Prediction method for mechanical properties of graphene-coated SiC particles reinforced aluminum matrix composites

Abstract

The present invention discloses a method for predicting the mechanical properties of graphene-coated SiC particle-reinforced aluminum-based composite materials, specifically comprising the following steps: Step 1: preparing a sample of the graphene-coated SiC particle-reinforced aluminum-based composite material using a solvothermal method, and measuring its microscopic characteristics and macroscopic elastic-plastic mechanical properties; Step 2: establishing periodic representative volume units based on the microscopic characteristics obtained in Step 1; Step 3: establishing a constitutive model for the plasticity and damage coupling of each component phase and the composite material based on the mechanical characteristics of the metal aluminum matrix, graphene, SiC particles, and interface phases, and predicting the mechanical properties of the graphene-coated SiC particle-reinforced aluminum-based composite material. The present invention can quickly determine the elastic-plastic mechanical properties of the graphene-coated SiC particle-reinforced aluminum-based composite material under different graphene contents and interface effects.

Description

Technical Field

[0001] The present invention belongs to the technical field of optimizing the mechanical properties of nano-carbon and ceramic particle synergistically reinforced metal-based composite materials, and particularly relates to a method for predicting the mechanical properties of graphene-wrapped SiC particle reinforced aluminum-based composite materials. Background Art

[0002] To meet the urgent needs of large-scale national projects such as deep space probes and large passenger aircraft, research on the optimization design theory and methods of the mechanical properties of lightweight materials, represented by high-performance aluminum-based composites, has become an increasingly hot topic in academia. SiC nanoceramic particles are widely used to reinforce aluminum-based composites, helping to improve the elastic modulus and tensile strength of the composites. However, during the preparation process, nanoceramic particles tend to agglomerate due to the interaction of van der Waals forces, especially when the nanoceramic particles are present at high concentrations, resulting in a decrease in the elongation of the composite material. This contradiction has limited the in-depth development of aluminum-based composites in cutting-edge high-tech fields, making it difficult to meet the further application needs of lightweight, high-strength and tough aluminum-based composites in social and technological development.

[0003] Compared with traditional ceramic particle reinforcements, graphene is considered to be an ideal reinforcement phase for the new generation of lightweight aluminum-based composites due to its excellent intrinsic mechanical properties. The new lightweight aluminum-based composites constructed by introducing high-level ordered assembled nano-core-shell composite particles formed by coating or wrapping graphene on the surface of nano-ceramic particles into the metal aluminum matrix have good strength and plasticity matching and broad application prospects. The interfacial reaction products of appropriate thickness between graphene / metal aluminum can effectively enhance the pinning ability of SiC nanoparticles in the matrix and are a key factor in enhancing the plastic properties of composites. However, the quantitative influence of the interface effect and its influencing factors on the macroscopic elastic-plastic mechanical properties of graphene-wrapped SiC particle reinforced aluminum-based composites is still unclear. Therefore, how to provide a method for predicting the mechanical properties of graphene-wrapped SiC particle reinforced aluminum-based composites is of great research significance. Summary of the Invention

[0004] The purpose of the present invention is to provide a method for predicting the mechanical properties of graphene-wrapped SiC particle reinforced aluminum matrix composites, which can quickly determine the elastic-plastic mechanical properties of graphene-wrapped SiC particle reinforced aluminum matrix composites under different graphene contents and interface effects.

[0005] The technical solution adopted by the present invention is a method for predicting the mechanical properties of graphene-coated SiC particles reinforced aluminum-based composite materials, which specifically includes the following steps:

[0006] Step 1: Prepare a graphene-wrapped SiC particle reinforced aluminum matrix composite sample by a solvothermal method, and measure its microscopic characteristics and macroscopic elastic-plastic mechanical properties;

[0007] Step 2, establishing a representative volume unit of the graphene-wrapped SiC particle reinforced aluminum matrix composite material based on the microscopic features obtained in step 1;

[0008] Step 3: Based on the mechanical characteristics of the metal aluminum matrix, graphene, SiC particles and the interface phase, a constitutive model of the plasticity and damage coupling of each component phase and the composite material is established to predict the mechanical properties of the graphene-wrapped SiC particle reinforced aluminum matrix composite material.

[0009] The present invention is also characterized in that

[0010] In step 1, a solvothermal method is used to prepare a graphene-wrapped SiC particle-reinforced aluminum-based composite material sample, specifically selecting aluminum salt, carbon-containing compound, SiC particles, organic solvent and surfactant, ultrasonically dispersing the SiC particles in the organic solvent, adding the surfactant and mixing with the precursor solution containing aluminum salt and carbon-containing compound to obtain a mixed solution; transferring the mixed solution to a stainless steel high-pressure reactor with a polytetrafluoroethylene liner, and reacting at a temperature of 150°C to 300°C for 10h to 24h; cooling, washing and drying to obtain a composite powder, mixing the composite powder with aluminum powder, and hot-pressing and sintering at 500°C to 600°C and 100MPa to 50MPa to obtain a graphene-wrapped SiC particle-reinforced aluminum-based composite material.

[0011] The microscopic characteristics of the aluminum matrix composite material are characterized by scanning electron microscopy and transmission electron microscopy. The microscopic characteristics include the spatial distribution of SiC particles, the size characteristics of SiC particles in the graphene-wrapped layer, and the microscopic characteristics of the interface layer.

[0012] The macroscopic elastic-plastic mechanical properties of graphene-wrapped SiC particles reinforced aluminum matrix composites were measured using an electronic universal testing machine.

[0013] Step 2: Establishing a representative volume unit. Specifically, first construct graphene-wrapped SiC core-shell particles and distribute them periodically in cubic cells to form a geometric model of the representative volume unit.

[0014] The expression for the periodic displacement field applied on a pair of boundary surfaces of a representative volume element is given by:

[0015] ;

[0016] in, is the average strain of the representative volume element; is the coordinate of any node of the representative volume element; and Indicates the positive and negative direction of the global coordinate axis.

[0017] In step 3, the mechanical characteristics of the metal aluminum matrix are obtained by performing a tensile test on the metal aluminum matrix, and the mechanical characteristics of the interface phase are obtained by inversely deducing the tensile test of the graphene-wrapped SiC particle reinforced aluminum matrix composite material.

[0018] In step 3, the constitutive model of the plasticity and damage coupling of each component phase and the composite material is established:

[0019] The plastic constitutive model is shown as follows:

[0020] ;

[0021] in, σ represents the flow stress, ε pl represents the effective plastic strain, and A 、 B 、 C 、 M and N represent the yield strength, hardening modulus, strain rate coefficient, temperature coefficient and hardening coefficient of the matrix respectively; C and M Both parameters are set to zero;

[0022] The damage constitutive model can be expressed as:

[0023] ;

[0024] Where, is the failure strain, d 1 ~d 5 is the material damage related constant, p and q are the hydrostatic pressure and von- Mises Stress, where d 4 and d The value of 5 is zero.

[0025] In the linear elastic stage of the constitutive model, the stiffness of the interface internal force unit is K 0, the relationship between stress and displacement is shown as follows:

[0026] ;

[0027] Where, t n is the normal stress, t s is the tangential stress, δ n is the positive displacement, δ s is the tangential displacement;

[0028] When the sum of the squares of the nominal stress ratios in all directions is equal to 1, damage begins to occur. The initial damage of the cohesive element adopts the quadratic nominal stress criterion in the traction-separation failure criterion, as shown in the following formula:

[0029] ;

[0030] Where, refers to the positive strength, and is the tangential strength; Ф 〉=( Ф +| Ф |) / 2, which means that the cohesive element does not suffer damage under compressive stress;

[0031] When a cohesive unit fails, its displacement is determined by the fracture energy G, as shown in the following formula:

[0032] ;

[0033] Where, and are the normal fracture energy and normal critical fracture energy, and are the tangential fracture energy and the tangential critical fracture energy, respectively.

[0034] When making predictions in step 3, based on the macroscopic mechanical properties of the composite material obtained in step 1, the stress-strain data when the volume fraction of graphene-wrapped SiC particles is zero is selected, and the plasticity and damage-related parameters in the constitutive model are obtained through data fitting; the microscopic parameters of graphene and SiC particles in the composite material are substituted into the constructed constitutive model for solution.

[0035] The constitutive prediction model is solved using the ABAQUS explicit solver.

[0036] The beneficial effects of the present invention are:

[0037] The method for predicting the mechanical properties of graphene-wrapped SiC particle-reinforced aluminum-based composite materials of the present invention establishes a representative volume unit of the graphene-wrapped SiC particle-reinforced aluminum-based composite material based on the microscopic characteristics of component phases such as the aluminum matrix, the graphene-wrapped layer, the SiC particles, and the interface layer, combined with periodic boundary conditions, and then constructs a Johnson-Cook constitutive model that takes interface damage into account. The model can quantitatively describe the intrinsic relationship between the interface effect of the composite material and the macroscopic elastic-plastic mechanical properties, providing technical support for optimizing the elastic-plastic properties of the graphene-wrapped SiC particle-reinforced aluminum-based composite material, and significantly reducing experimental cycle and cost. BRIEF DESCRIPTION OF THE DRAWINGS

[0038] Figure 1is a transmission electron microscope morphology image of the graphene-wrapped SiC particle reinforced aluminum-based composite material in step 1 of the present invention;

[0039] Figure 2 is the representative volume unit established in step 2 of the present invention;

[0040] Figure 3 A comparison diagram of stress-strain curves of a graphene-wrapped SiC particle reinforced aluminum matrix composite material and a SiC particle reinforced aluminum matrix composite material predicted by the model constructed in step 3 of the present invention;

[0041] Figure 4 This is a diagram of the damage evolution process of the interface cohesive force unit of the graphene-wrapped SiC particle reinforced aluminum-based composite material of the present invention. DETAILED DESCRIPTION

[0042] The following will be combined with the drawings in the embodiments of this application to clearly and completely describe the technical solutions in the embodiments of this application. Obviously, the embodiments described are only part of the embodiments of this application, not all of the embodiments. Based on the embodiments in this application, all other embodiments obtained by ordinary technicians in this field without making creative efforts are within the scope of protection of this application.

[0043] Example 1

[0044] The method for predicting the mechanical properties of the graphene-coated SiC particle reinforced aluminum-based composite material of the present invention specifically comprises the following steps:

[0045] Step 1: Prepare a graphene-wrapped SiC particle reinforced aluminum matrix composite sample by a solvothermal method, and measure its microscopic characteristics and macroscopic elastic-plastic mechanical properties;

[0046] Step 2, establishing a representative volume unit of the graphene-wrapped SiC particle reinforced aluminum matrix composite material based on the microscopic features obtained in step 1;

[0047] Step 3: Based on the mechanical characteristics of the metal aluminum matrix, graphene, SiC particles and the interface phase, a constitutive model of the plasticity and damage coupling of each component phase and the composite material is established to predict the mechanical properties of the graphene-wrapped SiC particle reinforced aluminum matrix composite material.

[0048] Example 2

[0049] This embodiment is based on Example 1. In step 1 of the present invention, a solvent thermal method is used to prepare a sample of graphene-wrapped SiC particle-reinforced aluminum-based composite material. Specifically, aluminum salt, carbon-containing compound, SiC particles, organic solvent and surfactant are prepared. The SiC particles are ultrasonically dispersed in an organic solvent, a surfactant is added to prevent agglomeration, and then mixed with a precursor solution containing aluminum salt and carbon-containing compound. The mixed solution is transferred to a stainless steel autoclave with a polytetrafluoroethylene lining and reacted at 150°C to 300°C for 10 to 24 hours to carbonize the carbon-containing material and convert the aluminum salt. After the product is cooled, it is washed and dried to obtain a composite powder, which is mixed with aluminum powder and hot-pressed and sintered at 500 to 600°C and 10 to 50 MPa to produce a graphene-wrapped SiC particle-reinforced aluminum-based composite material.

[0050] The microscopic characteristics of the graphene-wrapped SiC particles reinforced aluminum matrix composite material are measured using scanning electron microscopy and transmission electron microscopy, such as Figure 1 As shown in Figure 3, the microscopic characteristics include the spatial distribution of SiC particles, the size of SiC particles in the graphene-wrapped layer, and the microscopic characteristics of the interface layer.

[0051] Furthermore, the microscopic characteristics of the interface layer refer to whether the interface products can be observed and the thickness of the interface layer.

[0052] Under quasi-static loading, the macroscopic elastic-plastic mechanical properties of graphene-wrapped SiC particle reinforced aluminum matrix composites were measured by an electronic universal testing machine.

[0053] Example 3

[0054] This embodiment is based on embodiment 2. Figure 2 As shown, step 2 of the present invention establishes a periodic representative volume element (RVE) based on the microscopic characteristics of the graphene-wrapped SiC particle-reinforced aluminum-based composite material obtained in step 1. Specifically, graphene-wrapped SiC core-shell particles are first constructed to be periodically distributed in the cubic cell to form a geometric model of the RVE; in order to meet the continuity of stress and the coordination of displacement on the boundary of the representative volume element, the nodes on the symmetry plane of the representative volume element need to correspond one to one and have equal stress and deformation, that is, a periodic displacement boundary condition needs to be applied to the boundary of the RVE.

[0055] On a pair of boundary surfaces of a representative volume unit, the expression of the periodic displacement field applied is shown in formula (1):

[0056] (1);

[0057] in, is the average strain of RVE; is the coordinate of any node of RVE; superscript and Indicates the positive and negative directions of the global coordinate axis. For each set of relatively parallel faces of the representative volume unit model, is a constant. If , then the right side of formula (1) is a constant, that is, formula (1) does not contain the periodic displacement correction. Therefore, in the finite element analysis, the periodic boundary conditions can be applied to the three faces of the representative volume unit model of the graphene-wrapped SiC particle reinforced aluminum matrix composite material by applying multi-point constraint equations.

[0058] Example 4

[0059] In this embodiment, based on the embodiment 3, the mechanical characteristics of the graphene and SiC particles in step 3 of the present invention can be obtained by consulting existing literature, and the mechanical characteristics of the metal aluminum matrix are obtained by tensile testing. The mechanical characteristics of the metal aluminum matrix specifically include:

[0060] During the initial stretching phase, stress and strain are proportional, and the material undergoes elastic deformation. After unloading, the deformation fully recovers. The elastic modulus can be obtained at this stage, reflecting the aluminum matrix's ability to resist elastic deformation and serving as an indicator of the material's stiffness.

[0061] When the stress reaches a certain value, the material begins to show obvious plastic deformation. The stress corresponding to 0.2% plastic strain is recorded as yield strength, which is an indicator of the resistance of the aluminum matrix material to plastic deformation.

[0062] After yielding, as the plastic deformation increases, the strength of the material gradually increases, and the stress needs to be continuously increased to make the material continue to deform. This indicates that the material has undergone work hardening. At this stage, the tensile strength can be obtained, which is the maximum stress that the material can withstand in a tensile test.

[0063] When the stress reaches the tensile strength, the material begins to neck in a localized area, with deformation concentrated at the necking point, ultimately leading to fracture. Tensile testing can also measure elongation and reduction of area, which are important indicators of the plasticity of aluminum-based materials. Higher elongation and reduction of area indicate greater plasticity.

[0064] The mechanical characteristics of the interfacial phase in step 3 are inferred by inverse analysis of tensile tests on graphene-wrapped SiC particles reinforced aluminum matrix composites. The inverse analysis technique is known in the art and will not be elaborated in detail in this proposal.

[0065] Example 5

[0066] In this embodiment, based on the embodiment 4, a constitutive model of plasticity and damage coupling of each component phase and the composite material is established in step 3 of the present invention:

[0067] The plastic constitutive model is shown in formula (2):

[0068] (2);

[0069] in, σ represents the flow stress, ε pl represents the effective plastic strain, and A 、 B 、 C 、 M and N represent the yield strength, hardening modulus, strain rate coefficient, temperature coefficient and hardening coefficient of the matrix respectively; C and M Both parameters are set to zero;

[0070] The damage constitutive model is shown in formula (3):

[0071] (3);

[0072] Where, is the failure strain, d 1 ~d 5 is the material damage related constant, p and q are the hydrostatic pressure and von- Mises Stress, where d 4 and d The value of 5 is zero.

[0073] Because the interface between graphene and the aluminum substrate is typically non-ideal, this paper employs three-dimensional cohesive elements (COH3D6) to describe interfacial effects. While the structure of cohesive elements appears consistent with that of solid elements, they offer advantages over solid elements in providing accurate solutions at large aspect ratios. Furthermore, cohesive elements can transmit and withstand tensile and shear strains but do not generate stress themselves, thus supporting only the traction-separation failure criterion. This paper employs a bilinear constitutive model, describing the constitutive structure through the relationship between stress and displacement.

[0074] In the linear elastic stage of the constitutive model, the stiffness of the interface internal force unit is K 0, the relationship between stress and displacement is shown in formula (4):

[0075] (4);

[0076] in, t n is the normal stress, t s is the tangential stress, δ n is the positive displacement, δ s is the tangential displacement.

[0077] When the sum of the squares of the nominal stress ratios in all directions is equal to 1, damage begins to occur. The initial damage of the cohesive element adopts the quadratic nominal stress criterion in the traction-separation failure criterion, and its expression is shown in formula (5):

[0078] (5);

[0079] in, refers to the positive strength, and is the tangential strength; Ф 〉=( Ф +| Ф |) / 2, which means that the cohesive element will not be damaged under compressive stress. The interface element will degrade linearly if damaged: , D is the cohesive unit damage factor, D The corresponding values are 1 and 0 respectively. D =0, the stiffness is the initial value without any change, and D = 1, the stiffness degenerates to 0.

[0080] When a cohesive unit fails, its displacement is determined by the fracture energy G, as shown in formula (6):

[0081] (6);

[0082] in, and are the normal fracture energy and normal critical fracture energy, and are the tangential fracture energy and the tangential critical fracture energy, respectively.

[0083] Example 6

[0084] Based on Example 5, this embodiment predicts the mechanical properties of the graphene-wrapped SiC particle reinforced aluminum-based composite material. Specifically, based on the macroscopic mechanical properties of the composite material obtained in step 1, the stress-strain data when the volume fraction of the graphene-wrapped SiC particles is zero is selected, and the plasticity and damage-related parameters in the constitutive model are obtained by data fitting; the constitutive model constructed based on the microscopic parameters of the graphene and SiC particles in the composite material is substituted into the constructed model for solution to obtain the entire stress-strain curve of the graphene-wrapped SiC particle reinforced aluminum-based composite material.

[0085] Furthermore, the constitutive prediction model of the present invention is solved using the ABAQUS explicit solver.

[0086] The stress-strain process of graphene-wrapped SiC particle reinforced aluminum matrix composites and SiC particle reinforced aluminum matrix composites was compared, such as Figure 3 As shown in the figure, with the addition of graphene, the tensile strength and failure strain of the composite material are significantly improved, mainly due to the unique advantages of graphene's onion-like shell structure and negative thermal expansion coefficient in preventing SiC particle agglomeration and regulating interface bonding strength and wettability.

[0087] Record the damage evolution of the interface cohesive unit of graphene-wrapped SiC particle reinforced aluminum matrix composites during loading, such as Figure 4 As shown, it reveals the experimental observation ( Figure 1 ) interface effect phenomenon. A suitable interface effect can effectively enhance the pinning ability of SiC particles in the matrix and delay the direct destruction of graphene-wrapped SiC particles. It is a key factor in enhancing the plastic properties of composite materials.

[0088] The various embodiments in this specification are described in a progressive manner, and each embodiment focuses on the differences from other embodiments. The same or similar parts between the various embodiments can be referenced to each other.

[0089] The above description of the disclosed embodiments is intended to enable one skilled in the art to implement or use the present application. Various modifications to these embodiments will be readily apparent to one skilled in the art, and the general principles defined herein may be implemented in other embodiments without departing from the spirit or scope of the present application. Therefore, the present application is not limited to the embodiments shown herein, but is intended to conform to the widest scope consistent with the principles and novel features disclosed herein.

Claims

1. A method for predicting the mechanical properties of graphene-coated SiC particles reinforced aluminum matrix composites, characterized in that: The specific steps include: Step 1: Prepare a graphene-wrapped SiC particle reinforced aluminum matrix composite sample by a solvothermal method, and measure its microscopic characteristics and macroscopic elastic-plastic mechanical properties; Step 2, establishing a representative volume unit of the graphene-wrapped SiC particle reinforced aluminum matrix composite material based on the microscopic features obtained in step 1; Step 3: Based on the mechanical characteristics of the aluminum matrix, graphene, SiC particles, and the interface phase, a constitutive model for the plasticity and damage coupling of each component phase and the composite material is established to predict the mechanical properties of the graphene-coated SiC particle reinforced aluminum matrix composite material; Specifically, the step 2 of establishing the representative volume unit comprises first constructing graphene-wrapped SiC core-shell particles so that they are periodically distributed in cubic cells to form a geometric model of the representative volume unit; The expression for the periodic displacement field applied on a pair of boundary surfaces of a representative volume element is given by: ； in, is the average strain of the representative volume element; is the coordinate of any node of the representative volume element; and Indicates the positive and negative direction of the overall coordinate axis; In step 3, a constitutive model of plasticity and damage coupling of each component phase and the composite material is established: The plastic constitutive model is shown as follows: ； in, σ represents the flow stress, ε pl represents the effective plastic strain, and A 、 B 、 C 、 M and N represent the yield strength, hardening modulus, strain rate coefficient, temperature coefficient and hardening coefficient of the matrix respectively; C and M Both parameters are set to zero; The damage constitutive model can be expressed as: ； Where, is the failure strain, d 1 ~d 5 is the material damage related constant, p and q are the hydrostatic pressure and von-Mises Stress, where d 4 and d The value of 5 is zero; In the linear elastic stage of the constitutive model, the stiffness of the interface internal force unit is K 0, the relationship between stress and displacement is shown as follows: ； Where, t n is the normal stress, t s is the tangential stress, δ n is the positive displacement, δ s is the tangential displacement; When the sum of the squares of the nominal stress ratios in all directions is equal to 1, damage begins to occur. The initial damage of the cohesive element adopts the quadratic nominal stress criterion in the traction-separation failure criterion, as shown in the following formula: ； Where, refers to the positive strength, and is the tangential strength; Ф 〉=( Ф +| Ф |) / 2, which means that the cohesive element does not suffer damage under compressive stress; When a cohesive unit fails, its displacement is determined by the fracture energy G, as shown in the following formula: ； Where, and are the normal fracture energy and normal critical fracture energy, and are the tangential fracture energy and the tangential critical fracture energy, respectively.

2. The method for predicting the mechanical properties of graphene-coated SiC particles reinforced aluminum matrix composite materials according to claim 1, characterized in that: In the step 1, a solvothermal method is used to prepare a sample of graphene-wrapped SiC particle-reinforced aluminum-based composite material. Specifically, aluminum salt, carbon-containing compound, SiC particles, organic solvent and surfactant are selected, the SiC particles are ultrasonically dispersed in the organic solvent, and after adding the surfactant, the mixture is mixed with a precursor solution containing aluminum salt and carbon-containing compound to obtain a mixed solution; the mixed solution is transferred to a stainless steel high-pressure reactor with a polytetrafluoroethylene liner, and reacted at a temperature of 150°C to 300°C for 10h to 24h; after cooling, the composite powder is washed and dried to obtain a composite powder, the composite powder is mixed with aluminum powder, and hot-pressed and sintered at 500°C to 600°C and 100MPa to 50MPa to obtain a graphene-wrapped SiC particle-reinforced aluminum-based composite material.

3. The method for predicting the mechanical properties of graphene-coated SiC particles reinforced aluminum matrix composite materials according to claim 1, characterized in that: The microscopic characteristics measured in step 1 specifically include using scanning and transmission electron microscopy to characterize the microscopic characteristics of the graphene-wrapped SiC particle reinforced aluminum-based composite material, wherein the microscopic characteristics include the spatial distribution of the SiC particles, the size characteristics of the graphene-wrapped SiC particles, and the microscopic characteristics of the interface layer; The macroscopic elastic-plastic mechanical properties of graphene-wrapped SiC particles reinforced aluminum matrix composites were measured using an electronic universal testing machine.

4. The method for predicting the mechanical properties of graphene-coated SiC particles reinforced aluminum matrix composite materials according to claim 1, characterized in that: The mechanical characteristics of the metal aluminum matrix in step 3 are obtained by performing a tensile test on the metal aluminum matrix, and the mechanical characteristics of the interface phase are obtained by inverse deduction of a tensile test on a graphene-wrapped SiC particle reinforced aluminum matrix composite material.

5. The method for predicting the mechanical properties of graphene-coated SiC particles reinforced aluminum matrix composite materials according to claim 1, characterized in that: When making the prediction in step 3, based on the macroscopic mechanical properties of the composite material obtained in step 1, the stress-strain data when the volume fraction of the graphene-wrapped SiC particles is zero is selected, and the plasticity and damage-related parameters in the constitutive model are obtained by data fitting; the microscopic parameters of the graphene and SiC particles in the composite material are substituted into the constructed constitutive model for solution.

6. The method for predicting the mechanical properties of graphene-coated SiC particles reinforced aluminum matrix composite materials according to claim 5, characterized in that: The constitutive model is solved using the ABAQUS explicit solver.

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