Aluminum alloy for simulating neutron irradiation transmutation silicon effect and manufacturing method thereof

Abstract

The invention discloses an aluminum alloy for simulating a neutron irradiation transmutation silicon effect and a manufacturing method thereof, and belongs to the field of aluminum alloys. The manufacturing method of the aluminum alloy for simulating the neutron irradiation transmutation silicon effect comprises the following steps: determining the Si element content in the alloy according to the state of the aluminum alloy to be simulated, and preparing a supersaturated solid solution raw material with corresponding components, an aluminum alloy bar is prepared through a powder metallurgy process, and an aluminum alloy structure for simulating the generation of the transmutation silicon effect is obtained through heat treatment. According to the aluminum alloy preparation method, the simulated alloy can be prepared to effectively simulate a precipitated phase structure formed by transmutation reaction after the aluminum alloy is irradiated by neutrons for a long time, and the aluminum alloy preparation method plays an important role in researching the influence of irradiation transmutation products on the performance of the aluminum alloy; the current situation that irradiation performance evaluation of a metal material with a solid transmutation product is extremely dependent on neutron irradiation resources is relieved, the research efficiency is improved, and therefore the design level and the safety performance of an aluminum alloy structural part in a research reactor are improved.

Description

Technical Field

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

[0002] 5 series aluminum alloys have good neutron economy, low nuclear heat generation rate, fast heat dissipation, and good corrosion resistance and processing performance. Therefore, they are widely used in the manufacture of research reactor structures. After long-term service under neutron irradiation conditions, aluminum alloys will become brittle due to neutron irradiation, affecting 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. Al atoms capture neutrons and are converted into Si atoms. Si and Mg, the main solid solution element of 5 series aluminum alloys, will form dispersed precipitation phases (Mg 2 Si, Si single substance, etc.) lead to rapid hardening and embrittlement of aluminum alloys. Therefore, studying the performance changes of aluminum alloys under neutron irradiation conditions is very important for the safe design of research reactors. Research reactors have a high injection rate and a long life, and the total injection received by the material at the end of its life is high. It takes a very long time to use neutron irradiation tests to evaluate the performance of materials to reach the neutron injection at the end of the research reactor life, and the operability is low. Therefore, providing an aluminum alloy preparation method to simulate the transmutation Si effect of aluminum alloys after irradiation is of 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 method for manufacturing an aluminum alloy that simulates the neutron irradiation transmutation effect of silicon, and to simulate the structural characteristics of the 5-series aluminum alloy after neutron irradiation. The present invention also provides an aluminum alloy that simulates the neutron irradiation transmutation effect of silicon.

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

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

[0006] 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;

[0007] 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;

[0008] 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.

[0009] Aluminum alloy parts can be used in research reactors for decades, and the accumulated transmuted silicon will form nanoscale Mg 2 Si and elemental Si precipitation phase are 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. According to the composition of the aluminum alloy to be simulated, the method uses the supersaturated solid solution powder prepared by the method of rapid solidification and powder making as raw material, 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 the composition and precipitation phase of aluminum alloy after neutron irradiation, and solves the problem that the existing technology cannot fully realize the control of precipitation phases in high silicon content aluminum alloys. The preparation method of the simulated alloy also alleviates the current situation that the radiation performance evaluation of metal materials with solid transmutation products is extremely dependent on neutron irradiation, effectively improving the test efficiency and reducing 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] Furthermore, in some embodiments, 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.

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

[0019] Furthermore, in some embodiments, in the step d), the aging treatment temperature is 150° C.-170° C., and the heat treatment time 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 effect of silicon, and the aluminum alloy is manufactured using the method for manufacturing the aluminum alloy simulating the neutron irradiation transmutation effect of silicon provided in any of the aforementioned embodiments.

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

[0022] Furthermore, in some embodiments, the aluminum alloy contains, by weight, 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, the total weight of the unavoidable impurities not exceeding 0.05%.

[0023] Further, in some embodiments, 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 Mg with an average diameter of 3nm-20nm is dispersed. 2 Si precipitation phase and Si precipitation phase, room temperature tensile yield strength is 200MPa-400MPa. BRIEF DESCRIPTION OF THE DRAWINGS

[0024] Figure 1 This is a scanning electron microscope photo of the powder raw material in one embodiment; Figure 2 A transmission electron microscope photograph of Si precipitation phase in the aluminum alloy structure in one embodiment; Figure 3 A transmission electron microscope photo of Si precipitate formed in a pair of aluminum alloys after neutron irradiation; Figure 4 1. The tensile test curves of the aluminum alloy sample in an embodiment and the comparative example sample; Figure 5 EBSD test results of aluminum alloy in one embodiment; Figure 6 is a transmission electron microscope photograph of Si precipitation phase in the aluminum alloy structure in another embodiment; Figure 7 This is a transmission electron microscope photo of Si precipitate phase formed after neutron irradiation of aluminum alloy in another comparative example; Figure 8 1 is a tensile test curve of an aluminum alloy sample in another embodiment and a comparative example sample.

[0025] The purpose of the above drawings is to explain the present invention in detail so that those skilled in the art can understand the technical concept of the present invention, but it is not intended to limit the present invention. DETAILED DESCRIPTION

[0026] The present invention is further described in detail below through specific embodiments in conjunction with the accompanying drawings.

[0027] Reference to "embodiments" herein means that a particular feature, structure, or characteristic described in conjunction with the embodiments may be included in at least one embodiment of the present invention. The phrase appearing in various locations 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 herein may be combined with other embodiments without causing structural conflicts.

[0028] In the description of this article, the terms "first", "second" and the like are only used to distinguish different objects, and cannot be understood as indicating relative importance or limiting the quantity, specific order or primary and secondary relationship of the described technical features. In the description of this article, the meaning of "plurality" is at least two.

[0029] 5 series aluminum alloys (Al-Mg alloys) are widely used in the manufacture of various research reactor structural materials and have been widely used in various research reactors. Research reactors usually have a high neutron injection rate. Under long-term neutron irradiation conditions, aluminum alloys will deteriorate in mechanical properties due to solid transmutation damage. Specifically, Al atoms are transmuted into Si atoms under the action of thermal neutrons:

[0030]

[0031] Transmuted Si will form a nano-scale dispersed precipitate phase in the aluminum alloy matrix, resulting in rapid hardening and embrittlement of the aluminum alloy. Studying the changing law of the mechanical properties of aluminum alloy after neutron irradiation transmutation is very important for the safe operation of research reactors. Since the life of a research reactor is usually as long as several decades, it is unacceptable in terms of time and cost to use real neutron irradiation tests to test the transmutation damage of aluminum alloys, and the operability is low. This state is not conducive to the optimization of the research reactor structure design and the improvement of safety performance.

[0032] In order to solve the above problems, an embodiment of one aspect of the present invention provides an aluminum alloy that simulates the neutron irradiation transmutation effect of silicon, by forming a precipitation phase structure similar to that of the aluminum alloy after the transmutation reaction to simulate the influence of the neutron irradiation transmutation effect on the performance of the aluminum alloy.

[0033] The aluminum alloy is manufactured by the following method:

[0034] First, the target aluminum alloy to be simulated and the neutron injection corresponding to the state of the target aluminum alloy to be simulated are determined.

[0035] Next, the target Si element content in the target aluminum alloy is determined according to the target neutron injection, and 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 by theoretical calculation, or it can be determined by testing aluminum alloy parts that have undergone neutron irradiation under actual working conditions. According to the composition of the target aluminum alloy and the target Si element content, a raw ingot is prepared. In different embodiments, the raw ingot can be directly smelted according to the final component ratio, or it can be obtained by melting the target aluminum alloy and then adding additional Si to the target amount.

[0036] Next, the raw material ingot is atomized and powdered. After the raw material ingot is heated and melted, the molten metal droplets are blown into fine droplets using high-pressure airflow, and then quickly solidified into spherical powder as the powder raw material for preparing aluminum alloy. 4 ℃ / s-10 5 ℃ / s, Si exists in the form of supersaturated solid solution in the spherical powder.

[0037] Finally, the powder raw material is sintered and extruded to obtain an aluminum alloy rod, which is then subjected to homogenization heat treatment and aging treatment to precipitate the supersaturated Si to form uniformly dispersed nanoscale Mg 2Si and Si precipitate phase particles are used to obtain a microstructure equivalent to that of the target aluminum alloy after long-term neutron irradiation, which is used to simulate and evaluate the neutron irradiation transmutation effect on the mechanical properties of the aluminum alloy. The difference between this alloy and the actual aluminum alloy structure after long-term neutron irradiation is that its organizational morphology is a uniform and dense hot extrusion state organization, in which there is no irradiation damage such as de-situ damage and transmutation gas caused by neutron irradiation.

[0038] In different embodiments, the target aluminum alloy may be 5052 alloy, 5154 alloy or 5754 alloy, etc., or other 5-series aluminum alloys suitable for manufacturing research reactor structures may be used. The homogenization heat treatment temperature is 480°C-520°C, the heat treatment time is 18h-24h, the aging treatment temperature is 150°C-170°C, and the heat treatment time is 10h-30h. The above heat treatment process is suitable for simulating the heat treatment process of aluminum alloys simulating the neutron irradiation transmutation silicon effect of various 5-series aluminum alloys. The specific heat treatment temperature and heat treatment time can be adaptively adjusted according to the size of the Si precipitate phase in the final state of the simulated alloy.

[0039] In one embodiment, the composition of the target aluminum alloy is: 2.2%-3.9% Mg, 0.15%-0.35% Cr, no more than 0.4% 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. Further, the total amount of unavoidable impurity elements is ≤0.05%. Generally, for general research reactors, the target aluminum alloy structural parts are subjected to the influence of long-term neutron irradiation within the design life, and the weight ratio of Si atoms produced by transmutation is in the range of 1%-5%. The aluminum alloy used to simulate the neutron irradiation transmutation silicon effect is obtained after smelting, powder metallurgy, hot extrusion and heat treatment. The average diameter of the Si precipitate phase ranges from 3nm to 20nm, and the room temperature tensile yield strength of the hot-extruded rod after aging treatment is 200MPa-400MPa, which can better simulate the mechanical properties of the target aluminum alloy affected by neutron irradiation transmutation.

[0040] In the first preferred embodiment, the target aluminum alloy is 5052 alloy, and the simulation state is that 5052 alloy is subjected to 15×10 26 n / m 2 According to theoretical calculations, at this thermal neutron dose, the weight ratio of the generated transmuted Si is about 3%.

[0041] After determining the composition of the aluminum alloy, 5052+3%Si alloy raw material ingots were smelted: pure Al, Al-Si master alloy and Al-Cr master alloy were melted at 800°C, heated to 850°C and kept warm for 15 minutes, and the surface scum was removed; the alloy melt was cooled to 680±20°C, and a Mg block was quickly pressed into the melt with a graphite rod and allowed to stand for at least 3 minutes to completely melt the Mg block, and the temperature was controlled to reduce the gasification loss of Mg during the melting process; after Mg was fully melted, the melt was heated to 760±20°C, a refining agent was added to refine for 5 minutes and the scum was removed, a covering agent was sprinkled and vacuum degassing was performed for 10 minutes, and after removing the scum again, it was cast at about 740°C and air-cooled to obtain a raw material ingot.

[0042] Next, the raw material ingot is used to prepare the powder raw material. The 5052+3%Si raw material ingot is placed in the crucible in the melting chamber of the gas atomization equipment, and the air in the melting chamber is replaced by nitrogen. The raw material ingot is heated to 800°C by electromagnetic induction and kept warm for 30 minutes to completely melt the raw material ingot. The melt is added to the nozzle, and the melt flows along the nozzle under the action of gravity. The melt is broken into droplets under the impact of the fast-flowing atomized nitrogen. The droplets are rapidly cooled and solidified into powder during the falling process. Due to the high cooling rate, the Si in the powder exists in the Al matrix in a supersaturated form and does not form precipitation. Collect the resulting mixture at the bottom of the cavity. Figure 1 The powder raw material shown has a typical powder particle size of 10μm-100μm under this process parameter and has a very high sphericity.

[0043] Next, sintering is performed. In order to improve the density of sintering, in the preferred embodiment, a variety of powder raw materials with a particle size of 10μm-50μm are selected and sintered by a spark plasma process. The powder is loaded into a graphite mold and heated to 400±20℃, sintered at a current of up to 2kA under a pressure of 50±10MPa, and air-cooled to room temperature.

[0044] Subsequently, the sintered alloy was kept at 350°C for 1 hour, and then extruded into rods using a 1 cm diameter circular hole die at an extrusion ratio of 9:1 and an extrusion rate of 1 mm / s. The alloy was kept at 500±20°C for 24 hours for homogenization to eliminate the structural inhomogeneity formed during casting and extrusion; and was kept at 160±10°C for 24 hours for aging treatment to precipitate Si atoms from the supersaturated solid solution to form nano-scale dispersed Si precipitation phase particles.

[0045] Samples were taken by drilling holes in the aged bars, and no less than 5 g of debris was weighed for composition determination using the quantum yield and transient fluorescence test system of Hamamatsu, Japan. The average of three measurements was taken, and the composition (weight ratio) of the alloy sample was: 3.01% Si, 2.50% Mg, 0.25% Cr, 0.13% Fe, 0.0013% Cu, 0.0038% Mn, 0.0071% Zn, and the balance was Al.

[0046] The samples were cut from the aged rods and characterized by transmission electron microscopy. The microstructures were as follows: Figure 2 As shown (Mg is not shown in the photo) 2 Si phase), it can be seen that the average size of the Si-containing precipitate phase in the Al solid solution matrix is ​​8nm. Figure 3 The actual microstructure of aluminum alloy under neutron irradiation in a comparative example is shown. The size and morphology of Si-containing precipitates in the embodiment and the comparative example are consistent. The atomic displacement and diffusion channel brought by fast neutrons can increase the diffusion rate of Si and promote the growth of precipitates. Therefore, when the aluminum alloy enters the late stage of neutron irradiation, the density of precipitates produced by transmuted Si will not increase infinitely. The newly transmuted Si tends to gather around the existing precipitates to make the existing precipitates grow. Therefore, in the process of simulating alloy preparation, the microstructure morphology of the late irradiation period can be simulated by extending the aging and heat preservation time, and the growth of Si-containing precipitates can be promoted by thermodynamics to achieve the equivalent result of fast neutron irradiation.

[0047] The tensile test results of the aging treated bar sample and the 5052 extruded alloy sample subjected to the same heat treatment are shown in Figure 2. Figure 4 As shown in the figure, the yield strength of the rod sample in the embodiment is 280MPa, and the total elongation is 8.5%, wherein the yield strength is increased by about 130MPa compared with the 5052 alloy, and the elongation is reduced by 57%. 2 The precipitation of Si and Si nanoparticles has a significant effect on the strength and plasticity of the samples. This result is highly consistent with the estimated precipitation phase strengthening after neutron irradiation reported in the literature Neutron Irradiation Effects in 5xxx and 6xxx Series Aluminum Alloys: A Literature Review.

[0048] In the second preferred embodiment, the thermal neutron flux is 11.4×10 26 n / m 2 The 5052 aluminum alloy of the research reactor heavy water tank was taken as the simulation object, and the aluminum alloy used to simulate the neutron irradiation transmutation silicon effect was prepared.

[0049] According to theoretical calculation, it can withstand 11.4×1026 n / m 2 When the thermal neutron injection rate is 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 material ingot is cast; the powder raw material is atomized by the same method as in the previous embodiment, sintered at 400°C and 50MPa, and air-cooled to room temperature; then the material is kept at 350°C for 1 hour, and an aluminum alloy rod is obtained by extrusion molding using a 1cm diameter circular hole mold with an extrusion ratio of 9:1 and an extrusion rate of 1mm / s; the extruded aluminum alloy rod is subjected to a homogenization heat treatment at 500°C for 24 hours, and finally kept at 160°C for 10 hours to obtain a 5052+2.28%Si aluminum alloy structure with a uniformly dispersed Si nanoparticle precipitation phase.

[0050] Samples were taken by drilling holes in the aged bars, and no less than 5 g of debris was weighed for composition determination using the quantum yield and transient fluorescence test system of Hamamatsu, Japan. The average of three measurements was taken, and the composition (weight ratio) of the alloy sample was: 2.28% Si, 2.60% Mg, 0.25% Cr, 0.12% Fe, 0.0008% Cu, 0.0031% Mg, 0.0070% Zn, and the balance was Al.

[0051] The backscattered electron diffraction (EBSD) image of the cross section of the extruded rod of the prepared 5052+2.28%Si alloy sample is as follows: Figure 5 As shown in Figure 1, the internal structure of the alloy rod is dense and uniform, with an average grain size of about 3 μm. Samples were cut from the rod for transmission electron microscopy characterization, and the organizational morphology obtained was shown in Figure 1. Figure 6 As shown in Figure 2, the average diameter of Si precipitates is 3 nm, which is similar to Figure 7 The literature Effect of neutron fluence on microstructure and mechanical properties of Al 5052 irradiated in the National Research Universal (NRU) reactor reported that the NRU reactor had a 11.9×10 26 n / m 2 The sizes of the precipitated phases in 5052 aluminum alloy under thermal neutron injection are consistent.

[0052] The tensile test results of the aging treated bar sample and the 5052 extruded alloy sample subjected to the same heat treatment are shown in Figure 2. Figure 8As shown, the yield strength of the rod sample of the embodiment is 260 MPa, which is about 110 MPa higher than that of the 5052 alloy, and the elongation is reduced by 53%. The precipitation of dispersed Si-containing nanoparticles has a significant effect on the strength and plasticity of the sample.

[0053] The aluminum alloy for simulating the neutron irradiation transmutation effect of silicon provided in the above embodiment does not need to rely on neutron irradiation resources, and can simulate the microstructure of the aluminum alloy affected by neutron irradiation by using conventional processes, which effectively saves the test cost and test cycle, and is convenient for batch and large-scale tests. The aluminum alloy can carry out a large number of extended studies on the transmutation effect of aluminum alloys at a low cost.

[0054] The manufacturing method of the aluminum alloy for simulating the neutron irradiation transmutation effect provided in the above embodiment avoids the appearance of the coarse hypoeutectic structure commonly seen in conventional aluminum-magnesium-silicon alloys by combining rapid solidification with precise heat treatment, and can effectively form a structure morphology with dispersed nano-Si particles. By regulating the heat treatment system, the neutron irradiation transmutation structure of the aluminum alloy equivalent to that under different neutron injections can be conveniently and accurately prepared, and the technical solution is simple, low-cost, and highly operable.

[0055] The purpose of the above embodiments is to further explain the present invention in detail in conjunction with the accompanying drawings so that those skilled in the art can understand the technical concept of the present invention. Within the scope of the present invention, the optimization or equivalent replacement of the components or method steps involved, and the combination of implementation methods in different embodiments without conflict of 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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