A high-strength and high-toughness aluminum alloy for low-temperature environments, its preparation method and application

Abstract

This invention relates to the field of aluminum alloy materials, and more particularly to a high-strength and high-toughness aluminum alloy for low-temperature environments, its preparation method, and its applications. This invention achieves optimized microstructure and synergistic effects of the strengthening phases in the aluminum alloy at low temperatures by rationally designing the alloy composition and employing a two-stage heat treatment process to construct high-density transition metal nanoclusters and nano-sized reinforcing phases within the alloy, while simultaneously controlling the grain size distribution. Through the above design, the high-strength and high-toughness aluminum alloy prepared by this invention exhibits excellent mechanical properties at 77K, exceeding the low-temperature mechanical properties of traditional aluminum alloys at 77K.

Description

Technical Field

[0001] This invention relates to the field of aluminum alloy materials, and in particular to a high-strength and high-toughness aluminum alloy for low-temperature environments, its preparation method, and its application. Background Technology

[0002] With the rapid development of high technologies such as aerospace, superconductivity, and liquefied natural gas (LNG) storage, the demand for high-performance materials for cryogenic environments is becoming increasingly urgent. For example, critical equipment such as rocket liquid fuel tanks and cryogenic storage tanks operate under extreme low-temperature conditions, placing higher demands on the strength, toughness, and service reliability of materials. Aluminum alloys are characterized by low density, good toughness, and high strength. Face-centered cubic aluminum alloys exhibit good low-temperature performance and do not exhibit a ductile-brittle transition, thus making them widely used in cryogenic applications.

[0003] Currently, commonly used low-temperature aluminum alloy systems include Al-Mg, Al-Zn-Mg-Cu, Al-Cu, and Al-Li. Studies have shown that they typically exhibit a simultaneous increase in strength and plasticity at low temperatures, known as the "dual-increase effect," which is a significant advantage over other metals. This effect is closely related to grain size and microstructure characteristics. Common approaches to improving the low-temperature performance of aluminum alloys include preparing aluminum-based composites and using multi-stage heat treatment processes to control the microstructure. However, the distribution of reinforcing particles in aluminum-based composites is often uneven, limiting their formability. Furthermore, complex multi-stage heat treatment processes are time-consuming and have poor repeatability, making them unsuitable for large-scale preparation and engineering applications. Therefore, further improving the low-temperature strength and toughness of aluminum alloys through rational microstructure design and preparation processes is of great significance for promoting the research and application of low-temperature performance. Summary of the Invention

[0004] Therefore, the technical problem to be solved by the present invention is to overcome the problem of poor low-temperature performance in the prior art, thereby providing an aluminum alloy with high strength and toughness at low temperatures.

[0005] To address the aforementioned technical problems, this invention provides a high-strength and high-toughness aluminum alloy for low-temperature environments and its preparation method, thereby solving one or more technical problems existing in the prior art and providing a new method for lightweight high-strength and high-toughness aluminum alloy materials for low-temperature environments.

[0006] This invention provides a high-strength and high-toughness aluminum alloy for low-temperature environments, wherein the high-strength and high-toughness aluminum alloy for low-temperature environments contains nanoclusters with a size of 2-20 nm, wherein the nanoclusters are composed of Al and alloying element I, wherein the alloying element I is selected from one or more of Mn, Zr, Cr, Ti, Sc, V, Mo and Fe;

[0007] The high-strength and high-toughness aluminum alloy for low-temperature environments also contains a reinforcing phase with a size of 10-50 nm; the reinforcing phase is composed of Al and alloying element II, which is selected from one or more of Cu, Mg and Si;

[0008] In the high-strength and high-toughness aluminum alloy for low-temperature environments, the proportion of grains with a size of less than 1 μm is 20%-30%, the proportion of grains with a size of 1-5 μm is 30%-50%, and the proportion of grains with a size of 5-10 μm is 20%-50%.

[0009] This invention promotes the dispersed distribution of dislocations during alloy deformation at low temperatures by synergistically regulating the size range of nanoclusters and reinforcing phases, combined with fine grain structure. It also inhibits the weakening of dislocation mobility at low temperatures, which leads to excessive localization, effectively delaying the initiation of deformation cracks and enabling the alloy to achieve high strength and toughness at low temperatures.

[0010] Preferably, the high-strength and high-toughness aluminum alloy for low-temperature environments is composed of the following elements by weight percentage: 1-8% Si, 0.1-1% Mg, 0.5-3% Cu, 0.2-3% Mn, 0.1-3% Zr, 0.1-1% Cr, 0.1-0.8% Ti, 0.1-2% Sc, 0.1-1% V, 0.1-2% Mo, 0.1-3% Fe, with the balance being Al.

[0011] Preferably, the number density of the nanoclusters is not less than 5 × 10⁻⁶. 13 / m 2 The number density of the reinforcing phase is not less than 1×10 13 / m 2 .

[0012] Preferably, the high-strength and high-toughness aluminum alloy for low-temperature environments has a yield strength of not less than 400 MPa, a tensile strength of not less than 650 MPa, and an elongation of not less than 15% at 77 K.

[0013] This invention also provides a method for preparing the above-mentioned high-strength and high-toughness aluminum alloy for low-temperature environments, wherein the alloy contains high-density nanoclusters of transition metal elements, comprising the following steps:

[0014] S11: Al, Mg, Cu and a master alloy are mixed and smelted to obtain a molten alloy; the molten alloy is composed of the following elements by weight percentage: 1-8% Si, 0.1-1% Mg, 0.5-3% Cu, 0.2-3% Mn, 0.1-3% Zr, 0.1-1% Cr, 0.1-0.8% Ti, 0.1-2% Sc, 0.1-1% V, 0.1-2% Mo, 0.1-3% Fe, with the balance being Al;

[0015] S12: The molten alloy is atomized and then sieved to obtain alloy powder with a particle size of 20-70 μm;

[0016] S13: Solidify the alloy powder into shape, and then use 10 4 -10 6 Cooling at a rate of K / s yields a solidified alloy;

[0017] S14: The solidified alloy is subjected to aging treatment at 100-150℃ for 2-10 h and heat treatment at 300-400℃ for 2-10 h in sequence to obtain the high strength and toughness aluminum alloy for low temperature environment.

[0018] Preferably, in step S11, the melting is carried out under vacuum conditions.

[0019] Preferably, in step S11, the melting temperature is 760-780℃ and the time is 20-40 min.

[0020] Preferably, the intermediate alloy comprises Al-10%Si, Al-5%Fe, Al-5%Mn, Al-5%Zr, Al-5%Cr, Al-3%Ti, Al-3%Sc, Al-5%V, and Al-5%Mo.

[0021] Preferably, in step S12, the atomization method is: high-pressure atomization spraying under argon gas conditions.

[0022] Preferably, in step S13, the solidification molding method is spray molding or 3D printing.

[0023] Preferably, in step S14, the heating rate of the heat treatment is 2-5℃ / min.

[0024] The present invention also provides the application of the above-mentioned high-strength and high-toughness aluminum alloy for low-temperature environments as a low-temperature storage and transportation material, wherein the low-temperature storage and transportation material is used at a temperature of 77K.

[0025] Compared with the prior art, the above-described technical solution of the present invention has the following advantages:

[0026] This invention achieves optimized microstructure and synergistic effect of strengthening phases in aluminum alloys at low temperatures by rationally designing the alloy composition and employing a two-stage heat treatment process to construct high-density transition element nanoclusters and reinforcing phases within the alloy, while simultaneously controlling grain size distribution. Through this design, the high-strength and high-toughness aluminum alloy prepared by this invention exhibits excellent mechanical properties at 77K, exceeding the low-temperature mechanical properties of traditional aluminum alloys at 77K. Attached Figure Description

[0027] To make the content of this invention easier to understand, the invention will be further described in detail below with reference to specific embodiments and accompanying drawings.

[0028] Figure 1 This is a microstructure diagram of the aluminum alloy prepared in Example 1 of the present invention;

[0029] Figure 2 This is a microstructure diagram of the aluminum alloy prepared in Example 2 of the present invention;

[0030] Figure 3 This is a microstructure diagram of the aluminum alloy prepared in Example 3 of the present invention. Detailed Implementation

[0031] The present invention will be further described below with reference to the accompanying drawings and specific embodiments, so that those skilled in the art can better understand and implement the present invention. However, the embodiments described are not intended to limit the present invention.

[0032] In the following examples and comparative examples, the test method for grain size range and ratio is electron backscatter diffraction (EBSD), and the test method for nanoclusters is transmission electron microscopy (TEM).

[0033] Tensile specimens were prepared according to GB / T228.3-2019 standard. The tensile tests were performed on a MEST SANS CMT5000 low-temperature mechanical testing machine at a time of 0.001s. -1 The specimen was stretched at a constant strain rate until it fractured. The test environment temperature was maintained at 77K by liquid nitrogen immersion to obtain experimental data on yield strength, tensile strength and elongation.

[0034] Example 1:

[0035] This embodiment discloses a high-strength and high-toughness aluminum alloy for low-temperature environments and its preparation method. The alloy composition and weight percentages are as follows: Si 6.47%, Mg 0.51%, Cu 2.58%, Mn 1.26%, Zr 1.15%, Cr 0.23%, Ti 0.22%, Sc 0.43%, V 0.35%, Mo 1.36%, Fe 0.11%, and the remainder is Al.

[0036] In this embodiment, the aluminum alloy with the above-mentioned composition is prepared using a high-speed cooling 3D printing method, with a cooling rate of 10. 6 K / s, the specific steps are as follows:

[0037] (1) Preparation of alloy powder

[0038] First, high-purity Al, pure Mg, and pure Cu are mixed with intermediate alloys Al-10%Si, Al-5%Fe, Al-5%Mn, Al-5%Zr, Al-5%Cr, Al-3%Ti, Al-3%Sc, Al-5%V, and Al-5%Mo in a specific ratio to obtain the target composition. The mixture is then melted at 780°C for 30 minutes in a vacuum induction melting apparatus (model: VIM 02-70, ALD Vacuum Technologies GmbH) to ensure complete melting and homogenization of the chemical composition.

[0039] Subsequently, alloy powder was prepared using high-pressure inert gas atomization technology. Specifically, molten metal was injected through a nozzle and atomized into fine droplets under the action of a high-pressure argon gas flow. During this process, the nozzle inner diameter was 1 mm, the overpressure applied to the top of the melt was 40 kPa, the melt mass flow rate was 87.97 kg / h, the atomizing gas pressure was 2.0 MPa, the gas mass flow rate was 200 kg / h, the gas-liquid mass flow rate ratio was 2.27, and the melt superheat was 150 K. After atomization, approximately spherical alloy powder was obtained, and the collected powder was then sieved to obtain a particle size distribution in the range of 20-50 μm.

[0040] (2) 3D printing

[0041] A selective laser melting (SLM) 3D printer, model HBD-150, was used for sample printing. The printing process was conducted in an inert atmosphere filled with high-purity argon (oxygen content <100ppm) to prevent oxidation. The printing parameters were set as follows: laser power 280W, scanning speed 1600mm / s, laser spot diameter 0.1mm, scanning interval 0.12mm, and layer thickness 0.03mm. To reduce thermal stress and residual strain, the scanning direction for each layer was rotated 67° relative to the previous layer. After the powder was heated and melted by the laser, it rapidly solidified on a cooling substrate at a cooling rate of 10... 6 K / s.

[0042] (3) Heat treatment

[0043] The printed alloy sample was first aged at 150℃ for 8 hours, and then heated to 300℃ at a heating rate of 5℃ / min for 2 hours to finally obtain the prepared alloy.

[0044] The resulting aluminum alloy microstructure is as follows Figure 1 As shown. Observation results indicate that the alloy in this embodiment contains fine transition metal nanoclusters within its grains, with a number density and average size of 7.2 ± 1.1 × 10⁻⁶. 13 / m 2The average grain size is 10.1 ± 2.2 nm, and the constituent elements are Al, Mn, Zr, Cr, Ti, Sc, V, Mo, and Fe. Grains smaller than 1 μm account for 30% of the alloy, grains with a size of 1-5 μm account for 50%, and grains with a size of 5-10 μm account for 20%, with an average grain size of 3.0 μm ± 0.9 μm. The strengthening phase has an average size of 35 nm, is composed of Al, Cu, Mg, and Si, and has a number density of 1.5 × 10⁻⁶. 13 / m 2 The alloy sheet was subjected to a mechanical tensile test at 77K, and its yield strength was 434MPa, tensile strength was 683MPa, and elongation was 17.8%.

[0045] Example 2:

[0046] This embodiment discloses a high-strength and high-toughness aluminum alloy for low-temperature environments and its preparation method. The alloy composition and weight percentages are as follows: Si 6.57%, Mg 0.46%, Cu 2.29%, Mn 1.15%, Zr 0.98%, Cr 0.36%, Ti 0.46%, Sc 0.14%, V 0.31%, Mo 1.13%, Fe 0.17%, and the remainder is Al.

[0047] In this embodiment, the aluminum alloy with the above-mentioned composition is prepared using a high-speed cooling 3D printing method, with a cooling rate of 10. 5 K / s, the specific steps are as follows:

[0048] (1) Preparation of alloy powder

[0049] First, high-purity Al, pure Mg, and pure Cu are mixed with intermediate alloys Al-10%Si, Al-5%Fe, Al-5%Mn, Al-5%Zr, Al-5%Cr, Al-3%Ti, Al-3%Sc, Al-5%V, and Al-5%Mo in a specific ratio to obtain the target composition. The mixture is then melted at 760°C for 30 minutes in a vacuum induction melting apparatus (model: VIM 02-70, ALD Vacuum Technologies GmbH) to ensure complete melting and homogenization of the chemical composition.

[0050] Subsequently, alloy powder was prepared using high-pressure inert gas atomization technology. Specifically, molten metal was injected through a nozzle and atomized into fine droplets under the action of a high-pressure argon gas flow. During this process, the nozzle inner diameter was 3 mm, the overpressure applied to the top of the melt was 30 kPa, the melt mass flow rate was 139.2 kg / h, the atomizing gas pressure was 2.0 MPa, the gas mass flow rate was 200 kg / h, the gas-liquid mass flow rate ratio was 1.44, and the melt superheat was 150 K. After atomization, approximately spherical alloy powder was obtained, and the collected powder was then sieved to obtain a particle size distribution in the range of 30-70 μm.

[0051] (2) 3D printing

[0052] A selective laser melting (SLM) 3D printer, model HBD-150, was used for sample printing. The printing process was conducted in an inert atmosphere filled with high-purity argon (oxygen content <100ppm) to prevent oxidation. The printing parameters were set as follows: laser power 380W, scanning speed 1800mm / s, laser spot diameter 0.1mm, scanning interval 0.12mm, and layer thickness 0.03mm. To reduce thermal stress and residual strain, the scanning direction for each layer was rotated 67° relative to the previous layer. After the powder was melted by the laser, it rapidly solidified on a cooling substrate at a cooling rate of 10... 5 K / s.

[0053] (3) Heat treatment

[0054] The printed alloy sample was first aged at 120℃ for 6 hours, and then heated to 300℃ at a heating rate of 5℃ / min for 4 hours to finally obtain the prepared alloy.

[0055] The resulting aluminum alloy microstructure is as follows Figure 2 As shown. Observation results indicate that the alloy in this embodiment contains fine transition metal nanoclusters within its grains, with a number density and average size of 6.1 ± 1.0 × 10⁻⁶. 13 / m 2 The average grain size is 15.6 ± 2.8 nm, and the constituent elements are Al, Mn, Zr, Cr, Ti, Sc, V, Mo, and Fe. The alloy has 25% grains smaller than 1 μm, 50% grains between 1 and 5 μm, and 25% grains between 5 and 10 μm, with an average grain size of 5.1 ± 2.2 μm. The strengthening phase has an average size of 40 nm, is composed of Al, Cu, Mg, and Si, and has a number density of 1.7 × 10⁻⁶. 13 / m 2 The alloy sheet was subjected to mechanical tensile testing at 77K, and its yield strength was 411MPa, tensile strength was 653MPa, and elongation was 15.8%.

[0056] Example 3:

[0057] This embodiment discloses a high-strength and high-toughness aluminum alloy for low-temperature environments and its preparation method. The alloy composition and weight percentages are as follows: Si 5.97%, Mg 0.37%, Cu 1.39%, Mn 1.35%, Zr 1.38%, Cr 0.44%, Ti 0.32%, Sc 0.53%, V 0.23%, Mo 0.96%, Fe 0.13%, and the remainder is Al.

[0058] In this embodiment, the aluminum alloy with the above-mentioned composition is prepared using a high-speed cooling 3D printing method, with a cooling rate of 10. 5 K / s, the specific steps are as follows:

[0059] (1) Preparation of alloy powder

[0060] First, high-purity Al, pure Mg, and pure Cu are mixed with intermediate alloys Al-10%Si, Al-5%Fe, Al-5%Mn, Al-5%Zr, Al-5%Cr, Al-3%Ti, Al-3%Sc, Al-5%V, and Al-5%Mo in a specific ratio to obtain the target composition. The mixture is then melted at 760°C for 30 minutes in a vacuum induction melting apparatus (model: VIM 02-70, ALD Vacuum Technologies GmbH) to ensure complete melting and homogenization of the chemical composition.

[0061] Subsequently, alloy powder was prepared using high-pressure inert gas atomization technology. Specifically, molten metal was injected through a nozzle and atomized into fine droplets under the action of a high-pressure argon gas flow. During this process, the nozzle inner diameter was 2 mm, the overpressure applied to the top of the melt was 35 kPa, the melt mass flow rate was 102.27 kg / h, the atomizing gas pressure was 2.0 MPa, the gas mass flow rate was 200 kg / h, the gas-liquid mass flow rate ratio was 1.96, and the melt superheat was 150 K. After atomization, approximately spherical alloy powder was obtained, and the collected powder was then sieved to obtain a particle size distribution in the range of 20-60 μm.

[0062] (2) 3D printing

[0063] A selective laser melting (SLM) 3D printer, model HBD-150, was used for sample printing. The printing process was conducted in an inert atmosphere filled with high-purity argon (oxygen content <100ppm) to prevent oxidation. The printing parameters were set as follows: laser power 340W, scanning speed 1600mm / s, laser spot diameter 0.1mm, scanning interval 0.12mm, and layer thickness 0.03mm. To reduce thermal stress and residual strain, the scanning direction for each layer was rotated 67° relative to the previous layer. After the powder was melted by the laser, it rapidly solidified on a cooling substrate at a cooling rate of 10... 5 K / s.

[0064] (3) Heat treatment

[0065] The printed alloy sample was first aged at 120℃ for 8 hours, and then heated to 350℃ at a heating rate of 3℃ / min for 1 hour to finally obtain the prepared alloy.

[0066] The resulting aluminum alloy microstructure is as follows Figure 3 As shown. Observation results indicate that the alloy in this embodiment contains fine transition metal nanoclusters within its grains, with a number density and average size of 6.3 ± 0.9 × 10⁻⁶. 13 / m 2 The average grain size is 15.6 ± 2.6 nm, and the constituent elements are Al, Mn, Zr, Cr, Ti, Sc, V, Mo, and Fe. The alloy has 20% grains smaller than 1 μm, 40% grains with a size of 1-5 μm, and 40% grains with a size of 5-10 μm, with an average grain size of 4.1 μm ± 1.4 μm. The strengthening phase has an average size of 25 nm, is composed of Al, Cu, Mg, and Si, and has a number density of 1.6 × 10⁻⁶. 13 / m 2 The alloy sheet was subjected to mechanical tensile testing at 77K, and its yield strength was 421MPa, tensile strength was 662MPa, and elongation was 16.8%.

[0067] Comparative Example 1:

[0068] The alloy composition and weight percentages are as follows: Si 5.97%, Mg 0.37%, Cu 1.39%, with the remainder being Al.

[0069] In this embodiment, the aluminum alloy with the above-mentioned composition is prepared using a high-speed cooling 3D printing method, with a cooling rate of 10. 5 K / s, the specific steps are as follows:

[0070] (1) Preparation of alloy powder

[0071] First, high-purity Al, pure Mg, and pure Cu are mixed with the master alloy Al-10%Si in a specific ratio to obtain the target composition. The mixture is then melted at 760°C for 30 minutes in a vacuum induction melting apparatus (model: VIM 02-70, ALD Vacuum Technologies GmbH) to ensure complete melting and homogenization of the chemical composition.

[0072] Subsequently, alloy powder was prepared using high-pressure inert gas atomization technology. Specifically, molten metal was injected through a nozzle and atomized into fine droplets under the action of a high-pressure argon gas flow. During this process, the nozzle inner diameter was 2 mm, the overpressure applied to the top of the melt was 35 kPa, the melt mass flow rate was 102.27 kg / h, the atomizing gas pressure was 2.0 MPa, the gas mass flow rate was 200 kg / h, the gas-liquid mass flow rate ratio was 1.96, and the melt superheat was 150 K. After atomization, approximately spherical alloy powder was obtained, and the collected powder was then sieved to obtain a particle size distribution in the range of 20-60 μm.

[0073] (2) 3D printing

[0074] A selective laser melting (SLM) 3D printer, model HBD-150, was used for sample printing. The printing process was carried out in an inert atmosphere filled with high-purity argon (oxygen content <100ppm) to prevent oxidation. The printing parameters were set as follows: laser power 340W, scanning speed 1600mm / s, laser spot diameter 0.1mm, scanning interval 0.12mm, and layer thickness 0.03mm. To reduce thermal stress and residual strain, the scanning direction of each layer was rotated 67° relative to the previous layer.

[0075] (3) Heat treatment

[0076] The printed alloy sample was first aged at 120℃ for 8 hours, and then heated to 350℃ at a heating rate of 3℃ / min for 1 hour to finally obtain the prepared alloy.

[0077] The resulting aluminum alloy exhibited a uniform grain distribution with an average grain size of 4.1 μm ± 1.4 μm. Tensile testing of the alloy sheet at 77 K revealed a yield strength of 320 MPa, a tensile strength of 460 MPa, and an elongation of 9.2%.

[0078] The technical content and features of the present invention have been disclosed above. However, those skilled in the art may still make various substitutions and modifications that do not depart from the spirit of the present invention based on the teachings and disclosures of the present invention. Therefore, the scope of protection of the present invention should not be limited to the content disclosed in the embodiments, but should include various substitutions and modifications that do not depart from the present invention, and should be covered by the claims of this patent application.

Claims

1. A high strength-to-toughness aluminum alloy for cryogenic environments, characterized by: The low-temperature environment high-toughness aluminum alloy contains nanoclusters with a size of 2-20 nm, the nanoclusters are composed of Al and alloying element I, and the alloying element I is selected from one or more of Mn, Zr, Cr, Ti, Sc, V, Mo and Fe; The low-temperature environment high-toughness aluminum alloy also contains a strengthening phase with a size of 10-50 nm; the strengthening phase is composed of Al and alloying element II, and the alloying element II is selected from one or more of Cu, Mg and Si; In the low-temperature environment high-toughness aluminum alloy, the proportion of grains with a size of less than 1 μm is 20%-30%, the proportion of grains with a size of 1-5 μm is 30%-50%, and the proportion of grains with a size of 5-10 μm is 20%-50%; The preparation method of the low-temperature environment high-toughness aluminum alloy comprises the following steps: S11: Al, Mg, Cu and intermediate alloy are mixed and then melted to obtain a molten alloy; the molten alloy is composed of the following elements in percentage by weight: 1-8% Si, 0.1-1% Mg, 0.5-3% Cu, 0.2-3% Mn, 0.1-3% Zr, 0.1-1% Cr, 0.1-0.8% Ti, 0.1-2% Sc, 0.1-1% V, 0.1-2% Mo, 0.1-3% Fe, and the balance of Al; S12: The molten alloy is atomized and then sieved to obtain an alloy powder with a particle size of 20-70 μm; S13: solidification forming the alloy powder, and cooling at a rate of 10 4 -10 6 K / s to obtain a solidified alloy; the method of solidification forming is spray forming or 3D printing preparation; S14: The solidified alloy is subjected to aging treatment at 100-150 ℃ for 2-10 h and heat treatment at 300-400 ℃ for 2-10 h in sequence to obtain the low-temperature environment high-toughness aluminum alloy.

2. The high strength to toughness aluminum alloy for cryogenic environments of claim 1, wherein: The number density of the nanoclusters is not less than 5×10 13 / m 2 , and the number density of the strengthening phase is not less than 1×10 13 / m 2 .

3. The high-strength high-ductility aluminum alloy for cryogenic environments of claim 1, wherein: The low-temperature environment high-toughness aluminum alloy has a yield strength of not less than 400 MPa, a tensile strength of not less than 650 MPa and an elongation of not less than 15% at 77 K.

4. The high-strength high-toughness aluminum alloy for cryogenic environments of claim 1, wherein: In the step S11, the melting temperature is 760-780 ℃.

5. The high-strength high-toughness aluminum alloy for cryogenic environments of claim 1, wherein: The intermediate alloy includes Al-10% Si, Al-5% Fe, Al-5% Mn, Al-5% Zr, Al-5% Cr, Al-3% Ti, Al-3% Sc, Al-5% V and Al-5% Mo.

6. The high-strength toughness aluminum alloy for cryogenic environments of claim 1, wherein: In the step S12, the atomization method is high-pressure atomization spraying under argon.

7. The high-strength toughness aluminum alloy for cryogenic environments of claim 1, wherein: In the step S14, the heating rate of the heat treatment is 2-5 ℃ / min.

8. Use of the high-strength high-toughness aluminum alloy for a low temperature environment according to any one of claims 1 to 3 as a low temperature storage and transportation material, characterized in that, The temperature of the low-temperature storage and transportation material in application is 77 K.

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