that not only is stress concentrated formed and an alpha-Al matrix severely cracked, but also undissolved Q phases bind a large number of Cu and Mg solute atoms, the precipitation of precipitation phases in the subsequent aging process is reduced, the aging strengthening effect of the alloy is weakened, and the alloy performance is reduced.
The Ti, nb, la, B and other elements in the Al-Ti-RE-B intermediate alloy not only can inhibit the growth of aluminum alloy grains and effectively refine the grains, but also promotes the formation of equiaxed grains and obviously improves the mechanical property of the alloy, and the interaction between Nb and Si is weaker than that between Ti and Si, so that a niobium silicon compound with toxic action is not easy to form, the grain structure of the aluminum alloy with high Si content (Si > 5%) can be effectively refined, and the defect that the traditional Al-Ti-B refiner fails due to the phenomenon of 'poisoning' (formation of a titanium silicon compound with toxic action) in the aluminum alloy with high Si content is avoided. The Sr element can effectively modify eutectic Si into fine fibers, and obviously improves the elongation and tensile strength of the A1-Si-Cu-Mg alloy.
The invention relates to a preparation method of a high-performance cast aluminum alloy material, which sequentially comprises the following steps:
step 1, batching:
weighing Al ingot, mg ingot, single crystal Si, al-50Cu intermediate alloy, al-10Sr intermediate alloy and Al-Ti-RE-B intermediate alloy according to the proportion of each element in the high-performance cast aluminum alloy material, and drying and preheating for standby;
step 2, smelting:
after the smelting furnace is electrified, throwing an Al ingot along with the furnace, after the Al ingot is melted, sequentially adding monocrystalline Si, al-50Cu intermediate alloy, al-Ti-RE-B intermediate alloy and Mg ingot, stirring for 4-8 min after the melting is finished, finally adding Al-10Sr intermediate alloy, stirring for 5-10 min after the melting of Al-10Sr is finished, refining for 10-40 min by pure Ar gas, standing for 5-15 min, slagging off, obtaining refined alloy liquid, and waiting for pouring;
and 3, pouring:
pouring the alloy liquid refined in the step 2 into a casting mould preheated to 230-260 ℃ by gravity or pouring the alloy liquid into the casting mould by counter gravity at 710-730 ℃, and cooling and solidifying to form a casting or an ingot;
step 4, heat treatment:
after the casting or the cast ingot after the cleaning is subjected to solution treatment, water quenching is carried out, the casting or the cast ingot is cooled to room temperature, and then artificial aging treatment is carried out.
The technical scheme of the preferred preparation method also comprises the following contents:
in the step 2, the charging temperature of the monocrystal Si and Mg ingot is 680-710 ℃, the charging temperature of the Al-50Cu intermediate alloy and the Al-Ti-RE-B intermediate alloy is 730-760 ℃, the charging temperature of the Al-10Sr intermediate alloy is 710-730 ℃, and the refining temperature is 700-730 ℃.
When the alloy contains Mn and/or V and/or Zr, in the step 2, adding an Al-10Mn intermediate alloy and/or an Al-4V intermediate alloy together with an Al ingot, melting, and then adding the Al-10Zr intermediate alloy at the temperature of 730-760 ℃.
In step 4, in order to form solid solution of each secondary phase (θ phase, Q phase, etc.) formed during solidification into the α -Al matrix, element segregation of the alloy during solidification is eliminated and occurrence of tissue overburning is prevented, the present invention employs a multi-stage solid solution treatment.
The heat treatment system of the step 4 is as follows: performing multistage solid solution treatment at 455-545 ℃ for less than 30h, transferring to 25-75 ℃ in 5-10 s, cooling to normal temperature in water, and performing aging treatment at 145-195 ℃ for less than 25 h;
the multi-stage solid solution treatment is a secondary solid solution treatment or a tertiary solid solution treatment:
if the solution treatment is the second-level solution treatment, the requirements are satisfied: preserving heat for 4-10 h at 455-515 ℃, and then raising the temperature to 515-545 ℃ for 8-20 h;
if three-stage solution treatment is adopted, the requirements are satisfied: preserving heat for 1-4 h at 455-485 ℃, then heating to 485-515 ℃ for 4-10 h, and finally heating to 520-540 ℃ for 6-15 h.
The tensile strength of the aluminum alloy is 410-460 MPa, the yield strength is 320-360 MPa, and the elongation is 5.5-10.5%.
The regulation and control of the alloy structure and the strengthening phase are mainly carried out from the following three aspects:
(1) Controlling precipitation of the strengthening phase by adjusting alloy components;
(2) Controlling the precipitation of the strengthening phase through a heat treatment process;
(3) The grains of the microstructure are refined by adding rare earth elements RE in the form of Al-Ti-RE-B alloy.
Through the regulation and control of the alloy structure and the precipitation of the strengthening phase, the invention obtains a fine and uniform grain structure and fine and dispersed precipitation strengthening phases theta and Q, the size of the precipitation strengthening phase is below 1 micron, and the precipitation strengthening phase is dispersed and distributed in an alloy matrix, as shown in figure 3, so that the alloy has extremely high tensile strength and elongation at normal temperature, and shows excellent mechanical properties.
The beneficial effects of the invention are as follows:
the invention provides a high-performance cast aluminum alloy mainly used for high-end equipment and a preparation method thereof, and the high-performance cast aluminum alloy material with high strength, high elongation and good casting performance is obtained by scientific alloying component design and proper heat treatment process, and the mechanical properties of the alloy and typical alloy are shown in table 3. Under the condition of room temperature, the tensile strength of the cast aluminum alloy can reach 410-460 MPa, the yield strength can reach 320-360 MPa, the elongation can reach 5.5-10.5%, the performance standard of the A1-Si series alloy for the existing vehicles, aerospace and high-end equipment parts is far exceeded, the performance level of the Al-Cu series high-strength alloy is achieved, the alloy has strong fluidity, small shrinkage cavity and hot cracking tendency, the whole casting manufacturability is good, and the fluidity of the alloy and a typical alloy is shown in figure 5.
According to the invention, the mass ratio of Cu and Mg elements is limited between Cu/Mg=3.5-7.5, a multistage solution treatment process is adopted, the occurrence of the phenomenon of tissue overburning can be effectively prevented, the quenching temperature of the alloy can be increased, the secondary phases (theta phase and Q phase are equal) generated in the solidification process of the alloy can be completely dissolved into an alpha-Al matrix, the subsequent aging strengthening effect is greatly improved, and the problems that the high-strength aluminum alloy such as ZL201A, ZL A in China has high Cu content, serious segregation and hot cracking tendency, poor overall casting manufacturability, easy tissue overburning and the like are avoided.
According to the invention, the Al-Ti-RE-B intermediate alloy is adopted to refine the alloy structure, elements such as Ti, nb, la, B and the like can inhibit the growth of aluminum alloy grains, effectively refine the grains, promote the formation of equiaxed grains, obviously improve the mechanical property of the alloy, and also effectively refine the aluminum alloy with high Si content (Si is more than 5%), thereby avoiding the defect that the traditional Al-Ti-B refiner fails due to the phenomenon of poisoning (forming titanium silicon compound with toxic action) in the aluminum alloy with high Si content, and simultaneously reducing the consumption of rare earth RE and the alloy refining cost compared with the addition of expensive Al-RE-B alloy.
The preparation method is simple and easy to operate, and has strong operability; only conventional equipment is needed, the cost is low, and the method is suitable for industrial production. The aluminum alloy material has excellent strength and elongation and good casting manufacturability, and is particularly suitable for the fields of national defense equipment, aerospace and the like.
Drawings
FIG. 1 is a diagram (magnified 100 times) of an as-cast metallographic structure of a high-performance aluminum alloy prepared in example 1;
FIG. 2 is a metallographic structure chart (magnified 100 times) of the high-performance aluminum alloy prepared in example 1 after solutionizing and aging;
FIG. 3 is a metallographic structure chart (500 times magnification) of the high-performance aluminum alloy prepared in example 1 after solutionizing and aging;
FIG. 4 is a metallographic structure chart (200 times enlarged) of the high-performance aluminum alloy prepared in comparative example 1 after solutionizing;
FIG. 5 is the fluidity of 6 exemplary brands of alloys with the alloys of the present invention at a casting temperature of 700 ℃;
FIG. 6 shows simulation calculation results of the material affected by the content of Cu and Mg elements.
Detailed Description
The invention is further illustrated, but not limited, by the following examples and figures of the specification.
Example 1
A high-performance cast aluminum alloy material and a preparation method thereof are provided: A1-Si-Cu-Mg cast aluminum alloy. The preparation process comprises the following steps:
step 1, batching:
the proportioning requirements of the high-performance casting aluminum alloy material are as follows: 88.25%, si:9.0%, cu:2.0%, mg:0.4%, ti:0.15%, RE:0.15%, sr:0.03%, B:0.04%.
According to the proportion requirement, weighing Al ingot, single crystal Si, al-50Cu intermediate alloy, mg ingot, al-Ti-RE-B intermediate alloy and Al-10Sr intermediate alloy, preparing 35Kg of alloy altogether, and drying and preheating.
Step 2, smelting: after the smelting furnace is electrified, an Al ingot is put into the furnace, after the Al ingot is melted, the temperature of an aluminum melt is controlled at 680-710 ℃, single crystal Si is added, al-50Cu intermediate alloy and Al-Ti-RE-B intermediate alloy are added at 730-760 ℃, the temperature is reduced to 680-710 ℃, an Mg ingot is added, stirring is carried out for 4-8 min after the Mg ingot is melted, finally Al-10Sr intermediate alloy is added at 710-730 ℃, stirring is carried out for 5-10 min after the Al-10Sr is melted, ar gas refining is carried out for 10-40 min at 700-730 ℃, and slag skimming is carried out after standing for 5-15 min, and casting is waited.
And 3, pouring: pouring refined aluminum alloy liquid into a casting mould preheated to 230-260 ℃ by adopting ladle gravity at 710-730 ℃, and cooling and solidifying to form an ingot;
step 4, heat treatment: carrying out multistage solid solution treatment on the cleaned cast ingot, preserving heat for 6 hours at 455-515 ℃, and then raising the temperature to 515-545 ℃ for 15 hours; aging treatment: aging treatment is carried out at 145-195 ℃ for less than 25 hours.
The chemical compositions of the alloy finally prepared in this example are shown in table 1, the as-cast microstructure of the alloy is shown in fig. 1, the as-cast microstructure of the aluminum alloy is obviously refined by the refining effect of the Al-Ti-RE-B alloy, and the average intercept method shows that the alpha-Al crystal grain size is less than 20 microns and is uniformly distributed. The microstructure of the alloy after solid solution and aging is shown in fig. 2 and 3, the alloy mainly comprises an alpha-Al matrix, eutectic Si and fine dispersed precipitation strengthening phases (theta phase and Q phase), the size of the aging precipitation strengthening phases is less than 1 micron, the aging precipitation strengthening phases are uniformly distributed in the alloy matrix, the strength of the alloy is effectively improved by the precipitation phases, and the mechanical properties of the alloy at normal temperature are shown in table 2.
Example 2
Most of the contents of this embodiment are the same as embodiment 1, except that:
in the step 1, the ingredients of the high-performance casting aluminum alloy material are as follows: 88.27%, si:9.0%, cu:2.0%, mg:0.4%, ti:0.25%, sr:0.03%, B: weighing 0.05 percent of the components; in step 4, solution treatment: preserving heat for 2h at 455-485 ℃, then heating to 485-515 ℃ for 8h, finally heating to 520-540 ℃ for 14h, and aging treatment: aging treatment is carried out at 145-195 ℃ for less than 25 hours.
The chemical compositions of the alloy finally prepared in the embodiment are shown in table 1, and the mechanical properties of the alloy at normal temperature are shown in table 2.
Example 3
Most of the contents of this embodiment are the same as embodiment 1, except that:
in the step 1, the ingredients of the high-performance casting aluminum alloy material are as follows: 88.77%, si:9.0%, cu:1.40%, mg:0.35%, ti:0.1%, RE:0.08%, sr:0.03%, B: the proportion of 0.04% is weighed.
The chemical compositions of the alloy finally prepared in this example are shown in Table 1, and the mechanical properties at normal temperature are shown in Table 2.
Example 4
Most of the contents of this embodiment are the same as embodiment 1, except that:
in the step 1, the ingredients of the high-performance casting aluminum alloy material are as follows: 87.80%, si:9.0%, cu:1.8%, mg:0.35%, ti:0.1%, mn:0.4%, zr:0.3%, RE:0.2%, sr:0.03%, B: weighing at a ratio of 0.04%
The chemical compositions of the alloy finally prepared in this example are shown in Table 1, and the mechanical properties at normal temperature are shown in Table 2.
Example 5
Most of the contents of this embodiment are the same as embodiment 1, except that:
in the step 1, the ingredients of the high-performance casting aluminum alloy material are as follows: 87.00%, si:9.0%, cu:2.5%, mg:0.55%, ti:0.2%, zr:0.35%, RE:0.35%, sr:0.03%, B: weighing 0.04 percent; in step 4, solution treatment: preserving heat for 3h at 455-485 ℃, then heating to 485-515 ℃ for 6h, finally heating to 520-540 ℃ for 12h, aging treatment: aging treatment is carried out at 145-195 ℃ for less than 25 hours.
The chemical compositions of the alloy finally prepared in this example are shown in Table 1, and the mechanical properties at normal temperature are shown in Table 2.
Comparative example 1
The preparation procedure is identical to example 1, except that it is not specifically described: in the step 1, the ingredients are mixed according to the following formula: 88.44%, si:9.0%, cu:0.8%, mg:0.7%, ti:0.15%, RE:0.15%, sr:0.03%, B: weighing 0.04 percent.
The chemical compositions of the alloy finally prepared in the comparative example are shown in table 1, the mass ratio of Cu and Mg elements in the comparative example is far beyond the limit of Cu/Mg=3.5-7.5, the Mg element in the alloy and Si, cu and other elements form a large number of large-size blocky Q phases in the solidification process, the phase size is more than 15 microns, and the undissolved large-size Q phases after the solution treatment of the alloy are shown in fig. 4. The large-size phases are difficult to dissolve completely in the solution treatment process, stress concentration can be formed, an alpha-Al matrix is severely cracked, undissolved Q phases bind a large number of Cu and Mg solute atoms, precipitation of precipitation strengthening phases (theta and Q phases) in the subsequent aging process can be reduced, the aging strengthening effect of the alloy is weakened, and the alloy performance is reduced. The mechanical properties of the alloy at normal temperature are shown in Table 2.
Table 1 alloy composition (wt.%)
Table 2 results of mechanical properties test of alloys
TABLE 3 mechanical Properties of alloys of the invention and typical brands of alloys
The invention is not a matter of the known technology.
The above embodiments are provided to illustrate the technical concept and features of the present invention and are intended to enable those skilled in the art to understand the content of the present invention and implement the same, and are not intended to limit the scope of the present invention. All equivalent changes or modifications made in accordance with the spirit of the present invention should be construed to be included in the scope of the present invention.
Claims (9)
1. A high performance cast aluminum alloy material, characterized by: the high-performance cast aluminum alloy material comprises the following elements in percentage by weight: si:7.0 to 10.0wt.%, cu:0.5 to 3.0wt.%, mg:0.10 to 0.75wt.%, rare earth element RE:0 to 0.50wt.%, ti:0.05 to 0.30wt.%, sr: 0.005-0.20 wt.%, B:0.01 to 0.20wt.%, total amount of impurity elements: less than 0.1wt.%, balance aluminum.
2. The high performance cast aluminum alloy material according to claim 1, wherein the rare earth element RE is added in the form of an Al-Ti-RE-B master alloy.
3. The high performance cast aluminum alloy material according to claim 2, wherein the rare earth element RE is at least one of Nb, la, ce, eu or some combination thereof.
4. The high performance cast aluminum alloy material according to claim 1, wherein the aluminum alloy further comprises at least one of the following groups of elements, each element satisfying the following requirements in terms of weight percent: mn:0 to 0.8wt.%, V:0 to 0.5wt.%, zr:0 to 0.7wt.%.
5. The high-performance cast aluminum alloy material according to claim 1, 3 or 4, wherein the mass ratio of Cu and Mg elements in the aluminum alloy is Cu/mg=3.5 to 7.5.
6. The method for preparing the high-performance cast aluminum alloy material as claimed in claim 1, which is characterized by comprising the following steps in sequence:
step 1, batching:
weighing Al ingot, mg ingot, single crystal Si, al-50Cu intermediate alloy, al-10Sr intermediate alloy and Al-Ti-RE-B intermediate alloy according to the proportion of each element in the high-performance cast aluminum alloy material, and drying and preheating for standby;
step 2, smelting:
after the smelting furnace is electrified, throwing an Al ingot along with the furnace, after the Al ingot is melted, sequentially adding monocrystalline Si, al-50Cu intermediate alloy, al-Ti-RE-B intermediate alloy and Mg ingot, stirring for 4-8 min after the melting is finished, finally adding Al-10Sr intermediate alloy, stirring for 5-10 min after the melting of Al-10Sr is finished, refining for 10-40 min by pure Ar gas, standing for 5-15 min, slagging off, obtaining refined alloy liquid, and waiting for pouring;
and 3, pouring:
pouring the alloy liquid refined in the step 2 into a casting mould preheated to 230-260 ℃ by gravity or pouring the alloy liquid into the casting mould by counter gravity at 710-730 ℃, and cooling and solidifying to form a casting or an ingot;
step 4, heat treatment:
after the casting or the cast ingot after the cleaning is subjected to solution treatment, water quenching is carried out, the casting or the cast ingot is cooled to room temperature, and then artificial aging treatment is carried out.
7. The method for producing a high-performance cast aluminum alloy material according to claim 6, wherein: in the step 2, the charging temperature of the monocrystal Si and Mg ingot is 680-710 ℃, the charging temperature of the Al-50Cu intermediate alloy and the Al-Ti-RE-B intermediate alloy is 730-760 ℃, the charging temperature of the Al-10Sr intermediate alloy is 710-730 ℃, and the refining temperature is 700-730 ℃.
8. The method for producing a high-performance cast aluminum alloy material according to claim 6, wherein: when the alloy contains Mn and/or V and/or Zr, in the step 2, adding an Al-10Mn intermediate alloy and/or an Al-4V intermediate alloy together with an Al ingot, melting, and then adding the Al-10Zr intermediate alloy at the temperature of 730-760 ℃.
9. The method for producing a high-performance cast aluminum alloy material according to claim 6, wherein: the heat treatment system of the step 4 is as follows: performing multistage solid solution treatment at 455-545 ℃ for less than 30h, transferring to 25-75 ℃ in 5-10 s, cooling to normal temperature in water, and performing aging treatment at 145-195 ℃ for less than 25 h;
the multi-stage solid solution treatment is a secondary solid solution treatment or a tertiary solid solution treatment; if the solution treatment is the second-level solution treatment, the requirements are satisfied: preserving heat for 4-10 h at 455-515 ℃, and then raising the temperature to 515-545 ℃ for 8-20 h;
if three-stage solution treatment is adopted, the requirements are satisfied: preserving heat for 1-4 h at 455-485 ℃, then heating to 485-515 ℃ for 4-10 h, and finally heating to 520-540 ℃ for 6-15 h.
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