An aluminum alloy simulating the effect of neutron irradiation-induced transmutation of silicon and a manufacturing method thereof

Abstract

An aluminum alloy simulating the effect of neutron irradiation-induced silicon transmutation and its manufacturing method belong to the field of aluminum alloys. Among them, the manufacturing method of the aluminum alloy simulating the effect of neutron irradiation-induced silicon transmutation includes the following steps: determining the Si element content in the alloy according to the aluminum alloy state to be simulated and preparing a supersaturated solid solution raw material with the corresponding composition, using powder metallurgy technology to obtain an aluminum alloy bar and obtaining an aluminum alloy structure simulating the generation of silicon transmutation effect through heat treatment. This aluminum alloy preparation method can prepare a simulated alloy to effectively simulate the precipitation phase structure formed by the transmutation reaction after the aluminum alloy is irradiated by neutrons for a long time, which plays an important role in studying the influence of irradiation transmutation products on the properties of aluminum alloys, alleviates the current situation that the irradiation performance evaluation of metal materials with solid transmutation products highly depends on neutron irradiation resources, improves the research efficiency, and thus improves the design level and safety performance of aluminum alloy structural parts in research reactors.

Description

Technical Field

[0001] The present invention belongs to the field of aluminum alloys, and particularly relates to an aluminum alloy simulating the effect of neutron irradiation-induced silicon transmutation and a manufacturing method thereof. Background Art

[0002] 5-series aluminum alloys have good neutron economy, low nuclear heating rate, fast heat dissipation, and at the same time have good corrosion resistance and processing performance. Therefore, they are widely used in the manufacture of research reactor structural components. When serving under neutron irradiation conditions for a long time, the aluminum alloy will become embrittled due to neutron irradiation, affecting the structural strength and reliability. The main damage mechanism for the deterioration of the mechanical properties of aluminum alloys caused by neutron irradiation is solid transmutation damage. After Al atoms capture neutrons, they are transformed into Si atoms, and Si and the main solid solution element Mg of 5-series aluminum alloys will form dispersed precipitation phases (such as Mg2Si, Si single substance, etc.) in the aluminum alloy matrix, resulting in rapid hardening and embrittlement of the aluminum alloy. Therefore, studying the performance changes of aluminum alloys under neutron irradiation conditions is very important for the safety design of research reactors. The neutron fluence rate of research reactors is high and the service life is long. The total fluence received by materials at the end of the service life is high. It takes an extremely long time to reach the neutron fluence at the end of the service life of the research reactor by using neutron irradiation tests for material performance evaluation, and the operability is low. Therefore, providing a method for preparing aluminum alloys to simulate the transmutation Si effect after aluminum alloy irradiation has positive significance for improving the efficiency of aluminum alloy irradiation performance research. Summary of the Invention

[0003] The purpose of the present invention is to provide a manufacturing method of an aluminum alloy simulating the effect of neutron irradiation-induced silicon transmutation, simulating the tissue characteristics of 5-series aluminum alloys after neutron irradiation. The present invention also provides an aluminum alloy simulating the effect of neutron irradiation-induced silicon transmutation.

[0004] According to an embodiment of one aspect of the present invention, there is provided a manufacturing method of an aluminum alloy simulating the effect of neutron irradiation-induced silicon transmutation, the method comprising the following steps:

[0005] Step a): Provide a target aluminum alloy to be simulated, and provide the target thermal neutron fluence of the target aluminum alloy;

[0006] Step b): Determine the target Si element content in the target aluminum alloy according to the target thermal neutron fluence, and provide a raw material ingot according to the target aluminum alloy composition and the target Si element content;

[0007] Step c): Atomize and powder the raw material ingot to obtain a powder raw material, and the powder raw material is a supersaturated solid solution of Si;

[0008] Step d): Sinter and hot extrude the powder raw material to obtain an aluminum alloy bar, and perform homogenization heat treatment and aging treatment on the aluminum alloy bar to obtain an aluminum alloy simulating the effect of neutron irradiation-induced silicon transmutation.

[0009] Aluminum alloy parts can serve for decades in research reactors. The accumulated transmuted silicon will form nano-sized Mg2Si and elemental Si precipitation phases dispersed in the aluminum alloy matrix. The time cost of directly using neutron irradiation test to prepare samples is unacceptable. Excessive Si in conventional smelting process will form coarse hypoeutectic structure and micron-sized precipitation phase, which is very different from the organizational morphology and performance under real working conditions. This method uses the supersaturated solid solution powder prepared by the rapid solidification powder making method as raw material according to the aluminum alloy composition to be simulated, and then performs powder metallurgy. Rapid solidification technology can effectively reduce element diffusion, maintain the supersaturated state of the alloy, avoid the formation of micron-sized hypoeutectic, and provide favorable conditions for the formation of subsequent precipitation phases. The powder is made into a dense block sample by hot extrusion after sintering, and then a specific heat treatment process is used to promote the formation of nano-precipitation phases in the alloy that are close to those after neutron irradiation. The above technical route can effectively simulate the changes in composition and precipitation of aluminum alloy after neutron irradiation, solving the problem that the existing technology cannot fully realize the control of precipitation phase in high-silicon aluminum alloy. The preparation method of the simulated alloy also alleviates the current situation that the irradiation performance evaluation of metal materials with solid transmutation products is extremely dependent on neutron irradiation. It effectively improves the test efficiency and reduces the test cost.

[0010] Furthermore, in some embodiments, in the step b), the raw material ingot contains, by weight, 2.2%≤Mg≤3.9%, 0.15%≤Cr≤0.35%, 1%≤Si≤5.4%, Fe≤0.4%, Mn≤0.5%, Cu≤0.1%, Zn≤0.2%, Ti≤0.2%, and the balance is Al and unavoidable impurities.

[0011] Furthermore, in some embodiments, the method for manufacturing the raw material ingot is:

[0012] The target aluminum alloy is melted and Si element is added until the target Si element content is reached and then cast.

[0013] Furthermore, in some embodiments, the method for manufacturing the raw material ingot is:

[0014] The pure Al, Al-Si master alloy and Al-Cr master alloy are melted at 800°C-850°C to obtain an alloy melt;

[0015] The alloy melt is cooled to 650° C.-700° C., and pure Mg is added;

[0016] The alloy melt is heated to 740° C.-780° C., refined and cast.

[0017] Further, in some embodiments, in step d), the sintering conditions of the powder raw material are a heating temperature of 380°C - 420°C and a sintering pressure of 40 MPa - 60 MPa.

[0018] Further, in some embodiments, in step d), the homogenization heat treatment temperature is 480°C - 520°C and the heat treatment duration is 18 h - 24 h.

[0019] Further, in some embodiments, in step d), the aging treatment temperature is 150°C - 170°C and the heat treatment duration is 10 h - 30 h.

[0020] According to an embodiment of another aspect of the present invention, there is provided an aluminum alloy simulating the neutron irradiation transmutation silicon effect, and this aluminum alloy is manufactured by using the manufacturing method of the aluminum alloy simulating the neutron irradiation transmutation silicon effect provided in any of the foregoing embodiments.

[0021] This aluminum alloy simulates the precipitation phase state formed by transmutation silicon in 5-series aluminum alloys after long-term service in a neutron irradiation environment by introducing additional Si atoms, so as to obtain a precipitation phase structure similar to that of the aluminum alloy after neutron irradiation without undergoing real neutron irradiation treatment, thereby effectively reducing the test cost of studying the influence of the neutron irradiation transmutation effect on aluminum alloys and improving the research efficiency.

[0022] Further, in some embodiments, this aluminum alloy contains 2.2% - 3.9% of Mg, 0.15% - 0.35% of Cr, 1% - 5.4% of Si, not more than 0.4% of Fe, not more than 0.5% of Mn, not more than 0.1% of Cu, not more than 0.2% of Zn, not more than 0.2% of Ti by weight, and the balance is Al and unavoidable impurities, and the total weight of the unavoidable impurities does not exceed 0.05%.

[0023] Further, in some embodiments, after the aluminum alloy simulating the neutron irradiation transmutation silicon effect undergoes homogenization heat treatment, aging treatment and hot extrusion treatment, the tissue matrix is an Al solid solution, in which Mg2Si precipitation phases and Si precipitation phases with an average diameter of 3 nm - 20 nm are dispersedly distributed, and the room temperature tensile yield strength is 200 MPa - 400 MPa. Description of the Drawings

[0024] Figure 1 It is a scanning electron microscope photograph of the powder raw material in an embodiment;

[0025] Figure 2 It is a transmission electron microscope photograph of the Si precipitation phase in the aluminum alloy tissue in an embodiment;

[0026] Figure 3TEM micrograph of Si precipitates formed in an aluminum alloy after neutron irradiation in a comparative example;

[0027] Figure 4 Tensile test curves of the aluminum alloy sample and the comparative example sample in an embodiment;

[0028] Figure 5 EBSD test results of an aluminum alloy in an embodiment;

[0029] Figure 6 TEM micrograph of Si precipitates in the aluminum alloy microstructure in another embodiment;

[0030] Figure 7 TEM micrograph of Si precipitates formed in an aluminum alloy after neutron irradiation in another comparative example;

[0031] Figure 8 Tensile test curves of the aluminum alloy sample and the comparative example sample in another embodiment.

[0032] The purpose of the above-mentioned drawings is to make a detailed description of the present invention so that those skilled in the art can understand the technical concept of the present invention, rather than to limit the present invention. Detailed implementation manners

[0033] The present invention will be further described in detail below through specific embodiments in conjunction with the drawings.

[0034] The mention of "embodiment" in this article means that the specific features, structures or characteristics described in connection with the embodiment can be included in at least one embodiment of the present invention. The phrase appearing in various positions in the specification does not necessarily refer to the same embodiment, nor is it limited to mutually exclusive independent or alternative embodiments. Those skilled in the art should be able to understand that the embodiments in this article can be combined with other embodiments without structural conflicts.

[0035] In the description of this article, terms such as "first" and "second" are only used to distinguish different objects, and cannot be understood as indicating relative importance or limiting the quantity, specific order or primary-secondary relationship of the described technical features. In the description of this article, the meaning of "a plurality" is at least two.

[0036] 5xxx series aluminum alloys (Al-Mg alloys) are widely used in the manufacture of structural materials for various research reactors and have been widely used in various research reactors. Research reactors usually have a relatively high neutron fluence rate. Aluminum alloys will deteriorate in mechanical properties due to solid transmutation damage under long-term neutron irradiation conditions. Specifically, Al atoms are transmuted into Si atoms under the action of thermal neutrons:

[0037]

[0038] The transmuted Si will form precipitates with nano-scale dispersion distribution in the aluminum alloy matrix, leading to rapid hardening and embrittlement of the aluminum alloy. Studying the variation law of the mechanical properties of aluminum alloy after neutron irradiation transmutation is very important for the safe operation of research reactors. Since the service life of research reactors is usually up to several decades, it is unacceptable in terms of time and cost to conduct experiments on the transmutation damage of aluminum alloy using real neutron irradiation tests, and the operability is low. This state is not conducive to the optimization of the structural design of research reactors and the improvement of safety performance.

[0039] To solve the above problems, an embodiment of one aspect of the present invention provides an aluminum alloy that simulates the transmutation silicon effect of neutron irradiation, and simulates the influence of the neutron irradiation transmutation effect on the performance of the aluminum alloy by forming a precipitate structure similar to that of the aluminum alloy after the transmutation reaction occurs.

[0040] This aluminum alloy is manufactured by the following method:

[0041] First, determine the target aluminum alloy to be simulated and the neutron fluence corresponding to the target aluminum alloy state to be simulated.

[0042] Next, determine the target Si element content in the target aluminum alloy according to the target neutron fluence. The target Si element content includes the original Si element content in the target aluminum alloy and the transmuted Si content increased after neutron irradiation. The content of transmuted Si can be obtained through theoretical calculation or determined by detecting aluminum alloy parts that have experienced neutron irradiation under real working conditions. Prepare the raw material ingot according to the composition of the target aluminum alloy and the target Si element content. In different embodiments, the raw material ingot can be directly smelted according to the final component ratio, or the target aluminum alloy can be melted and then Si can be additionally added to the target amount to obtain it.

[0043] Next, atomize the raw material ingot into powder. Heat and melt the raw material ingot, and then use high-pressure gas flow to blow the molten metal droplets into fine droplets, and quickly solidify them into spherical powder as the powder raw material for preparing the aluminum alloy. Since the cooling rate of the droplets during the condensation process can reach 10 4 ℃ / s - 10 5 ℃ / s, Si exists in the spherical powder in the form of supersaturated solid solution.

[0044] Finally, an aluminum alloy bar is obtained by sintering and extruding powder raw materials. The aluminum alloy bar is subjected to homogenization heat treatment and aging treatment, so that supersaturated Si in it precipitates to form uniformly dispersed nanoscale Mg2Si and Si precipitate particles, obtaining a microstructure equivalent to that of the target aluminum alloy after long-term neutron irradiation, thereby being used for the simulation and evaluation of the mechanical property performance of aluminum alloy due to the neutron irradiation transmutation effect. The difference between this alloy and the microstructure of the aluminum alloy actually after long-term neutron irradiation is that its microstructure is a uniform and dense hot extrusion microstructure, and there are no irradiation damages such as displacement damage and transmutation gas generated by neutron irradiation in it.

[0045] In different embodiments, the target aluminum alloy can be 5052 alloy, 5154 alloy, 5754 alloy, etc., or other 5-series aluminum alloys suitable for the manufacture of research reactor structural components can also be used. The homogenization heat treatment temperature is 480°C - 520°C, the heat treatment duration is 18h - 24h, the aging treatment temperature is 150°C - 170°C, and the heat treatment duration is 10h - 30h. The above heat treatment process is applicable to the heat treatment process of aluminum alloys for simulating the simulated neutron irradiation transmutation silicon effect of various 5-series aluminum alloys. The specific heat treatment temperature and heat treatment duration can be adaptively adjusted according to the size of the Si precipitate phase in the final state of the alloy to be simulated.

[0046] In one embodiment, the components of the target aluminum alloy are: 2.2% - 3.9% of Mg, 0.15% - 0.35% of Cr, no more than 0.4% of Si, no more than 0.4% of Fe, no more than 0.5% of Mn, no more than 0.1% of Cu, no more than 0.2% of Zn, no more than 0.2% of Ti, and the balance is Al and unavoidable impurities. Further, the total amount of unavoidable impurity elements ≤ 0.05%. Generally, for a general research reactor, within the design life of the target aluminum alloy structural component, after experiencing the influence of long-term neutron irradiation, the weight ratio of the transmutation-generated Si atomic weight is in the range of 1% - 5%. The aluminum alloy for simulating the neutron irradiation transmutation silicon effect obtained after melting, powder metallurgy, hot extrusion and heat treatment, the average diameter range of the Si precipitate phase in it is 3nm - 20nm, and the room temperature tensile yield strength of the hot extrusion bar after aging treatment is 200MPa - 400MPa, which can better simulate the mechanical properties of the target aluminum alloy affected by neutron irradiation transmutation.

[0047] In the first preferred embodiment, the target aluminum alloy is 5052 alloy, and the simulation state is the microstructure of 5052 alloy after being subjected to a thermal neutron fluence of 15×10 26 n / m 2 . According to theoretical calculations, at this thermal neutron fluence, the weight ratio of the generated transmutation Si is about 3%.

[0048] After determining the composition of the aluminum alloy, melt the 5052 + 3% Si alloy raw material ingot: Melt pure Al, Al-Si master alloy, and Al-Cr master alloy at 800 °C, heat to 850 °C and hold for 15 min, and remove the surface scum; Cool the alloy melt to 680 ± 20 °C, quickly press the Mg block into the melt with a graphite rod and let it stand for at least 3 min until the Mg block is completely melted, controlling the temperature to reduce the vaporization loss during the melting of Mg; After the Mg is fully melted, heat the melt to 760 ± 20 °C, add a refining agent and refine for 5 min and remove the scum, sprinkle a covering agent and carry out vacuum degassing for 10 min, and then remove the scum again and cast at about 740 °C and air-cool to obtain the raw material ingot.

[0049] Next, prepare the powder raw material using the raw material ingot. Place the 5052 + 3% Si raw material ingot in a crucible in the melting chamber of the gas atomization equipment, replace the air in the melting chamber with nitrogen, heat to 800 °C using electromagnetic induction and hold for 30 min to completely melt the raw material ingot; Add the melt to the nozzle, and let the melt flow along the nozzle under the action of gravity, and the melt is broken into droplets by the impact of the rapidly flowing atomizing nitrogen. The droplets are rapidly cooled and solidified into powder during the falling process. Due to the high cooling rate, Si exists in the Al matrix in a supersaturated form and does not form precipitates. Collect the powder raw material as shown Figure 1 in the figure. Under these process parameters, the typical powder particle size of the powder raw material is 10 μm - 100 μm and has a high sphericity.

[0050] Next, perform sintering. In order to improve the sintering density, in the preferred embodiment, select powder raw materials of various different sizes with a particle size of 10 μm - 50 μm and sinter by the spark plasma process. After loading the powder into a graphite mold, heat to 400 ± 20 °C, and sinter into shape at a current of up to 2 kA under a pressure of 50 ± 10 MPa and air-cool to room temperature.

[0051] Subsequently, after holding the sintered alloy at 350 °C for 1 h, extrude it into a bar using a 1 cm diameter circular hole mold with an extrusion ratio of 9:1 and an extrusion rate of 1 mm / s. Hold at 500 ± 20 °C for 24 h for homogenization treatment to eliminate the microstructural inhomogeneity formed during casting and extrusion; Hold at 160 ± 10 °C for 24 h for aging treatment to precipitate Si atoms from the supersaturated solid solution to form nano-scale dispersed Si precipitate phase particles.

[0052] Drill samples from the aged bars, weigh no less than 5 g of debris, and use the quantum yield and transient fluorescence test system of Hamamatsu, Japan to determine the composition. Take the average of three measurements to obtain the alloy sample composition (weight ratio) as follows: 3.01% Si, 2.50% Mg, 0.25% Cr, 0.13% Fe, 0.0013% Cu, 0.0038% Mn, 0.0071% Zn, and the balance is Al.

[0053] Cut samples from the aged bars for transmission electron microscopy characterization. The obtained microstructure morphology is shown as Figure 2 shown (the Mg2Si phase is not shown within the photo range). It can be seen that the average size of the Si precipitation phase in the Al solid solution matrix is 8 nm. Figure 3 Shown is the actual microstructure of the aluminum alloy under the influence of neutron irradiation in a pair of comparative examples. The sizes and morphologies of the Si precipitation phases in the examples and comparative examples are consistent. The atomic displacement and diffusion channels brought by fast neutrons can increase the diffusion rate of Si and promote the growth of the precipitation phase. Therefore, in the later stage of neutron irradiation of the aluminum alloy, the density of the precipitation phase generated by the transmutation of Si will not increase infinitely. The newly transmutated Si often aggregates around the existing precipitation phases to make the existing precipitation phases grow. Therefore, during the simulation of the alloy preparation process, the microstructure morphology in the later stage of irradiation can be simulated by extending the aging holding time, and the growth of the Si-containing precipitation phase can be promoted thermodynamically to achieve the same result as fast neutron irradiation.

[0054] The tensile test results of the aged bar samples of the examples and the 5052 extruded alloy samples subjected to the same heat treatment are shown as Figure 4 shown. The yield strength of the bar samples of the examples is 280 MPa, and the total elongation is 8.5%. Among them, the yield strength is increased by about 130 MPa compared with the 5052 alloy, and the elongation is reduced by 57%. The dispersed Mg2Si and Si nanoparticle precipitation phases have a significant impact on the strength and plasticity of the samples. This result has a high consistency with the estimated precipitation strengthening amount reported in the literature "Neutron Irradiation Effects in 5xxx and 6xxx Series Aluminum Alloys: A Literature Review" after neutron irradiation.

[0055] In the second preferred embodiment, the 5052 aluminum alloy in the heavy water tank of the research reactor with a thermal neutron fluence of 11.4×10 26 n / m 2 is used as the simulation object to prepare an aluminum alloy for simulating the transmutation silicon effect of neutron irradiation.

[0056] According to theoretical calculations, to withstand 11.4×10 26 n / m2 When the thermal neutron fluence is [value not provided], about 2.28% by weight of transmuted Si is generated in the aluminum alloy. 2.28% of Si is additionally added to the molten 5052 alloy, and the raw ingot is obtained by casting; the powder raw material is prepared by atomization using the same method as in the previous embodiment, sintered and formed at 400 °C and 50 MPa and air-cooled to room temperature; then it is held at 350 °C for 1 h, and an aluminum alloy bar is extruded and formed using a circular hole die with a diameter of 1 cm at an extrusion ratio of 9:1 and an extrusion rate of 1 mm / s; the extruded aluminum alloy bar is subjected to homogenization heat treatment at 500 °C for 24 h, and finally held at 160 °C for 10 h to obtain a 5052 + 2.28% Si aluminum alloy structure with uniformly dispersed Si nanoparticle precipitation phases.

[0057] Drill and sample from the aged bar, weigh no less than 5 g of debris, and use the quantum yield and transient fluorescence test system of Hamamatsu, Japan to determine the composition. Take the average value of three measurements to obtain the alloy sample composition (by weight) as follows: 2.28% Si, 2.60% Mg, 0.25% Cr, 0.12% Fe, 0.0008% Cu, 0.0031% Mg, 0.0070% Zn, and the balance is Al.

[0058] The backscattered electron diffraction image (EBSD) of the cross-section of the extruded bar of the prepared 5052 + 2.28% Si alloy sample is as Figure 5 shown. The internal structure of the alloy bar is dense and uniform, and the average grain size is about 3 μm. Samples are cut from the bar for transmission electron microscopy characterization, and the microstructure morphology obtained by photographing is as Figure 6 shown. The average diameter of the Si precipitation phase is 3 nm, which is consistent with the size of the precipitation phase in the 5052 aluminum alloy irradiated at a thermal neutron fluence of 11.9×10 Figure 7 reported in the literature "Effect of neutron fluence on microstructure and mechanical properties of Al 5052 irradiated in the National Research Universal (NRU) reactor" as shown in 26 n / m 2 under the thermal neutron fluence.

[0059] The tensile test results of the aged bar sample of the example and the 5052 extruded alloy sample subjected to the same heat treatment are as Figure 8As shown, the yield strength of the bar sample in the embodiment is 260 MPa. Its yield strength is increased by approximately 110 MPa compared to the 5052 alloy, and the elongation is decreased by 53%. The precipitation of dispersed Si-containing nanoparticles has a significant impact on the strength and plasticity of the sample.

[0060] The aluminum alloy provided in the above embodiment for simulating the silicon effect of neutron irradiation-induced transmutation does not rely on neutron irradiation resources and can simulate the microstructure of aluminum alloy affected by neutron irradiation using conventional processes, effectively saving the test cost and test cycle and facilitating the conduct of batch and large-scale tests. This aluminum alloy can conduct a large number of extended studies on the transmutation effect of aluminum alloy at low cost.

[0061] The manufacturing method of the aluminum alloy provided in the above embodiment for simulating the neutron irradiation-induced transmutation effect combines rapid solidification and precise heat treatment, avoiding the appearance of coarse hypoeutectic structures commonly found in conventional aluminum-magnesium-silicon alloys, and can effectively form a microstructure with dispersed nano-Si particles. By regulating the heat treatment regime, it is possible to conveniently and accurately prepare aluminum alloy neutron irradiation-induced transmutation microstructures equivalent to those under different neutron fluences. The technical solution is simple, low-cost, and highly operable.

[0062] The purpose of the above embodiment is to further elaborate on the present invention with reference to the accompanying drawings so that those skilled in the art can understand the technical concept of the present invention. Within the scope disclosed by the present invention, optimizing or equivalently replacing the components or method steps involved, and combining the implementation manners in different embodiments without conflict in structure and principle all fall within the protection scope of the present invention.

Claims

1. A method for manufacturing an aluminum alloy that simulates the neutron irradiation transmutation silicon effect, characterized in that: The following steps are involved: Step a): providing a target aluminum alloy to be simulated, and providing a target thermal neutron flux of the target aluminum alloy; Step b): determining a target Si element content in the target aluminum alloy according to the target thermal neutron injection, and providing a raw material ingot according to the target aluminum alloy composition and the target Si element content; Step c): atomizing and powdering the raw material ingot to obtain a powder raw material, wherein the powder raw material is a supersaturated solid solution of Si; Step d): sintering and hot extruding the powder raw material to obtain an aluminum alloy rod, performing homogenization heat treatment and aging treatment on the aluminum alloy rod to obtain an aluminum alloy simulating the neutron irradiation transmutation silicon effect.

2. The method for manufacturing an aluminum alloy simulating neutron irradiation transmutation silicon effect according to claim 1, characterized in that: In the step b), the raw material ingot contains, by weight, 2.2%≤Mg≤3.9%, 0.15%≤Cr≤0.35%, 1%≤Si≤5.4%, Fe≤0.4%, Mn≤0.5%, Cu≤0.1%, Zn≤0.2%, Ti≤0.2%, and the balance is Al and unavoidable impurities.

3. The method for manufacturing an aluminum alloy simulating neutron irradiation transmutation silicon effect according to claim 1, characterized in that: The manufacturing method of the raw material ingot is: The target aluminum alloy is melted and Si element is added until the target Si element content is reached and then cast.

4. The method for manufacturing an aluminum alloy simulating neutron irradiation transmutation silicon effect according to claim 2, characterized in that: The manufacturing method of the raw material ingot is: The pure Al, Al-Si master alloy and Al-Cr master alloy are melted at 800°C-850°C to obtain an alloy melt; The alloy melt is cooled to 650° C.-700° C., and pure Mg is added; The alloy melt is heated to 740° C.-780° C., refined and cast.

5. The method for manufacturing an aluminum alloy simulating neutron irradiation transmutation silicon effect according to claim 3 or 4, characterized in that: In the step d), the sintering conditions of the powder raw material are: a heating temperature of 380° C.-420° C. and a sintering pressure of 40 MPa-60 MPa.

6. The method for manufacturing an aluminum alloy simulating neutron irradiation transmutation silicon effect according to claim 2, characterized in that: In the step d), the homogenization heat treatment temperature is 480° C.-520° C., and the heat treatment time is 18 h-24 h.

7. The method for manufacturing an aluminum alloy simulating neutron irradiation silicon transmutation effect according to claim 6, characterized in that: In the step d), the aging treatment temperature is 150° C.-170° C., and the heat treatment time is 10 h-30 h.

8. An aluminum alloy simulating the neutron irradiation transmutation effect of silicon, characterized in that: The aluminum alloy is manufactured by the method for manufacturing an aluminum alloy simulating the neutron irradiation transmutation silicon effect as described in any one of claims 1 to 7.

9. The aluminum alloy simulating neutron irradiation silicon transmutation effect according to claim 8, characterized in that: It contains 2.2%-3.9% Mg, 0.15%-0.35% Cr, 1%-5.4% Si, no more than 0.4% Fe, no more than 0.5% Mn, no more than 0.1% Cu, no more than 0.2% Zn, no more than 0.2% Ti, and the balance is Al and unavoidable impurities, and the total weight of the unavoidable impurities does not exceed 0.05%.

10. The aluminum alloy simulating neutron irradiation silicon transmutation effect according to claim 9, characterized in that: After homogenization heat treatment, aging treatment and hot extrusion treatment, the aluminum alloy simulating the neutron irradiation transmutation silicon effect has an Al solid solution matrix in which Mg2Si precipitation phases and Si precipitation phases with an average diameter of 3nm-20nm are dispersed, and the room temperature tensile yield strength is 200MPa-400MPa.

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