CN116926384A - High-strength and high-toughness aluminum-based composite material and preparation method thereof - Google Patents
High-strength and high-toughness aluminum-based composite material and preparation method thereof Download PDFInfo
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- 239000002131 composite material Substances 0.000 title claims abstract description 46
- 229910052782 aluminium Inorganic materials 0.000 title claims abstract description 45
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 title claims abstract description 41
- 238000002360 preparation method Methods 0.000 title abstract description 14
- 239000000956 alloy Substances 0.000 claims abstract description 58
- 229910045601 alloy Inorganic materials 0.000 claims abstract description 57
- 238000010438 heat treatment Methods 0.000 claims abstract description 20
- 229910052710 silicon Inorganic materials 0.000 claims abstract description 8
- 239000012535 impurity Substances 0.000 claims abstract description 3
- 239000000155 melt Substances 0.000 claims description 16
- 238000011282 treatment Methods 0.000 claims description 15
- 238000009210 therapy by ultrasound Methods 0.000 claims description 12
- 238000000034 method Methods 0.000 claims description 10
- 238000005728 strengthening Methods 0.000 claims description 10
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- 230000032683 aging Effects 0.000 claims description 9
- 239000006104 solid solution Substances 0.000 claims description 8
- 238000003756 stirring Methods 0.000 claims description 8
- 229910018521 Al—Sb Inorganic materials 0.000 claims description 6
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 claims description 6
- 229910002804 graphite Inorganic materials 0.000 claims description 6
- 239000010439 graphite Substances 0.000 claims description 6
- 229910018575 Al—Ti Inorganic materials 0.000 claims description 5
- 238000001816 cooling Methods 0.000 claims description 4
- 229910052751 metal Inorganic materials 0.000 claims description 4
- 239000002184 metal Substances 0.000 claims description 4
- 238000010791 quenching Methods 0.000 claims description 4
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- 238000004519 manufacturing process Methods 0.000 claims description 3
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- 238000002844 melting Methods 0.000 claims description 3
- 238000012546 transfer Methods 0.000 claims description 3
- CSDREXVUYHZDNP-UHFFFAOYSA-N alumanylidynesilicon Chemical compound [Al].[Si] CSDREXVUYHZDNP-UHFFFAOYSA-N 0.000 abstract description 12
- 229910000676 Si alloy Inorganic materials 0.000 abstract description 11
- 230000001105 regulatory effect Effects 0.000 abstract 1
- 230000000052 comparative effect Effects 0.000 description 12
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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
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B22—CASTING; POWDER METALLURGY
- B22C—FOUNDRY MOULDING
- B22C9/00—Moulds or cores; Moulding processes
- B22C9/06—Permanent moulds for shaped castings
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- 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
- C22C1/10—Alloys containing non-metals
- C22C1/1036—Alloys containing non-metals starting from a melt
-
- 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
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- 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 discloses a high-strength and high-toughness aluminum-based composite material and a preparation method thereof, wherein the high-strength and high-toughness aluminum-based composite material comprises the following components in percentage by mass: 6.5 to 7.5 percent of Si, 0.2 to 0.4 percent of Mg, 0.2 to 1 percent of Ti, 0.2 to 1 percent of Zr, 0.1 to 0.5 percent of B, 0.2 to 1 percent of Sb, the content of unavoidable impurities is less than or equal to 0.2 percent, and the balance is Al. The invention adds Ti, zr and B elements into hypoeutectic aluminum-silicon alloy, and Al can be formed in the as-cast state 3 Ti、Al 3 Zr、TiB 2 And ZrB 2 The microstructure of the alloy is cooperatively regulated and controlled by virtue of the Sb element dispersed reinforced phase and a reasonable heat treatment processFinally, the aluminum-based composite material with the tensile strength more than or equal to 340MPa, the yield strength more than or equal to 290MPa and the elongation more than or equal to 10.0 percent is obtained.
Description
Technical Field
The invention belongs to the field of smelting and processing of aluminum alloy materials, and particularly relates to a high-strength and high-toughness aluminum-based composite material and a preparation method thereof.
Background
Among lightweight materials, aluminum is becoming the most widely used lightweight metal material in various industries due to its unique performance advantages. Hypoeutectic Al-Si alloy has the characteristics of high specific strength, high elastic modulus, high wear resistance, low thermal expansion coefficient and the like, and is widely applied to various fields such as aerospace, automobile industry, electronic packaging, sports equipment and the like. However, because the matrix grains are too coarse, the eutectic silicon phase is in a coarse flaky or blocky structure, so that the comprehensive mechanical property of the eutectic silicon phase is not high, and the requirements of certain fields on the property of the eutectic silicon phase are difficult to meet.
In order to further improve various mechanical properties of hypoeutectic aluminum-silicon alloy, modification treatment, alloying and heat treatment processes are generally adopted to eliminate dendrite segregation and needle-shaped structures in the structures, and meanwhile, the tensile strength of the alloy is improved and the internal stress of the alloy is removed. The composite material has high hardness, good plasticity, high impact toughness and other ideal performances, and may be used widely in producing various automobile parts. The yield strength is used as a mark for the material to enter the plastic deformation stage from the elastic deformation stage, is an important index for evaluating the tensile property and the safety of the material, and has important significance for engineering design and material selection. However, the research on high yield hypoeutectic aluminum-silicon alloy is lacking at present, the yield strength of the cast hypoeutectic aluminum-silicon alloy is less than 260Mpa, and the application range is not wide enough.
Patent CN108588513A discloses a modified A356 aluminum alloy and a multiple ageing heat treatment method thereof, trace Zr and Sr elements are used for carrying out refined grain treatment and modification treatment on a melt, and the A356 aluminum alloy prepared under T6 heat treatment of solution treatment and multiple ageing is provided with 319MPa of tensile strength and 12% of elongation. However, sr is very active in chemical properties, is very prone to burn during addition, and is prone to defects such as pores generated by the absorption of hydrogen in the molten aluminum, which makes the refining process more complicated.
Patent CN108486428A discloses a method for preparing a composite reinforced alloy, which is based on the components of the traditional A356 alloy, and is added with trace Ti and Zr elements for alloying modification.
Patent CN108193096A discloses a hypoeutectic aluminum-silicon casting alloy with high strength and high toughness and a preparation method thereof, and the obtained alloy has tensile strength reaching 366MPa and elongation of 6.5 percent through Sc, zr and Sr composite refinement and modification treatment, 545-548 ℃ multiplied by 12h solid solution and two-stage aging (120-130 ℃ multiplied by 4h low-temperature preaging and 170-175 ℃ multiplied by 5-6h final aging) heat treatment. However, the rare earth Sc in the invention has high price and high use cost, and the elongation of the alloy is lower than that of the invention.
In the article of research on the structure and performance of Ti and Zr composite modified A356 alloy, through the research on Ti and Zr two elements composite modified hypoeutectic Al-7Si-0.35Mg alloy, the research shows that the Ti and Zr elements can composite refine the alloy structure and cooperatively change the shape of eutectic silicon in an as-cast structure. After the heat treatment of the aluminum alloy after the composite modification, the tensile strength and the yield strength respectively reach 315MPa and 245MPa. The yield strength is still significantly insufficient compared to the preparation method of the present invention.
The influence of the Al-Ti-C-B refiner on the structure and the performance of the A356 aluminum alloy (special casting and nonferrous alloy, 2021.Vol.41, no. 11) is studied by adding the Al-Ti-C-B refiner, and the influence of Ti, C and B elements on the alpha-Al phase and the mechanical property in the A356 alloy is studied. The research shows that the addition of Al-Ti-C-B into the A356 alloy can obviously refine alpha-Al, when the addition amount is 1%, the tensile strength of the alloy is 320.8MPa, the yield strength is 273.3MPa, and the elongation is 12%. But the strength of the material is too low.
The influence and deterioration mechanism of Sb on A356 alloy structure and mechanical property (special casting and nonferrous alloy, 2017.Vol.37, no. 10) research the influence of Sb content on A356 alloy structure and mechanical property, and the result shows that Sb can effectively reduce the nucleation temperature of eutectic structure, improve the nucleation supercooling degree and reduce the nucleation rate of eutectic structure. When the Sb addition amount was 0.4%, the tensile strength of the T6 state alloy was 266MPa and the elongation was 13.3%. However, the addition of Sb alone to the modified eutectic silicon in this article does not provide a high strength hypoeutectic aluminum-silicon alloy.
In summary, there are many kinds of hypoeutectic aluminum-silicon alloys industrially produced at present, but the method for producing high-performance hypoeutectic aluminum-silicon alloys is still not mature, and particularly reports about obtaining high yield strength are few. Therefore, there is an urgent need for hypoeutectic aluminum-silicon alloy with excellent comprehensive properties to provide choices for more industrial fields.
Disclosure of Invention
Aiming at the defects existing in the prior hypoeutectic aluminum-silicon alloy preparation, the invention provides a high-toughness aluminum-based composite material and a preparation method thereof, and aims to ensure high toughness and simultaneously ensure that the alloy has good plasticity and toughness.
The invention adopts the following technical scheme to solve the technical problems:
the high-strength and high-toughness aluminum-based composite material comprises the following components in percentage by mass: 6.5 to 7.5 percent of Si, 0.2 to 0.4 percent of Mg, 0.2 to 1 percent of Ti, 0.2 to 1 percent of Zr, 0.1 to 0.5 percent of B, 0.2 to 1 percent of Sb, the content of unavoidable impurities is less than or equal to 0.2 percent, and the balance is Al. According to the invention, a large number of experimental components are optimized, and Ti, zr, B, sb element is added in the form of intermediate alloy to form Al 3 Ti、Al 3 Zr、TiB 2 And ZrB 2 And (3) strengthening phase. The Al-Sb has negative polarization effect on the aluminum melt, so that the reinforced phase distribution is more uniform. The high-strength and high-toughness aluminum-based composite material prepared by the method can realize microstructure optimization and remarkable improvement of mechanical properties, obtain extremely high yield strength and meet higher industrial safety requirements.
The preparation method of the high-strength and high-toughness aluminum-based composite material comprises the following steps:
step 1: melting A356 alloy at 700-750deg.C, and maintaining the temperature for 10-20min;
step 2: heating a smelting furnace to 760-780 ℃, adding Al-Ti, al-Zr and Al-B intermediate alloy, uniformly stirring by using a graphite stirring rod, and preserving heat for 5-30min;
step 3: when the temperature of the melt is reduced to 740+/-10 ℃, adding Al-Sb intermediate alloy, and preserving heat for 10-60min;
step 4: when the temperature of the melt is reduced to 720+/-10 ℃, applying high-energy ultrasonic treatment to the melt;
step 5: after ultrasonic treatment, standing for 10-20min, and removing surface scum;
step 6: pouring the molten metal prepared in the step 5 into a metal mold, and naturally cooling to room temperature to obtain an as-cast aluminum-based composite material;
step 7: and carrying out T6 heat treatment on the as-cast aluminum-based composite material to obtain the T6-state aluminum-based composite material with excellent tissue and mechanical properties.
Further, in the step 4, the ultrasonic vibration starting temperature of the high-energy ultrasonic treatment is 710-730 ℃, the ultrasonic time is 2-4min, the ultrasonic frequency is 20kHz, and the ultrasonic power is 1kw.
Further, in the step 7, the solid solution temperature of the heat treatment is 525-540 ℃, the solid solution time is 360-480 min, the quenching transfer time is less than or equal to 15s, the aging treatment temperature is 170-185 ℃, and the aging time is 420-540 min.
Compared with the prior art, the invention has the beneficial effects that:
1. the high-strength and high-toughness aluminum-based composite material prepared by the method disclosed by the invention meets the requirements that the tensile strength is more than or equal to 340MPa, the yield strength is more than or equal to 290MPa, and the elongation is more than or equal to 10.0%. Compared with the aluminum-silicon alloy used in the traditional industry, the high-strength and high-toughness aluminum-based composite material prepared by the method has higher tensile strength, greatly improves the yield strength of the alloy, reaches the leading level at home and abroad, greatly improves the safety and the range of material use, increases the practical use limit of the material, and ensures the safety of engineering application.
2. Unlike the conventional method of adding Ti, zr and B elements to refine alpha-Al, the preparation method of the high-strength and toughness aluminum-based composite material of the invention can form Al in the as-cast state by adding Ti, zr and B elements in the form of intermediate alloy 3 Ti、Al 3 Zr、TiB 2 And ZrB 2 And the reinforcing phases are subjected to heat treatment to form a plurality of uniformly distributed reinforcing phases, so that the tissue morphology of the aluminum-based composite material can be obviously optimized, and the mechanical property is improved.
3. In the invention, sb is added to disperse the strengthening phase, the bonding energy of the Sb element and the Al matrix is negative, and the interfacial energy of the strengthening phase/the Al matrix can be reduced to improve the dispersion. And the Sb element does not interact with other elements in the melt, so that poisoning reaction is avoided.
4. The ultrasonic vibration treatment in the invention brings a distribution optimization effect to the composite material, and the partial aggregation of the strengthening phase is effectively dispersed by the ultrasonic vibration treatment. Ultrasonic vibration treatment also has the functions of grain refinement and degassing.
Drawings
FIG. 1 shows the as-cast and T6 microstructures of the alloy obtained in example 2, wherein: (a) and (b) correspond to the low-power and high-power amplification of the microstructure of the as-cast alloy obtained in example 2, respectively, and (c) and (d) correspond to the low-power and high-power amplification of the microstructure of the T6 alloy obtained in example 2, respectively.
Detailed Description
The present invention will be described in detail with reference to specific examples. The following examples will assist those skilled in the art in further understanding the present invention, but are not intended to limit the invention in any way. It should be noted that variations and modifications could be made by those skilled in the art without departing from the inventive concept. These are all within the scope of the present invention.
Example 1
The embodiment provides a high-strength and high-toughness aluminum-based composite material, which comprises the following components in percentage by mass: 7.0% of Si, 0.31% of Mg, 0.45% of Ti, 0.25% of Zr, 0.4% of Sb, 0.1% of B and the balance of Al.
The preparation method of the high-strength and high-toughness aluminum-based composite material comprises the following steps:
1000g of A356 alloy cast ingot is added into a graphite crucible with the preheating temperature of 300 ℃, then the temperature of a smelting furnace is raised to 735 ℃, and after the alloy is completely melted in the smelting furnace, the temperature is kept for 10 minutes, so that the temperature of a melt is uniform, and surface scum is removed. Heating a smelting furnace to 770 ℃, adding Al-Ti, al-Zr and Al-B intermediate alloy, uniformly stirring by using a graphite stirring rod, and preserving heat for 15min; when the temperature of the melt is reduced to 740 ℃, adding Al-Sb intermediate alloy, and preserving heat for 10min; and after the temperature of the melt is reduced to 720 ℃, applying high-energy ultrasonic treatment to the melt. After ultrasonic treatment, standing for 10min, and removing surface scum. And slowly casting the alloy liquid into a cast steel mold preheated to 200 ℃, and air-cooling to obtain the reinforced as-cast aluminum-based composite material. The ultrasonic vibration starting temperature of the high-energy ultrasonic treatment is 720 ℃, the ultrasonic time is 2min, the ultrasonic frequency is 20kHz, and the ultrasonic power is 1kw.
The as-cast aluminum-based composite material is subjected to solid solution treatment, the solid solution temperature is 540 ℃, the solid solution time is 360min, and the quenching medium is water at 20 ℃. After the solution treatment is completed, the alloy is put into another heat treatment furnace for aging treatment, the quenching transfer time is 10s, the aging treatment temperature is 180 ℃, the heat preservation is carried out for 420min, and the alloy is taken out and then cooled to room temperature by air, so that the T6 state A356 alloy is obtained.
Cutting from castings to a size of 10X 6mm 3 The test piece is ground and polished, the test piece is corroded by 0.5vol.% HF reagent for 14-18s, and then the surface of the test piece is cleaned by alcohol and dried for metallographic structure observation. Cutting a tensile sample on the cast ingot, polishing, and obtaining the sheet tensile sample after the surface of the sheet tensile sample is smooth and flat. The tensile property test is carried out by using AG-100KNXplus universal electronic testing machine (reference standard is GB/T228.1-2010), and the displacement control mode is adopted, so that the tensile speed is 1.2mm/min.
Example 2
The embodiment provides a high-strength and high-toughness aluminum-based composite material, which comprises the following components in percentage by mass: 7.0% of Si, 0.31% of Mg, 0.45% of Ti, 0.25% of Zr, 0.8% of Sb, 0.1% of B and the balance of Al.
The preparation method of the high-strength and high-toughness aluminum-based composite material comprises the following steps:
1000g of A356 alloy cast ingot is added into a graphite crucible with the preheating temperature of 300 ℃, then the temperature of a smelting furnace is raised to 735 ℃, and after the alloy is completely melted in the smelting furnace, the temperature is kept for 10 minutes, so that the temperature of a melt is uniform, and surface scum is removed. Heating a smelting furnace to 770 ℃, adding Al-Ti, al-Zr and Al-B intermediate alloy, uniformly stirring by using a graphite stirring rod, and preserving heat for 15min; when the temperature of the melt is reduced to 740 ℃, adding Al-Sb intermediate alloy, and preserving heat for 10min; and after the temperature of the melt is reduced to 720 ℃, applying high-energy ultrasonic treatment to the melt. After ultrasonic treatment, standing for 10min, and removing surface scum. And slowly casting the alloy liquid into a cast steel mold preheated to 200 ℃, and air-cooling to obtain the reinforced as-cast aluminum-based composite material. The ultrasonic vibration starting temperature of the high-energy ultrasonic treatment is 720 ℃, the ultrasonic time is 2min, the ultrasonic frequency is 20kHz, and the ultrasonic power is 1kw.
The sample T6 heat treatment process in this example was the same as in example 1.
In this example, the sample preparation and test procedure were the same as in example 1.
The microscopic morphology of the as-cast and T6 states of the sample in this example is shown in fig. 1.
Comparative example 1
The difference between this comparative example and example 1 is that: the mass percentages of Ti and Zr in the alloy are respectively 0.5 percent and 0 percent.
Comparative example 2
The difference between this comparative example and example 1 is that: and (3) directly melting the A356 alloy cast ingot without adding other elements, and then carrying out T6 heat treatment.
Table 1: as-cast A356 alloy secondary dendrite spacing size (SDAS) measurements in the examples and comparative examples above
Table 1 shows visually the SDAS size of the as-cast alloys of examples 1-2 and comparative examples 1-2, where the SDAS of the novel hypo-eutectic aluminum-silicon alloy is smaller than that of comparative example 2, where the SDAS of the example 2 alloy is minimal, only 21.7 μm, and 40.5% drop compared to that of comparative example 2.
Table 2: mechanical Properties of the alloys of the above examples and comparative examples before and after heat treatment
As can be seen from Table 2, the aluminum-based composite material of the examples, whether in the as-cast or T6 state, has improved tensile strength, yield strength, and elongation to a different extent than the alloys of the comparative examples. In particular, the alloy of example 2 has the best mechanical properties in as-cast and T6 states, far exceeding the values specified in the implementation standard ASTM (tensile strength > 295MPa, elongation > 3%). Compared with the T6 state of the alloy subjected to the synergistic strengthening of Al-Ti and Al-Sb in the comparative example 1, the tensile strength and the yield strength of the alloy T6 state in the example 2 are respectively improved by 15.2 percent and 22.9 percent. Compared with the alloy T6 state without strengthening treatment in the comparative example 2, the tensile strength, the yield strength and the elongation of the alloy T6 state in the example 2 are respectively improved by 42.9%, 85.8% and 205.7%, and the improvement range is particularly obvious.
FIGS. 1 (a) - (d) correspond to the morphology of the as-cast and T6 reinforcement phases of example 2, respectively. It can be seen that the strengthening phases and the second phase particles are uniformly distributed in the matrix, and the strengthening phases can effectively improve the mechanical properties of the alloy. Compared with the as-cast aluminum-based composite material, the T6-state aluminum-based composite material after heat treatment has finer strengthening phases, more quantity, more uniform distribution and more excellent material performance.
In summary, the embodiment of the invention provides a high-strength and high-toughness aluminum-based composite material and a preparation method thereof. Compared with the alloy prepared by the traditional method, the high-strength and high-toughness aluminum-based composite material prepared by the invention has extremely high yield strength, greatly increases the safety and has wider industrial application range.
Claims (6)
1. The high-strength and high-toughness aluminum-based composite material is characterized by comprising the following components in percentage by mass: 6.5 to 7.5 percent of Si, 0.2 to 0.4 percent of Mg, 0.2 to 1 percent of Ti, 0.2 to 1 percent of Zr, 0.1 to 0.5 percent of B, 0.2 to 1 percent of Sb, the content of unavoidable impurities is less than or equal to 0.2 percent, and the balance is Al.
2. The high strength and toughness according to claim 1An aluminum-based composite material characterized in that: al is formed in the as-cast state of the aluminum-based composite material 3 Ti、Al 3 Zr、TiB 2 And ZrB 2 And (3) strengthening phase.
3. The high strength and toughness aluminum-based composite material according to claim 1, wherein: the tensile strength of the aluminum-based composite material is more than or equal to 340MPa, the yield strength is more than or equal to 290MPa, and the elongation is more than or equal to 10.0%.
4. A method for preparing the high-strength and toughness aluminum-based composite material according to any one of claims 1 to 3, which is characterized by comprising the following steps:
step 1: melting A356 alloy at 700-750deg.C and maintaining the temperature for 20min;
step 2: heating a smelting furnace to 760-780 ℃, adding Al-Ti, al-Zr and Al-B intermediate alloy, uniformly stirring by using a graphite stirring rod, and preserving heat for 5-30min;
step 3: when the temperature of the melt is reduced to 740+/-10 ℃, adding Al-Sb intermediate alloy, and preserving heat for 10-60min;
step 4: when the temperature of the melt is reduced to 720+/-10 ℃, applying high-energy ultrasonic treatment to the melt;
step 5: after ultrasonic treatment, standing for 10-20min, and removing surface scum;
step 6: pouring the molten metal prepared in the step 5 into a metal mold, and naturally cooling to room temperature to obtain an as-cast aluminum-based composite material;
step 7: and carrying out T6 heat treatment on the as-cast aluminum-based composite material to obtain the T6-state aluminum-based composite material.
5. The method of manufacturing according to claim 4, wherein: in the step 4, the ultrasonic vibration starting temperature of the high-energy ultrasonic treatment is 710-730 ℃, the ultrasonic time is 2-4min, the ultrasonic frequency is 20kHz, and the ultrasonic power is 1kw.
6. The method of manufacturing according to claim 4, wherein: in the step 7, the solid solution temperature of heat treatment is 525-540 ℃, the solid solution time is 360-480 min, the quenching transfer time is less than or equal to 15s, the aging treatment temperature is 170-185 ℃, and the aging time is 420-540 min.
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