A nanoscale TiB 2p / 6201 Ceramic Steel Aluminum Alloy, Its Cryogenic Melting Synthesis Method and Applications

Abstract

The application provides a nanoscale TiB 2p The application provides a porcelain aluminum alloy, a super-low-temperature melting synthesis method and application thereof, and a preparation method of the porcelain aluminum alloy, which comprises the following steps: melt casting preparation of a precursor: Al-10Ti and Al-3B intermediate alloy are heated and melted, mechanical stirring is combined with ultrasonic melt treatment to accelerate the reaction, the reaction temperature is kept at 660-670 DEG C to synthesize nanoscale particles at a low temperature; remelting and dilution; homogenization treatment; hot rolling; solid solution treatment; room temperature rolling; and artificial aging treatment, so that the nanoscale TiB 2p / 6201 porcelain aluminum alloy is prepared. The aluminum alloy has excellent mechanical properties and electrical conductivity, nanoscale TiB2 ceramic particles are introduced into the high-strength and high-conductivity power transmission aluminum material compared with traditional power transmission aluminum materials, the nanoscale TiB2 ceramic particles are synthesized at a low temperature by using a melt casting method, the preparation process is combined closely with traditional power transmission aluminum material preparation processes, is easy to popularize, and is low in cost, so that the nanoscale TiB2 ceramic particles can be produced in a large scale.

Description

Technical Field

[0001] This invention relates to new materials technology, and more particularly to a nanoscale TiB. 2p / 6201 ceramic-aluminum alloy, its ultra-low temperature melting synthesis method and applications. Background Technology

[0002] The large-scale preparation of nanoscale particle-reinforced metal matrix composites has significant research and application value. The size effect of the reinforcing phase in particle-reinforced metal matrix composites is the most critical factor determining the mechanical properties of the composite material; the finer the particles, the higher the strength. Therefore, reducing particle size during the preparation process has become paramount to further improving its strength.

[0003] In-situ generation of TiB2 ceramic particles to reinforce aluminum matrix composites via fluoride salt reaction, combined with traditional aluminum alloy casting processes, has led to its widespread application and demonstrates significant potential in power transmission conductors. The introduction of TiB2 ceramic particles not only refines the grain size, improving strength and elongation, but also enhances conductor stiffness, thereby reducing sag and improving safety. Due to the low content of ceramic particles (0.5–2 wt.%), this material is known as a ceramic-aluminum alloy.

[0004] The TiB2 ceramic particles prepared by the fluoride salt reaction method in ceramic-aluminum alloys range in size from several hundred nanometers to several micrometers. From the perspective of crystal nucleation and growth, during the in-situ generation and growth of ceramic particles, higher temperatures result in faster atomic diffusion, leading to larger final particle sizes. The thermodynamic conditions of this reaction system are relatively high, with reaction temperatures typically ranging from 800 to 900°C. Further lowering the reaction temperature leads to incomplete or insufficient reactions, or even prevents them from proceeding altogether. Furthermore, the reaction itself is an aluminothermic reaction, releasing a large amount of heat, inevitably increasing the reaction temperature. Therefore, developing a new approach to lower the reaction temperature and obtain nanoscale TiB2 ceramic particle reinforcing phases has become crucial for the preparation of high-performance ceramic-aluminum alloys. Summary of the Invention

[0005] The purpose of this invention is to address the problem of high thermodynamic conditions in the traditional fluoride salt reaction method for preparing ceramic-aluminum alloys, and to propose a nanoscale TiB... 2p The method for synthesizing 6201 ceramic-aluminum alloy by ultra-low temperature melting is based on the intermediate alloy reaction method, which can further reduce the size of the particle reinforcing phase. The method has a low melting temperature, simple process, and low cost. The prepared ceramic-aluminum alloy has excellent mechanical properties and electrical conductivity.

[0006] To achieve the above objectives, the technical solution adopted by the present invention is: a nanoscale TiB 2p The method for synthesizing 6201 ceramic-aluminum alloy by ultra-low temperature melting includes the following steps:

[0007] Step (1) Raw material preparation: 1) Al-10Ti master alloy (Al-10%Ti, mass fraction, unless otherwise specified, % in this invention refers to mass percentage content), wherein Ti element exists mainly in the form of Al3Ti intermetallic compound, except in trace amounts of solid solution atoms; 2) Al-3B master alloy (Al-3%B), wherein B element exists in the form of AlB2 ceramic particles; 3) Al-10Mg master alloy (Al-10%Mg); 4) Al-12Si master alloy (Al-12%Si); 5) Industrial pure aluminum (purity >99.7%);

[0008] Step (2) Precursor casting preparation: 1) The Al-10Ti master alloy and Al-3B master alloy are proportioned according to a B / Ti stoichiometric ratio of 2.0 to 2.1; 2) The two master alloys are simultaneously placed in a graphite clay crucible and heated to 710 to 720°C in a pit-type melting resistance furnace, and the melt is immediately cooled to 670 to 680°C; 3) Mechanical stirring (600 to 800 r / min, the same below) is applied for 5 to 10 minutes, and the melt temperature is 660 to 670°C; 4) Ultrasonic melt treatment is applied (frequency 20 kHz, 1) Power 400-500W (same below) 8-10 min, melt temperature 660-670℃; 5) Apply mechanical stirring for 15-20 min, melt temperature 660-670℃; 6) Hold at 660-670℃ for 20 min; 7) Apply ultrasonic melt treatment for 8-10 min, melt temperature 660-670℃; 8) Apply mechanical stirring for 15-20 min, melt temperature 660-670℃; 9) Refine the melt by introducing high-purity argon gas for 3-5 min; 10) Remove slag; 11) Cast to prepare Al-nTiB2 precursor;

[0009] Step (3) Remelting and dilution: 1) The Al-nTiB2 precursor, Al-10Mg master alloy, Al-12Si master alloy and industrial pure aluminum are placed in a graphite clay crucible at a weight ratio of 9-10:5.2-6.2:4.8-5:78.8-81 and heated to 710-720℃, and stirred to mix thoroughly; 2) Hold at this temperature for 5-10 min; 3) Refine with high-purity argon gas for 3-5 min; 4) Perform ultrasonic melt treatment for 3-5 min; 5) Cast to obtain nano-sized TiB2. 2p / 6201 porcelain-coated aluminum alloy ingot;

[0010] Step (4) Homogenization treatment: The nanoscale TiB 2p / 6201 ceramic-coated aluminum alloy ingots are held in a muffle furnace at 540-570℃ for 12-24 hours, then cooled in the furnace to 250-300℃ and air-cooled to avoid coarsening of the precipitated phases.

[0011] Step (5) Hot rolling: After homogenization treatment, the ingot is preheated to 450-470℃ and held for 30-60 minutes. It is then hot rolled using a twin-roll mill with a total reduction of 20-30%, a reduction of 3-5% per pass, and a roll speed of 100-150 r / min.

[0012] Step (6) Solution treatment: The hot-rolled plate is placed in a muffle furnace for solution treatment at a temperature of 550-570°C and a holding time of 30-60 minutes, followed by water quenching at room temperature.

[0013] Step (7) Room temperature rolling: The solution-treated product is rolled at room temperature using a twin-roll mill with a total reduction of 75-80%, a reduction of 3-4% per pass, and a roll speed of 50-100 r / min.

[0014] Step (8) Aging: Artificial aging treatment is carried out in an aging furnace at a temperature of 160-170℃ for 3-5 hours.

[0015] Furthermore, the content of TiB2 ceramic particles in the Al-nTiB2 precursor prepared in step (2) is 4.5-5.5%, preferably 5%.

[0016] Furthermore, the nanoscale TiB prepared in step (3) 2p The TiB2 ceramic particle content in the 6201 ceramic-aluminum alloy ingot is 0.45-0.55%, preferably 0.5%.

[0017] Furthermore, the nanoscale TiB prepared in step (3) 2p The 6201 ceramic-coated aluminum alloy ingot contains 0.6-0.9% Mg, 0.5-0.9% Si, less than 0.2% Fe, and less than 0.1% of each other impurity.

[0018] Furthermore, in steps (2) and (3), all raw materials are dried in a drying oven for 30 to 60 minutes before smelting at a temperature of 200 to 220°C.

[0019] Furthermore, step (6) requires strict control of the heat treatment temperature and duration to prevent recrystallization and coarsening of grains in the hot-rolled structure.

[0020] Another object of the present invention discloses a nanoscale TiB 2p The 6201 ceramic-coated aluminum alloy is prepared using the above method.

[0021] Furthermore, the nanoscale TiB 2p The 6201 ceramic-coated aluminum alloy comprises the following components by weight:

[0022] TiB2 0.45–0.55%;

[0023] Mg 0.6–0.9%;

[0024] Si 0.5-0.9%;

[0025] The Fe content of impurities is less than 0.2%;

[0026] The content of each other impurity is less than 0.1%;

[0027] The margin is Al.

[0028] Furthermore, the preferred nanoscale TiB 2p The 6201 ceramic-coated aluminum alloy comprises the following components by weight:

[0029] TiB2 0.5%;

[0030] Mg 0.6%;

[0031] Si 0.6%;

[0032] The Fe content of impurities is less than 0.2%;

[0033] The content of each other impurity is less than 0.1%;

[0034] The margin is Al.

[0035] Furthermore, the nanoscale TiB 2p The particles in the 6201 ceramic-coated aluminum alloy are 10-100 nanometers in size.

[0036] Another object of the present invention discloses a nanoscale TiB 2p Applications of / 6201 ceramic-coated aluminum alloy in the field of high-strength, high-conductivity aluminum materials.

[0037] Furthermore, the nanoscale TiB 2p / 6201 ceramic-coated aluminum alloy has a tensile strength of 375–380 MPa, an elongation after fracture of 6.8–7.1%, and an electrical conductivity of 56.2–56.4% IACS; for example, nano-sized TiB 2p When the TiB2 ceramic particle content in the / 6201 ceramic-coated aluminum alloy is 0.5%, the tensile strength reaches 380 MPa, the elongation after fracture is 6.8%, and the electrical conductivity reaches 56.3% IACS.

[0038] This invention relates to nanoscale TiB 2p / 6201 ceramic-aluminum alloy, its ultra-low temperature melting synthesis method and applications, have the following advantages compared with existing technologies:

[0039] I. The method of this invention uses the melting and casting method to prepare ceramic-coated aluminum alloy, which is closely integrated with the traditional preparation process of power transmission aluminum materials, is easy to promote, and has low cost, and can be mass-produced on a large scale.

[0040] II. Compared with the fluoride salt reaction method, the ultra-low temperature melting synthesis method of the present invention has the following advantages: 1) The product consists only of the reinforcing phase and the matrix, with no other reaction products; 2) The reaction of the present invention is carried out in the entire melt, while the fluoride salt reaction method is carried out only at the molten salt / melt interface; 3) The reaction of the present invention can be carried out at ultra-low temperature (660-670℃), and there is no aluminothermic reaction that releases a large amount of heat.

[0041] III. The Al-nTiB2 precursor prepared by the method of this invention yields a large number of nano-sized TiB2 ceramic particles, with the smallest particle size reaching as low as tens of nanometers. The nano-sized TiB2 prepared by this invention... 2p Most of the particles in the / 6201 ceramic-coated aluminum alloy have a particle size of 10-100 nanometers.

[0042] IV. Nanoscale TiB prepared by the method of this invention 2p / 6201 ceramic-coated aluminum alloy has excellent mechanical properties and electrical conductivity. For example, when the TiB2 ceramic particle content is only 0.5%, the tensile strength reaches 380MPa, the elongation after fracture is 6.8%, and the electrical conductivity reaches 56.3% IACS.

[0043] In this invention, P represents particle, n represents nanometer, and μ represents micrometer. Attached Figure Description

[0044] Figure 1 The figures show the morphology and size of ceramic particles in the Al-nTiB2 precursor prepared in Example 1. Figure (a) is a scanning electron microscope image of the 3D morphology of the particles after deep etching, Figure (b) is a magnified image of Figure (a), and Figure (c) is a transmission electron microscope image of the particle morphology.

[0045] Figure 2 6201 aluminum alloy and TiB prepared for Comparative Example 1, Comparative Example 2 and Example 1 2μp / 6201 ceramic-coated aluminum alloy and TiB 2np Engineering stress-engineering strain curve of / 6201 ceramic-coated aluminum alloy.

[0046] Figure 3 6201 aluminum alloy and TiB prepared for Comparative Example 1, Comparative Example 2 and Example 1 2μp / 6201 ceramic-coated aluminum alloy and TiB 2np The electrical conductivity of / 6201 ceramic-coated aluminum alloy.

[0047] Figure 4 6201 aluminum alloy and TiB prepared for Comparative Example 1, Comparative Example 2 and Example 12μp / 6201 ceramic-coated aluminum alloy and TiB 2np Scanning electron microscope image of the fracture morphology of / 6201 ceramic-coated aluminum alloy. Detailed Implementation

[0048] The present invention will be further described below with reference to the embodiments:

[0049] Compare with Example 1

[0050] This comparative example discloses a method for preparing 6201 aluminum alloy for power transmission aluminum materials, including the following steps:

[0051] Step (1) Raw material preparation

[0052] 1) Industrial pure aluminum (purity > 99.7%), mass fraction 88.8%; 2) Al-10Mg master alloy, mass fraction 6.2%; 3) Al-12Si master alloy, mass fraction 5%; 4) Raw materials were dried in a drying oven for 30 minutes at 200℃ before smelting; 5) The composition of the prepared 6201 aluminum alloy is 0.6% Mg, 0.6% Si, Fe content less than 0.2%, and the content of each other impurity less than 0.1%.

[0053] Step (2) Smelting

[0054] 1) Place Al-10Mg master alloy, Al-12Si master alloy and industrial pure aluminum into a graphite clay crucible and heat to 720℃, stirring to mix them thoroughly; 2) Hold for 10 min; 3) Refine with high-purity argon gas for 5 min; 4) Ultrasonic melt treatment for 3 min; 5) Cast to prepare 6201 aluminum alloy ingot.

[0055] Step (3) Homogenization

[0056] The 6201 aluminum alloy ingot was held at 560℃ for 12 hours in a muffle furnace, then cooled to 300℃ in the furnace and air-cooled to avoid coarsening of the precipitated phase.

[0057] Step (4) Hot rolling

[0058] After homogenization, the ingot is preheated to 460℃ and held for 60 minutes. It is then hot rolled using a twin-roll mill with a total reduction of 30%, a reduction of 5% per pass, and a roll speed of 150 r / min.

[0059] Step (5) Solution treatment

[0060] The hot-rolled plate was placed in a muffle furnace for solution treatment at a temperature of 560°C for 30 minutes, followed by water quenching at room temperature.

[0061] Step (6) Room temperature rolling

[0062] The solid solution sample was rolled at room temperature using a twin-roll mill with a total reduction of 78.6%, a reduction of 3.6% per pass, and a roll speed of 50 r / min.

[0063] Step (7) Time Limit

[0064] Artificial aging treatment was carried out in an aging furnace at a temperature of 170℃ for 4 hours.

[0065] Compare with Example 2:

[0066] This comparative example discloses a fluoride salt reaction method for synthesizing micron-sized TiB. 2p The preparation method of / 6201 ceramic-coated aluminum alloy for power transmission aluminum materials includes the following steps:

[0067] Step (1) Raw material preparation: 1) Industrial-grade Al-μTiB2 precursor (aluminum material containing micron-sized TiB2 particles), with Ti and B content of 4.01% and 1.75% respectively, added at a mass fraction of 8.3%; 2) Al-10Mg master alloy, mass fraction of 6.2%; 3) Al-12Si master alloy, mass fraction of 5%; 4) Industrial pure aluminum (purity >99.7%), mass fraction of 80.5%; 5) Raw materials are dried in a drying oven for 30 minutes at 200℃ before smelting; 6) Materials used to prepare micron-sized TiB2 particles. 2p The particle content of the 6201 ceramic-coated aluminum alloy is 0.5%, and the other components are 0.6% Mg, 0.6% Si, Fe impurity content is less than 0.2%, and the content of each other impurity is less than 0.1%.

[0068] Step (2) Melting: 1) Place Al-6% μTiB2 precursor, Al-10Mg master alloy, Al-12Si master alloy and industrial pure aluminum into a graphite clay crucible and heat to 720℃, stirring to mix thoroughly; 2) Hold at this temperature for 10 min; 3) Refine with high-purity argon for 5 min; 4) Ultrasonic melt treatment for 3 min; 5) Cast to obtain TiB 2μp / 6201 ceramic-coated aluminum alloy ingot.

[0069] Step (3) Homogenization treatment: TiB 2μp The 6201 ceramic-coated aluminum alloy ingot was held at 560℃ for 12 hours in a muffle furnace, then cooled to 300℃ in the furnace and air-cooled to avoid coarsening of the precipitated phase.

[0070] Step (4) Hot rolling: After homogenization, the ingot is preheated to 460℃ and held for 60 minutes. It is then hot rolled using a twin-roll mill with a total reduction of 30% and a reduction of 5% per pass. The roll speed is 150 r / min.

[0071] Step (5) Solution treatment: The hot-rolled plate is placed in a muffle furnace for solution treatment at a temperature of 560°C and a holding time of 30 minutes, followed by water quenching at room temperature.

[0072] Step (6) Room temperature rolling: The solid solution sample is rolled at room temperature using a twin-roll mill with a total reduction of 78.6% and a reduction of 3.6% per pass. The roll speed is 50 r / min.

[0073] Step (7) Time Limit

[0074] Artificial aging treatment was carried out in an aging furnace at a temperature of 170℃ for 4 hours.

[0075] Example 1

[0076] This embodiment discloses a method for synthesizing nanoscale TiB by ultra-low temperature melting. 2p The preparation method of / 6201 ceramic-coated aluminum alloy includes the following steps:

[0077] Step (1) Raw material preparation

[0078] 1) Al-10Ti master alloy, in which Ti element mainly exists in the form of Al3Ti intermetallic compound; 2) Al-3B master alloy, in which B element exists in the form of AlB2 ceramic particles; 3) Al-10Mg master alloy; 4) Al-12Si master alloy; 5) Industrial pure aluminum (purity >99.7%); 6) Raw materials are dried in a drying oven for 30 minutes at 200℃ before smelting.

[0079] Step (2) Precursor casting preparation

[0080] 1) Place Al-10Ti master alloy, Al-3B master alloy, and industrial pure aluminum in a graphite clay crucible at a ratio of 34.2:51.8:14 and heat to 720℃ in a pit-type melting resistance furnace, then immediately cool the melt to 680℃; 3) Apply mechanical stirring (700 r / min, the same below) for 10 min, melt temperature 660℃; 4) Apply ultrasonic melt treatment (frequency 20 kHz, power 400 W, the same below) for 10 min, melt temperature 660℃; 5) Apply mechanical stirring for 20 min, melt temperature 660℃; 6) Hold at 660℃ for 20 min; 7) Apply ultrasonic melt treatment for 10 min, melt temperature 660℃; 8) Apply mechanical stirring for 20 min, melt temperature 660℃; 9) Refine the melt with high-purity argon gas for 5 min; 10) Remove slag; 11) Cast to obtain Al-5%nTiB2 precursor ingot.

[0081] Step (3) Remelting and dilution

[0082] 1) Al-nTiB2 precursor, Al-10Mg master alloy, Al-12Si master alloy, and industrial pure aluminum were simultaneously placed in a graphite clay crucible at a ratio of 10:6.2:5:78.8 and heated to 720℃, stirring to ensure thorough mixing; 2) The mixture was held at this temperature for 10 min; 3) It was refined with high-purity argon gas for 5 min; 4) It was subjected to ultrasonic melt treatment for 3 min; 5) TiB2 was prepared by casting. 2np / 6201 ceramic-coated aluminum alloy ingot.

[0083] Step (4) Homogenization

[0084] TiB 2np The 6201 ceramic-coated aluminum alloy ingot was held at 560℃ for 12 hours in a muffle furnace, then cooled to 300℃ in the furnace and air-cooled to avoid coarsening of the precipitated phase.

[0085] Step (5) Hot rolling

[0086] After homogenization, the ingot is preheated to 460℃ and held for 60 minutes. It is then hot rolled using a twin-roll mill with a total reduction of 30% and a reduction of 5% per pass. The roll speed is 150 r / min.

[0087] Step (6) Solution treatment

[0088] The hot-rolled plate was placed in a muffle furnace for solution treatment at a temperature of 560°C for 30 minutes, followed by water quenching at room temperature.

[0089] Step (7) Room temperature rolling

[0090] The solid solution sample was rolled at room temperature using a twin-roll mill with a total reduction of 78.6%, a reduction of 3.6% per pass, and a roll speed of 50 r / min.

[0091] Step (8) Time Limit

[0092] Artificial aging treatment was carried out in an aging furnace at a temperature of 170℃ for 4 hours.

[0093] The nanoscale TiB prepared in this embodiment 2p / 6201 ceramic-coated aluminum alloy can be used as a high-strength, high-conductivity aluminum material for power transmission.

[0094] Combining Comparative Example 1, Comparative Example 2, and Example 1, the morphology and size of the synthesized nanoscale TiB2 particles, as well as the composition of 6201 aluminum alloy and TiB2, are analyzed. 2μp / 6201 ceramic-aluminum alloy and TiB 2np The mechanical properties, electrical conductivity, and tensile fracture morphology of / 6201 ceramic-aluminum alloy are as follows: Figures 1-4 As shown:

[0095] Figure 1The figures show the morphology and size of ceramic particles in the Al-nTiB2 precursor prepared in Example 1. Figure (a) is a scanning electron microscope (SEM) image of the 3D morphology of the particles after deep etching, Figure (b) is a magnified image of Figure (a), and Figure (c) is a transmission electron microscope (TEM) image of the particle morphology. As can be seen from the figures, in addition to the relatively mature hexagonal prism-shaped TiB2 ceramic particles of several hundred nanometers, a large number of nano-sized TiB2 particles are attached to them. The TEM images show that the nano-sized particles also exhibit a regular hexagonal shape, with sizes ranging from tens to hundreds of nanometers, and many even smaller particles can be observed. In summary, the ultra-low temperature melting synthesis of nano-sized TiB2 particles has a large size range, from tens to hundreds of nanometers, and the large number of tens-nanometer particles plays a crucial strengthening role in ceramic-aluminum alloys.

[0096] Figure 2 6201 aluminum alloy and TiB prepared for Comparative Example 1, Comparative Example 2 and Example 1 2μp / 6201 ceramic-coated aluminum alloy and TiB 2np The stress-strain curves of 6201 ceramic-coated aluminum alloy are shown in the figure. As can be seen from the figure, the tensile strength of 6201 aluminum alloy is the lowest, only 325 MPa. Introducing 0.5% micron-sized particles increases the tensile strength to 334.8 MPa, but the improvement is not significant. However, introducing 0.5% nano-sized particles increases the tensile strength to 380.1 MPa, showing a very significant improvement. This indicates that the strength increase brought about by particle refinement is substantial. Regarding elongation after fracture, the elongation after fracture of 6201 aluminum alloy is 7.8%. Introducing 0.5% micron-sized particles does not decrease the strength but increases it to 9.6%. This is because micron-sized particles act as heterogeneous nucleation points to refine the grains, thereby increasing the elongation. Introducing 0.5% nano-sized particles decreases the elongation after fracture, but increases the uniform elongation, meaning that nano-sized particles can achieve a synergistic improvement in strength and ductility.

[0097] Figure 3 6201 aluminum alloy and TiB prepared for Comparative Example 1, Comparative Example 2 and Example 1 2μp / 6201 ceramic-coated aluminum alloy and TiB 2npThe electrical conductivity of 6201 ceramic-coated aluminum alloy is shown in the figure. As can be seen, the electrical conductivity of 6201 aluminum alloy is only 49.5% IACS. Introducing 0.5% micron-sized particles only slightly improves the conductivity, but introducing 0.5% nano-sized particles significantly improves it. This is because the size of nano-sized particles and precipitated phases is almost on the same order of magnitude. The large number of nano-sized particles introduces numerous particle / matrix phase interfaces. Simultaneously, during heat treatment and deformation, due to the difference in elastic moduli between the two phases, a large number of CTE dislocations and geometrically necessary dislocations are generated around the particles. These dislocations and phase interfaces become channels for the rapid diffusion of solid-solution elements, thereby promoting the precipitation process and allowing solid-solution atoms to precipitate as much as possible, reducing their damage to electrical conductivity.

[0098] Figure 4 6201 aluminum alloy and TiB prepared for Comparative Example 1, Comparative Example 2 and Example 1 2μp / 6201 ceramic-coated aluminum alloy and TiB 2np Scanning electron microscope (SEM) images of the fracture morphology of 6201 ceramic-coated aluminum alloy. The images show that the fracture behavior of both 6201 aluminum alloy and the two ceramic-coated aluminum alloys is ductile fracture, producing numerous ductile fracture dimples. The difference lies in the size of the dimples: the 6201 aluminum alloy has larger dimples, while the ceramic-coated aluminum alloys have very small and deep dimples, particularly those in TiB. 2np / 6201 ceramic-aluminum alloy not only exists with TiB 2μp The / 6201 ceramic-coated aluminum alloy exhibits the same micron-sized dimples as other ceramic-coated aluminum alloys, but also contains a large number of nano-sized dimples. This is because the introduction of nano-sized particles leads to the formation of numerous small-angle grain boundaries in the matrix, and the subgrain size is extremely fine, thus producing a significant strengthening effect on the matrix. In contrast, TiB... 2μp The / 6201 ceramic-coated aluminum alloy has deep dimples, which is also the reason for its high elongation.

[0099] Finally, it should be noted that the above embodiments are only used to illustrate the technical solutions of the present invention, and not to limit them; although the present invention has been described in detail with reference to the foregoing embodiments, those skilled in the art should understand that modifications can still be made to the technical solutions described in the foregoing embodiments, or equivalent substitutions can be made to some or all of the technical features; and these modifications or substitutions do not cause the essence of the corresponding technical solutions to deviate from the scope of the technical solutions of the embodiments of the present invention.

Claims

1. A nanoscale TiB 2p The method for synthesizing 6201 ceramic-aluminum alloy by ultra-low temperature melting is characterized by... Includes the following steps: Step (1) Raw material preparation: 1) Al-10Ti master alloy; 2) Al-3B master alloy; 3) Al-10Mg master alloy; 4) Al-12Si master alloy; 5) Industrial pure aluminum; Step (2) Precursor casting preparation: 1) The Al-10Ti master alloy and Al-3B master alloy are mixed according to a B / Ti stoichiometric ratio of 2.0 to 2.1; 2) The two master alloys are placed in a graphite clay crucible and heated to 710 to 720°C in a pit-type melting resistance furnace, and the melt is immediately cooled to 670 to 680°C; 3) Mechanical stirring is applied for 5 to 10 minutes, and the melt temperature is 660 to 670°C; 4) Ultrasonic melt treatment is applied for 8 to 10 minutes. 5) Apply mechanical stirring for 15-20 min, melt temperature 660-670℃; 6) Hold at 660-670℃ for 20 min; 7) Apply ultrasonic melt treatment for 8-10 min, melt temperature 660-670℃; 8) Apply mechanical stirring for 15-20 min, melt temperature 660-670℃; 9) Refine the melt by introducing high-purity argon gas for 3-5 min; 10) Remove slag; 11) Cast to obtain Al-nTiB2 precursor; Step (3) Remelting and dilution: 1) The Al-nTiB2 precursor, Al-10Mg master alloy, Al-12Si master alloy and industrial pure aluminum are placed in a graphite clay crucible at a weight ratio of 9-10:5.2-6.2:4.8-5:78.8-81 and heated to 710-720℃, and stirred to mix thoroughly; 2) Hold at this temperature for 5-10 min; 3) Refine with high-purity argon gas for 3-5 min; 4) Perform ultrasonic melt treatment for 3-5 min; 5) Cast to obtain nano-sized TiB2. 2p / 6201 porcelain-coated aluminum alloy ingot; Step (4) Homogenization treatment; Step (5) Hot rolling; Step (6) Solution treatment; Step (7) Room temperature rolling; Step (8) time limit.

2. The nanoscale TiB according to claim 1 2p The method for synthesizing 6201 ceramic-aluminum alloy by ultra-low temperature melting is characterized by... The content of TiB2 ceramic particles in the Al-nTiB2 precursor prepared in step (2) is 4.5-5.5%.

3. The nanoscale TiB according to claim 1 2p The method for synthesizing 6201 ceramic-aluminum alloy by ultra-low temperature melting is characterized by... The nanoscale TiB prepared in step (3) 2p The TiB2 ceramic particle content in the 6201 ceramic-aluminum alloy ingot is 0.45-0.55%.

4. The nanoscale TiB according to claim 1 2p The method for synthesizing 6201 ceramic-aluminum alloy by ultra-low temperature melting is characterized by... The nanoscale TiB prepared in step (3) 2p The 6201 ceramic-coated aluminum alloy ingot contains 0.6-0.9% Mg, 0.5-0.9% Si, less than 0.2% Fe, and less than 0.1% of each other impurity.

5. The nanoscale TiB according to claim 1 2p The method for synthesizing 6201 ceramic-aluminum alloy by ultra-low temperature melting is characterized by... In steps (2) and (3), all raw materials are dried in a drying oven for 30 to 60 minutes before smelting at a temperature of 200 to 220°C.

6. The nanoscale TiB according to claim 1 2p The method for synthesizing 6201 ceramic-aluminum alloy by ultra-low temperature melting is characterized by... Step (4) Homogenization treatment: The ceramic-coated aluminum alloy ingot is held in a muffle furnace at 540-570℃ for 12-24 hours, then cooled to 250-300℃ in the furnace and air-cooled to avoid coarsening of the precipitated phase; And / or, step (5) hot rolling: after homogenization treatment, the ingot is preheated to 450-470℃ and held for 30-60 minutes. Hot rolling is carried out using a twin-roll mill with a total reduction of 20-30%, a reduction of 3-5% per pass, and a roll speed of 100-150 r / min. And / or, step (6) solution treatment: the hot-rolled plate is placed in a muffle furnace for solution treatment at a temperature of 550-570°C and a holding time of 30-60 min, followed by water quenching at room temperature; And / or, step (7) room temperature rolling: the solution-treated product is rolled at room temperature using a twin-roll mill, with a total reduction of 75-80%, a reduction of 3-4% per pass, and a roll speed of 50-100 r / min; And / or, step (8) aging: artificial aging treatment is carried out in an aging furnace at a temperature of 160-170℃ for 3-5 hours.

7. A nanoscale TiB 2p / 6201 ceramic-coated aluminum alloy, characterized in that... It is prepared by the method described in any one of claims 1-6.

8. The nanoscale TiB according to claim 7 2p / 6201 ceramic-coated aluminum alloy, characterized in that... The nanoscale TiB 2p The 6201 ceramic-coated aluminum alloy comprises the following components by weight: TiB2 0.45–0.55%; Mg 0.6–0.9%; Si 0.5-0.9%; The Fe content of impurities is less than 0.2%; the content of each of the other impurities is less than 0.1%. The margin is Al.

9. The nanoscale TiB according to claim 7 2p / 6201 ceramic-coated aluminum alloy, characterized in that... The nanoscale TiB 2p The tensile strength of the 6201 ceramic-coated aluminum alloy is 375–380 MPa, the elongation after fracture is 6.8–7.1%, and the electrical conductivity is 56.2–56.4% IACS.

10. A nanoscale TiB according to any one of claims 7-9 2p Applications of / 6201 ceramic-coated aluminum alloy in the field of high-strength, high-conductivity aluminum materials.

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