A method and system for constructing a constitutive model of a multilayer iron-based amorphous alloy matrix.

Abstract

This application discloses a method and system for constructing a constitutive model of a laminated iron-based amorphous alloy matrix, relating to the field of characterization technology for the mechanical properties of metallic materials. This application obtains the overall Poisson's ratio and Young's modulus of the laminated material through static compression and nanoindentation; it inverts the intrinsic Poisson's ratio of the strip based on the mechanical coupling relationship of the laminated structure; it uses the elastic limit to correlate quasi-static parameters with dynamic impact experiments, inverting to obtain impact dynamic parameters; it performs regression fitting on wide strain rate data to obtain the first strength parameter; it constructs a numerical simulation model, and obtains the second strength parameter through iterative optimization and decoupling; and it regresses the damage evolution parameters based on the ultimate plastic strain evolution data extracted from the simulation. In this way, the interference of the epoxy resin layer on the mechanical parameters of the strip can be effectively eliminated, achieving accurate calibration of all parameters of the constitutive model of the laminated iron-based amorphous alloy matrix from quasi-static to high strain rate conditions, thereby significantly improving the simulation prediction accuracy under dynamic conditions such as abrasive impact.

Description

Technical Field

[0001] This application relates to the technical field, and in particular to a method and system for constructing a constitutive model of a multilayer iron-based amorphous alloy matrix. Background Technology

[0002] Iron-based amorphous alloys possess excellent soft magnetic properties and low iron loss characteristics, making them suitable as novel soft magnetic materials for manufacturing stator cores in high-speed, high-frequency motors. To meet the forming and service requirements of stator cores, a thickness of approximately 25 mm is typically required. Iron-based amorphous alloy strip with a thickness of approximately 2 A laminated iron-based amorphous alloy bulk was prepared by alternating layers of epoxy resin. Iron-based amorphous alloys typically exhibit a brittle-elastic response under quasi-static compression conditions, but under high-speed impact loads, they are prone to complex failure behaviors such as rapid crack initiation and propagation, interlayer delamination, interfacial debonding, brittle fracture, and powdering. To study interfacial debonding and delamination in laminated iron-based amorphous alloys through numerical simulation, the laminated iron-based amorphous alloy cannot be simply treated as a whole; it is necessary to model the iron-based amorphous alloy layers and epoxy resin layers separately. Therefore, to accurately describe the impact response process of iron-based amorphous alloys in numerical simulations, a material constitutive model that can comprehensively characterize pressure-related strength, strain rate effects, damage accumulation evolution, and state equation response is required.

[0003] Constitutive models of materials are typically used to describe the dynamic response of brittle materials such as ceramics, glass, and rocks under high pressure, high strain rate, and impact loads, from integrity to damage to fragmentation. In related technologies, the construction methods for constitutive models are mainly designed for bulk brittle materials or bulk amorphous alloys. Iron-based amorphous alloy strips in laminated iron-based amorphous alloys differ significantly from traditional bulk materials, exhibiting characteristics such as extremely thin thickness, significant interlayer constraints, complex stress states, and inconsistent dynamic response behavior compared to bulk materials. Directly applying parameters from bulk materials to construct constitutive models can easily lead to parameter distortion, resulting in significant discrepancies between numerical simulation results and actual material responses. This makes it difficult to accurately reveal the damage evolution and material removal mechanisms under impact loads or high-speed particle erosion. Summary of the Invention

[0004] This application provides a method and system for constructing a constitutive model of a laminated iron-based amorphous alloy matrix to solve the following technical problem: how to effectively eliminate the interference of the epoxy resin layer on the mechanical parameters of the strip, and achieve accurate calibration of all parameters of the constitutive model of the laminated iron-based amorphous alloy matrix from quasi-static to high strain rate.

[0005] In a first aspect, embodiments of this application provide a method for constructing a constitutive model of a multilayer iron-based amorphous alloy matrix, the method comprising: Obtain the overall Poisson's ratio of the laminated iron-based amorphous alloy and the Young's modulus of the iron-based amorphous alloy strip; Based on the mechanical coupling relationship of the stacked structure, the overall Poisson's ratio of the stacked iron-based amorphous alloy, the Young's modulus of the iron-based amorphous alloy strip, and the prior parameters of the epoxy resin are inverted and calculated to obtain the intrinsic Poisson's ratio of the iron-based amorphous alloy strip. Based on the Young's modulus, intrinsic Poisson's ratio, and material density of the iron-based amorphous alloy strip, the velocity history of free-surface particles is parametrically inverted to obtain the impact dynamics parameters of the iron-based amorphous alloy strip. Based on the impact dynamics parameters of the iron-based amorphous alloy strip, the strength formula regression fitting process is performed on the stress-strain data with a wide strain rate to obtain the first strength parameter of the constitutive model of the laminated iron-based amorphous alloy matrix. Based on the Young's modulus of the iron-based amorphous alloy strip, the intrinsic Poisson's ratio of the iron-based amorphous alloy strip, and the first strength parameter, the constitutive model of the laminated iron-based amorphous alloy matrix is ​​iteratively optimized to obtain the second strength parameter of the constitutive model of the laminated iron-based amorphous alloy matrix. Based on the first strength parameter and the second strength parameter, regression processing is performed on the ultimate plastic strain evolution data in the numerical simulation model to obtain the damage evolution parameters of the constitutive model of the laminated iron-based amorphous alloy matrix, so as to complete the construction of the constitutive model of the laminated iron-based amorphous alloy matrix.

[0006] Secondly, embodiments of this application also provide a system for constructing a constitutive model of a multilayer iron-based amorphous alloy matrix. The system includes: at least one processor; and a memory communicatively connected to the at least one processor; wherein the memory stores instructions executable by the at least one processor, the instructions being executed by the at least one processor to enable the at least one processor to perform a method for constructing a constitutive model of a multilayer iron-based amorphous alloy matrix as described above.

[0007] Thirdly, embodiments of this application also provide a computer storage medium storing computer-executable instructions, which, when executed, implement a method for constructing a constitutive model of a multilayer iron-based amorphous alloy matrix as described above.

[0008] The method and system for constructing a constitutive model of a multilayer iron-based amorphous alloy matrix provided in this application have the following beneficial effects: First, by obtaining the overall Poisson's ratio of the laminate and the Young's modulus of the strip, benchmark data is provided for subsequent elimination of interlayer coupling effects. Next, the intrinsic Poisson's ratio of the strip is inverted based on the mechanical coupling relationship of the laminated structure, effectively eliminating the interference of the epoxy resin soft phase and restoring the true elastic properties of the strip. Subsequently, impact dynamic parameters are inverted using the intrinsic parameters of the strip combined with the particle velocity history of the free surface, establishing a physical link from quasi-static elastic parameters to the dynamic Hugoniot state. Based on this, the first strength parameter is obtained by regression fitting of the wide strain rate data using impact dynamic parameters, establishing a benchmark for the strength response under intact material conditions. Then, the first strength parameter and elastic parameters are iteratively optimized to decouple and obtain the second strength parameter, solving the problem of strong coupling between the fracture strength parameter and the pressure hardening index. Finally, the ultimate plastic strain evolution data in the simulation is extracted based on the previously determined strength parameters and state equation parameters, and the damage evolution parameters are obtained through regression. This achieves full parameter coverage from elasticity and strength to damage failure, significantly improving the prediction fidelity of the constitutive model under impact loads. Attached Figure Description

[0009] The accompanying drawings, which are included to provide a further understanding of this application and form part of this application, illustrate exemplary embodiments and are used to explain this application, but do not constitute an undue limitation of this application. In the drawings: Figure 1 A flowchart illustrating a method for constructing a constitutive model of a multilayer iron-based amorphous alloy matrix, as provided in this application embodiment; Figure 2 A schematic flowchart illustrating the constitutive model construction method for the iron-based amorphous alloy JH-2 provided in this application embodiment; Figure 3 A simplified diagram of the plate impact test apparatus and experimental setup provided in the embodiments of this application; Figure 4 This is a schematic diagram of the finite element model for numerical simulation of a plate impact test provided in an embodiment of this application; Figure 5 A schematic diagram comparing the numerical simulation results of particle velocities on the free surface of the sample with the results of a plate impact experiment provided in the embodiments of this application; Figure 6 This is a schematic diagram of a single spherical abrasive particle impacting a multilayer iron-based amorphous alloy, provided in an embodiment of this application. Figure 7 A schematic diagram of numerical simulation results of single spherical abrasive particles impacting laminated iron-based amorphous alloys provided in this application embodiment; Figure 8 A schematic diagram of a finite element model of multiple abrasive particles impacting a multilayer iron-based amorphous alloy, provided in an embodiment of this application. Figure 9A schematic diagram of numerical simulation results of multiple abrasive particles impacting a multilayer iron-based amorphous alloy provided in an embodiment of this application; Figure 10 This is a schematic diagram of the internal structure of a system for constructing a constitutive model of a multilayer iron-based amorphous alloy matrix, as provided in an embodiment of this application. Detailed Implementation

[0010] To make the objectives, technical solutions, and advantages of this application clearer, the technical solutions of this application will be clearly and completely described below in conjunction with specific embodiments and corresponding drawings. Obviously, the described embodiments are only a part of the embodiments of this application, and not all of them. Based on the embodiments in this application, all other embodiments obtained by those skilled in the art without creative effort are within the scope of protection of this application.

[0011] It is understood that in the embodiments of this application, data related to user information (such as user accounts) is involved. When the embodiments of this application are applied to specific products or technologies, user permission or consent is required, and the collection, use and processing of related data must comply with relevant laws, regulations and standards.

[0012] Unless otherwise defined, all technical and scientific terms used herein have the same meaning as commonly understood by one of ordinary skill in the art to which this application belongs. The terminology used herein is for the purpose of describing embodiments of this application only and is not intended to limit this application.

[0013] In the following description, the terms “first, second, ...” are used merely to distinguish similar objects and do not represent a specific ordering of objects. It is understood that “first, second, ...” may be interchanged in a specific order or sequence where permitted, so that the embodiments of this application described herein can be implemented in an order other than that illustrated or described herein.

[0014] Iron-based amorphous alloys possess excellent soft magnetic properties and low iron loss characteristics, making them suitable as novel soft magnetic materials for manufacturing stator cores in high-speed, high-frequency motors. To meet the forming and service requirements of stator cores, a thickness of approximately 25 mm is typically required. Iron-based amorphous alloy strip with a thickness of approximately 2 A laminated iron-based amorphous alloy bulk was prepared by alternating layers of epoxy resin. Iron-based amorphous alloys typically exhibit a brittle-elastic response under quasi-static compression conditions, but under high-speed impact loads, they are prone to complex failure behaviors such as rapid crack initiation and propagation, interlayer delamination, interfacial debonding, brittle fracture, and powdering. To study interfacial debonding and delamination in laminated iron-based amorphous alloys through numerical simulation, the laminated iron-based amorphous alloy cannot be simply treated as a whole; it is necessary to model the iron-based amorphous alloy layers and epoxy resin layers separately. Therefore, to accurately describe the impact response process of iron-based amorphous alloys in numerical simulations, a material constitutive model that can comprehensively characterize pressure-related strength, strain rate effects, damage accumulation evolution, and state equation response is required.

[0015] Constitutive models of materials are typically used to describe the dynamic response of brittle materials such as ceramics, glass, and rocks under high pressure, high strain rate, and impact loads, from integrity to damage to fragmentation. In related technologies, the construction methods for constitutive models are mainly designed for bulk brittle materials or bulk amorphous alloys. Iron-based amorphous alloy strips in laminated iron-based amorphous alloys differ significantly from traditional bulk materials, exhibiting characteristics such as extremely thin thickness, significant interlayer constraints, complex stress states, and inconsistent dynamic response behavior compared to bulk materials. Directly applying parameters from bulk materials to construct constitutive models can easily lead to parameter distortion, resulting in significant discrepancies between numerical simulation results and actual material responses. This makes it difficult to accurately reveal the damage evolution and material removal mechanisms under impact loads or high-speed particle erosion.

[0016] Based on this, the present application provides a method for constructing a constitutive model of a laminated iron-based amorphous alloy matrix, which can effectively eliminate the interference of the epoxy resin layer on the mechanical parameters of the strip, and realize the full parameter accurate calibration of the constitutive model of the laminated iron-based amorphous alloy matrix from quasi-static to high strain rate, thereby significantly improving the simulation prediction accuracy under dynamic working conditions such as abrasive impact.

[0017] The technical solutions proposed in the embodiments of this application will be described in detail below with reference to the accompanying drawings.

[0018] Figure 1This document provides a flowchart of a method for constructing a constitutive model of a laminated iron-based amorphous alloy substrate, as illustrated in an embodiment of this application. This method can be applied to various numerical simulation and analysis scenarios. For example, in the scenario of predicting abrasive erosion wear of laminated iron-based amorphous alloy coatings in aerospace / precision equipment, the method provided in this application obtains complete constitutive model parameters, assigns them to the laminated iron-based amorphous alloy substrate elements in finite element software, establishes a three-dimensional model of abrasive particles impacting the laminated surface at different angles and velocities, applies corresponding impact conditions, runs explicit dynamic simulation, and calls the constitutive model to calculate stress wave propagation, equivalent plastic strain accumulation, and damage variable development within the strip. Afterwards, post-processing is used to read damage cloud maps and element deletion criteria to predict the depth of abrasive erosion pits, spalling area, and mass loss rate, guiding coating thickness and process selection. In the scenario of optimizing process parameters for preparing laminated amorphous alloy layers using high-speed cold spraying or hot spraying, the constitutive model is obtained through the method provided in this application, and the model is then used to... The input parameters include the strain rate range corresponding to different impact velocities. Using the impact dynamics and strength parameters calibrated in this scheme, the simulation of local adiabatic heating, plastic work, and interface-induced deformation during particle-substrate collision is performed. The simulation compares whether the substrate undergoes excessive fragmentation or insufficient bonding under different process parameters, and uses the simulation results to select a reasonable spraying speed and temperature window. In the scenario of evaluating the penetration resistance of laminated amorphous alloy composite armor in ship / ballistics structures, the constitutive model of the laminated iron-based amorphous alloy substrate constructed in this application is assembled with an epoxy resin laminate structure into a composite target model. Long rods or spherical projectiles are set to penetrate with different initial velocities, and transient nonlinear explicit calculations are run. Based on the calibrated integrity / fracture strength branches and damage initiation criteria, the constitutive model automatically determines the entire process of shear band initiation-expansion-fracture of the iron-based amorphous layer under high pressure, outputting the projectile's remaining velocity, backplate bulge height, and delamination failure location for evaluating the armor's penetration resistance margin and lightweight structural design. Some input parameters or intermediate results in the process allow for manual adjustment to help improve accuracy.

[0019] This application provides a method for constructing a constitutive model of a layered iron-based amorphous alloy matrix. It should be noted that the execution entity in this specification can be a server or any terminal device with data processing capabilities. For example, the server can be an independent physical server, a server cluster or distributed system composed of multiple physical servers, or a cloud server providing basic cloud computing services such as cloud services, cloud databases, cloud computing, cloud functions, cloud storage, network services, cloud communication, middleware services, domain name services, security services, content delivery networks (CDNs), and big data and artificial intelligence platforms. The terminal device can be a smartphone, tablet, laptop, desktop computer, smart speaker, smartwatch, in-vehicle terminal, etc., but is not limited to these.

[0020] like Figure 1 As shown in the embodiments of this application, a method for constructing a constitutive model of a multilayer iron-based amorphous alloy matrix specifically includes the following steps: Step 101: Obtain the overall Poisson's ratio of the laminated iron-based amorphous alloy and the Young's modulus of the iron-based amorphous alloy strip.

[0021] It should be noted that laminated iron-based amorphous alloys refer to layered metal-polymer composite materials formed by alternating layers of iron-based amorphous alloy strips and polymer binders, followed by hot-pressing and curing; the overall Poisson's ratio refers to the absolute value of the ratio of transverse strain to axial strain in a laminated iron-based amorphous alloy block under axial compressive load; iron-based amorphous alloy strips are amorphous metal strips obtained by rapidly cooling molten iron-based alloys through a single-roll rapid quenching process, and their atomic arrangement lacks long-range order, exhibiting high hardness, high elastic limit, and no obvious work hardening behavior; Young's modulus is the ratio of stress to strain in the linear elastic stage of a material, used to characterize the material's ability to resist axial elastic deformation.

[0022] In some embodiments, step 101 described above can be implemented by: statically compressing the laminated iron-based amorphous alloy to obtain the transverse strain and axial strain of the laminated iron-based amorphous alloy; taking the negative of the ratio of the transverse strain to the axial strain as the overall Poisson's ratio of the laminated iron-based amorphous alloy; performing nanoindentation on the iron-based amorphous alloy strip to obtain a load-displacement curve, and performing fitting analysis on the load-displacement curve to obtain the Young's modulus of the iron-based amorphous alloy strip.

[0023] Thus, on the one hand, by statically compressing the laminated iron-based amorphous alloy block, the transverse and axial strains at the macroscopic scale are directly obtained, and the overall Poisson's ratio is determined using the inverse of their ratio. This process is simple to operate and the data is reliable, effectively reflecting the macroscopic mechanical response of composite materials including epoxy resin, providing realistic boundary constraints for subsequent inversion calculations. On the other hand, addressing the pain point that the iron-based amorphous alloy strip is extremely thin and it is difficult to obtain elastic parameters through traditional tensile tests, nanoindentation technology is used to directly test the surface of the strip. Young's modulus is extracted through the fitting analysis of the load-displacement curve. This method has a small test scale and controllable indentation depth, which can greatly avoid the interference of the substrate effect and ensure the accuracy of the intrinsic elastic parameters of the strip. Therefore, this scheme, through the combination strategy of "macroscopic compression + microindentation", can both retain the overall coupling information of the laminated structure and accurately peel off the intrinsic properties of the strip, laying a solid data foundation for subsequent inversion of the intrinsic Poisson's ratio based on the mechanical coupling relationship of the laminated structure, fundamentally solving the problem of parameter distortion caused by component mixing in laminated composite materials.

[0024] It should be noted that static compression refers to applying a slowly increasing axial load along a principal axis of the specimen, causing the strain rate to typically be below 10. -3 s -1 Compression experiments ensure the material is in a quasi-static equilibrium state, neglecting inertial effects and temperature rise. Axial strain refers to the relative elongation of the specimen along the loading axis. Transverse strain refers to the relative deformation of the specimen in the direction perpendicular to the loading axis. Nanoindentation is an instrumented micro / nanoscale indentation experiment in which an indenter with a known geometry is pressed into the material surface with a submicron-scale displacement, and the load and indentation depth are continuously recorded to obtain the local elastoplastic response of the material. The load-displacement curve is a continuous curve recording the change of the axial load of the indenter with the indentation depth during the indentation process.

[0025] As an example, a strip made of iron-based amorphous alloy (each layer approximately 25 mm thick) ) and epoxy resin (each layer is approximately 2 Taking the laminated iron-based amorphous alloy block formed by alternating hot pressing and curing as an example, the laminated block is first processed into a prism specimen with dimensions of 6 mm × 6 mm × 12 mm (width × depth × height), and the loading direction is parallel to the normal direction of the laminate; then, quasi-static compression is performed on an electronic universal testing machine in displacement control mode, and the strain rate is controlled at 1 × 10⁻⁶. -4 s -1 An axial extensometer and a transverse extensometer (or a digital image correlation (DIC) system) are installed in the axial direction and perpendicular to the axial direction of the sample, respectively, to collect axial displacement data in real time during the loading process. With lateral displacement Subsequently, the axial strain was calculated according to formulas (1) and (2). With transverse strain Then, the overall Poisson's ratio of the laminated amorphous alloy was calculated according to formula (3). Simultaneously, a single layer of iron-based amorphous alloy strip was peeled from the same stacked test block, flattened and fixed on the sample stage of a nanoindenter. A Berkovich three-phase pyramid indenter was used, and nanoindentation tests were performed at multiple points (e.g., a 9-point matrix) on the strip surface. The maximum indentation depth was set to 300–500 nm, much smaller than the strip thickness, to ensure negligible substrate effects. The indenter load was continuously recorded. With indentation depth The changing relationship yields the load. Displacement curve ( (curve), and on The unloading segment of the curve is fitted with Oliver-Pharr, based on the initial unloading slope (i.e., contact stiffness). Calculate the reduced modulus Then, by combining the indenter and the Poisson's ratio of the sample, the Young's modulus of the iron-based amorphous alloy strip is calculated. .

[0026] (1) (2) (3) in, The initial axial length of the sample is denoted as . The initial transverse width of the sample.

[0027] Step 102: Based on the mechanical coupling relationship of the stacked structure, the overall Poisson's ratio of the stacked iron-based amorphous alloy, the Young's modulus of the iron-based amorphous alloy strip, and the prior parameters of the epoxy resin are inverted and calculated to obtain the intrinsic Poisson's ratio of the iron-based amorphous alloy strip.

[0028] It should be noted that the mechanical coupling relationship of the laminated structure refers to the physical relationship describing the mutual constraint of stress, strain, and deformation of each single layer (iron-based amorphous alloy strip layer and epoxy resin layer) when they are jointly subjected to external load, which ultimately manifests as the overall macroscopic response of the laminate. The prior parameters of the epoxy resin are the intrinsic mechanical properties of the epoxy resin itself, determined through independent experiments or pre-determined material properties before inversion calculation of the laminated structure, such as the Young's modulus, intrinsic Poisson's ratio, and single-layer thickness of the epoxy resin. The intrinsic Poisson's ratio refers to the absolute value of the ratio of transverse strain to axial strain of the iron-based amorphous alloy strip material itself under uniaxial stress, that is, the true Poisson's ratio of the strip as a unidirectional material after removing the influence of the epoxy resin layer and interlayer constraints.

[0029] In some embodiments, step 102 described above can be implemented as follows: multiplying the Young's modulus of the iron-based amorphous alloy strip by the single-layer thickness of the iron-based amorphous alloy layer in the laminated iron-based amorphous alloy to obtain the stiffness weight of the iron-based amorphous alloy layer; multiplying the Young's modulus in the prior parameters of the epoxy resin by the single-layer thickness of the epoxy resin layer in the laminated iron-based amorphous alloy to obtain the stiffness weight of the epoxy resin layer; and solving the mechanical coupling relationship of the laminated structure based on the stiffness weight of the iron-based amorphous alloy layer, the stiffness weight of the epoxy resin layer, the overall Poisson's ratio of the laminated iron-based amorphous alloy, and the intrinsic Poisson's ratio in the prior parameters of the epoxy resin to obtain the intrinsic Poisson's ratio of the iron-based amorphous alloy strip.

[0030] Thus, by multiplying the Young's modulus of the strip by the thickness of a single layer to obtain the stiffness weight, and simultaneously calculating the stiffness weight of the epoxy resin layer, the complex interlayer coupling effect can be simplified into a weighted summation decoupling problem based on the axial stiffness ratio. The physical meaning is clear and the mathematical processing is efficient, avoiding the computational redundancy caused by traditional trial-and-error methods or complex microstructure modeling. Furthermore, by using the known overall Poisson's ratio of the laminate and the prior parameters of the epoxy resin, combined with the constructed mechanical coupling relationship for inversion calculation, the lifting effect of the soft phase resin on the overall macroscopic response can be effectively eliminated, restoring the true transverse shrinkage characteristics of the strip. This approach not only solves the technical problem of not being able to directly measure the Poisson's ratio of the strip due to interlayer constraints, but also provides accurate intrinsic elastic input for subsequent impact dynamics parameter inversion, ensuring the physical self-consistency of the entire constitutive model in the elastic stage, thereby fundamentally improving the prediction accuracy of stress wave propagation and damage evolution in the dynamic simulation of laminated composite materials.

[0031] It should be noted that the stiffness weight of the iron-based amorphous alloy layer refers to the ability of the iron-based amorphous alloy layer to resist elastic deformation in the axial direction, while the stiffness weight of the epoxy resin layer refers to the ability of the epoxy resin adhesive layer to resist elastic deformation in the axial direction.

[0032] As an example, taking a laminated iron-based amorphous alloy as an example, the laminate is formed by alternately laying iron-based amorphous alloy strips and epoxy resin, and then hot-pressing and curing them. The thickness of a single layer of the iron-based amorphous alloy strip is... 25 The thickness of a single layer of epoxy resin 2 Furthermore, the overall Poisson's ratio of the laminated iron-based amorphous alloy was obtained through measurement and calculation. The Young's modulus of the iron-based amorphous alloy strip is 0.31. 165 Young's modulus in the prior parameters of epoxy resin It is 3.2 Intrinsic Poisson's ratio The value is 0.36; firstly, the stiffness weight of the iron-based amorphous alloy layer is calculated according to formula (4). The stiffness weight of the epoxy resin layer is calculated according to formula (5). Subsequently, the intrinsic Poisson's ratio of the iron-based amorphous alloy strip was calculated by inversion using formula (6). .

[0033] (4) (5) (6) Step 103: Based on the Young's modulus, intrinsic Poisson's ratio, and material density of the iron-based amorphous alloy strip, perform parameter inversion on the free surface particle velocity history to obtain the impact dynamics parameters of the iron-based amorphous alloy strip.

[0034] It should be noted that the free surface particle velocity history refers to the curve of the velocity of a particle on the free surface of the back of the target plate changing with time in a planar impact (or flyer plate loading) experiment; the impact dynamic parameters refer to a set of material constants required to describe the dynamic response of iron-based amorphous alloy strips under one-dimensional strain high strain rate impact loads, which are usually obtained by joint inversion of plate impact experimental data and intrinsic elastic parameters of the strip.

[0035] In some embodiments, step 103 described above can be implemented as follows: Based on one-dimensional strain theory, the inflection point of the elastic precursor wave in the velocity history of free-surface particles is identified, and based on the Young's modulus, the intrinsic Poisson's ratio, and the material density of the iron-based amorphous alloy strip, the velocity amplitude of the elastic precursor wave inflection point is mapped to obtain the elastic limit parameter in the impact dynamics parameters; based on the linear relationship between shock wave velocity and particle velocity, the shock wave velocity and particle velocity in the impact experiment are fitted to obtain the shock wave velocity parameter in the shock wave mechanical parameters; based on the elastic limit parameter, the Young's modulus, the intrinsic Poisson's ratio, and the material density of the iron-based amorphous alloy strip, the relationship between impact pressure and volumetric strain is fitted to obtain the state equation parameter in the shock wave mechanical parameters.

[0036] Thus, by using one-dimensional strain theory to identify the inflection point of the elastic precursor wave in the velocity history of free-surface particles, and combining it with the accurately inverted intrinsic elastic parameters of the strip, the velocity amplitude is mapped to the elastic limit parameter. This not only accurately captures the critical threshold of the material's transition from elastic to plasticity, but also verifies the correctness of the previous intrinsic parameter calibration, providing a reliable physical benchmark for subsequent strength normalization. Furthermore, by fitting multiple experimental data based on the linear relationship between shock wave velocity and particle velocity, the shock wave velocity parameters describing the high-pressure response can be determined, thereby effectively establishing a quantitative relationship between impact pressure and material kinematics. In addition, by comprehensively utilizing the elastic limit parameter and the intrinsic properties of the strip, the relationship between impact pressure and volumetric strain is fitted to obtain the parameters of the equation of state. By organically coupling the material's hydrodynamic response and solid mechanical response, the constitutive model can be ensured to reflect both the strength effect and accurately simulate compression hardening characteristics when describing high-strain-rate large deformation behavior. Through progressive parameter calculation, a complete bridge is built from experimental observation to theoretical model, which can significantly improve the prediction fidelity of numerical simulation of laminated iron-based amorphous alloys under extreme impact loads.

[0037] It should be noted that one-dimensional strain theory refers to a simplified wave theory in which, during a plate impact, the material is allowed to produce strain in the loading direction (usually the z-axis), while being constrained and having approximately zero strain in the other two perpendicular directions (x and y axes). The elastic limit parameter refers to the critical stress value corresponding to the transition from purely elastic behavior to elastic-plastic behavior under one-dimensional strain impact loading conditions, commonly known as the Hugoniot elastic limit. The elastic precursor wave inflection point refers to the first significant velocity step caused by the arrival of the elastic wave in the free-surface particle velocity path during a plate impact experiment, corresponding to the moment when the elastic longitudinal wave traverses the target plate and reflects off the free surface. The velocity amplitude refers to the magnitude of the velocity step caused by the elastic precursor wave in the free-surface particle velocity path, i.e., the difference between the elastic precursor wave plateau value and the baseline value before impact. An impact experiment involves using a light gas cannon or Hopkinson pressure bar to launch a flying plate (usually made of the same material or impedance-matching material) at a controlled velocity, impacting the target plate head-on, and then using a laser velocity interferometry system for any reflector (VISAR) or a photonic Doppler velocimeter. Doppler Velocimetry (PDV) is an experiment that records the velocity-time history of particles on the free surface of the back of a target plate; the parameters of the equation of state are constants that describe the relationship between pressure and volumetric strain during the impact compression of a material.

[0038] As an example, taking a multilayer target plate made of iron-based amorphous alloy strip as an example, a plate impact experiment was conducted using a light gas gun, and the particle velocity history on the free surface of the back of the target plate was recorded using a VISAR interferometer. Young's modulus of iron-based amorphous alloy strip 165 Intrinsic Poisson's ratio The density of the material is 0.28. It is 7.18 First, in Identify the inflection point of the elastic precursor wave on the curve, i.e., the location of the first obvious velocity step, and read the velocity amplitude of that step. 85 Next, the one-dimensional strain longitudinal wave velocity is calculated according to formula (7). The Hugoniot elastic limit of the iron-based amorphous alloy strip was calculated according to the one-dimensional strain theory mapping relationship (formula (8)). (Corresponding to elastic limit parameters); subsequently, multiple star impact experiments were conducted (impact velocities 200–800 km / h). ), speed of each record flying chip Given the propagation time of the shock wave in the target, calculate the corresponding shock wave velocity. With particle velocity (For example ); then, multiple sets of experimental data ( , According to linear relationship Least squares fitting is performed to obtain the shock wave velocity parameters. (Typically close to one-dimensional strained longitudinal wave velocity) (sound intercept) and slope (Range 1.4~1.6); Finally, take the first-order bulk modulus. for Utilizing the impact pressure corresponding to HEL and higher pressure points ( , )data( The polynomial state equation (formula (9)) is fitted to determine the second-order coefficients. and third-order coefficients This yields the state equation parameters in the shock wave mechanical parameters.

[0039] (7) (8) (9) Step 104: Based on the impact dynamics parameters of the iron-based amorphous alloy strip, perform strength formula regression fitting on the stress-strain data with wide strain rate to obtain the first strength parameter of the constitutive model of the laminated iron-based amorphous alloy matrix.

[0040] It should be noted that the wide strain rate stress Strain data refers to data covering the range from quasi-static to high strain rates (typically spanning 10). -4 s -1 Up to 10 3 s -1 The above is a set of experimental data on flow stress-plastic strain; the strength formula is the formula in the constitutive model that describes the equivalent flow stress of the material in the undamaged state; the constitutive model of the laminated iron-based amorphous alloy matrix refers to the model used to describe the stress of the iron-based amorphous alloy strip in the laminate under impact / high strain rate loads. strain In this application, the mathematical model for the damage response is the JH-2 model, where JH is the constitutive model. Model 2 is an elastic model proposed by Johnson and Holmquist to describe the dynamic mechanical behavior of materials with high strain rates, large deformations, and damage evolution (such as ceramics, glass, metallic glass, concrete, etc.). Plastic damage constitutive model; the first strength parameter refers to JH 2. Core coefficients used in the constitutive model to describe the strength response of materials in an undamaged (intact) state include bond strength parameters, pressure hardening parameters, strain rate sensitive parameters, and dimensionless maximum fracture strength parameters.

[0041] In some embodiments, the first strength parameter includes a bond strength parameter, a pressure hardening parameter, a strain rate sensitive parameter, and a dimensionless maximum breaking strength parameter; step 104 above can be implemented as follows: based on the elastic limit parameter in the impact dynamics parameters, the stress-strain data with a wide strain rate is processed to be dimensionless to obtain dimensionless strength values, dimensionless hydrostatic pressure, and dimensionless strain rate; based on the strength formula, the dimensionless strength values, the dimensionless hydrostatic pressure, and the dimensionless strain rate are subjected to multiple regression fitting to obtain the bond strength parameter, the pressure hardening parameter, and the strain rate sensitive parameter; the maximum value among the dimensionless strength values ​​is taken as the dimensionless maximum breaking strength parameter.

[0042] Thus, by using the elastic limit parameter in impact dynamics as a normalization benchmark, the nominal stress, hydrostatic pressure, and strain rate at different strain rates are transformed into dimensionless forms. This effectively eliminates the interference of differences in the inherent strength magnitude of the material on the regression fitting, making direct comparison and joint fitting across experimental data possible, thereby significantly improving the physical consistency and statistical significance of the first strength parameter. Furthermore, based on this, multivariate regression fitting of the dimensionless strength value, dimensionless hydrostatic pressure, and dimensionless strain rate using the strength formula can clearly separate the pressure hardening effect, strain rate sensitivity, and normalized strength level under normal pressure, thus avoiding parameter drift caused by multi-factor coupling. At the same time, directly taking the maximum value in the dimensionless strength dataset as the dimensionless maximum intact fracture strength parameter can accurately define the critical threshold for the material to transform from an intact state to a fractured state, providing reliable boundary constraints for subsequent iterative optimization of the second strength parameter and damage evolution calculation, thereby ensuring the prediction accuracy of the entire constitutive model within the intact strength range.

[0043] It should be noted that the bond strength parameter refers to the initial strength multiple of the intact material relative to the Hugoniot elastic limit under dimensionless pressure or reference pressure; the pressure hardening parameter refers to the power law exponent describing the rate of increase of flow stress with hydrostatic pressure in the strength formula; the strain rate sensitivity parameter is used to describe the amplification factor of material strength with logarithmic strain rate; the dimensionless maximum fracture strength parameter refers to the maximum dimensionless flow stress that can be reached in the intact (undamaged) material branch, and exceeding this value is considered that the material has begun to enter the damage evolution (fracture) branch.

[0044] As an example, assuming the impact dynamics parameters of the iron-based amorphous alloy strip have been obtained through inversion, the Hugoniot elastic limit... It is 4.9 The corresponding hydrostatic pressure for Reference strain rate For 1 s -1 Wide strain rate stress Strain data sources include quasi-static compression experiments ( =10 -4 ~ 10 -2 s -1 ) and multiple SHPB experiments ( =5×10 2 ~ 5×10 3 s -1 First, for the flow stress in each set of data... Corresponding hydrostatic pressure and the applied strain rate Dimensionless values ​​were obtained by performing dimensionless processing on each of the following. Dimensionless hydrostatic pressure and dimensionless strain rate The specific dimensionless processing can be referred to formulas (10)-(12); then, the JH-2 complete strength formula (formula (13)) is used, and the bond strength parameters are obtained by multivariate nonlinear regression fitting of the whole dataset. Pressure hardening parameters Strain rate sensitive parameters ,For example 0.79, 0.80, 0.0035; Finally, from all dimensionless intensity values The maximum value is selected as the dimensionless maximum intact fracture strength parameter. ,For example 3.6.

[0045] (10) (11) (12) (13) Step 105: Based on the Young's modulus of the iron-based amorphous alloy strip, the intrinsic Poisson's ratio of the iron-based amorphous alloy strip, and the first strength parameter, iteratively optimize the constitutive model of the laminated iron-based amorphous alloy matrix to obtain the second strength parameter of the constitutive model of the laminated iron-based amorphous alloy matrix.

[0046] It should be noted that the second strength parameter refers to JH 2. The strength coefficients used in the constitutive model to describe the variation of residual flow stress with hydrostatic pressure and strain rate after damage (i.e., fracture / failure state) of the material are called fracture strength branch parameters; the second strength parameters include fracture strength parameters and the most extreme fracture pressure hardening parameters.

[0047] In some embodiments, the second strength parameter includes an optimal fracture strength parameter and an optimal fracture pressure hardening parameter; step 105 described above can be implemented as follows: based on the Young's modulus of the iron-based amorphous alloy strip, the intrinsic Poisson's ratio of the iron-based amorphous alloy strip, and the first strength parameter, a numerical simulation model consistent with the plate impact test conditions is constructed; the fracture pressure hardening parameter in the numerical simulation model is set to a preset value, simulation calculations are performed within the preset value range of the fracture strength parameter, and the fracture strength parameter corresponding to the minimum error between the free surface particle velocity curve output by the numerical model and the measured curve in the physical experiment is taken as the optimal fracture strength parameter; the fracture strength parameter in the numerical simulation model is set as the optimal fracture strength parameter, simulation calculations are performed within the value range of the fracture pressure hardening parameter, and the fracture pressure hardening parameter corresponding to the minimum error between the free surface particle velocity curve output by the numerical model and the measured curve in the physical experiment is taken as the optimal fracture pressure hardening parameter.

[0048] Thus, by constructing a numerical simulation model that is completely consistent with the experimental conditions of a flat plate impact, and strictly locking the precisely calibrated elastic parameters, impact dynamic parameters, and first strength parameters of the strip, it is possible to ensure that the iterative optimization process focuses only on the mechanical response of the fractured branch, thereby effectively avoiding ill-conditioned inversion problems caused by multi-parameter coupling. In the first iteration stage, the fracture pressure hardening parameter is fixed to a preset value. By traversing the fracture strength parameters and comparing the simulation and measured free surface particle velocity curve errors, the fractured material under low pressure can be accurately captured. The residual strength level in the medium-pressure region is used to determine the optimal fracture strength parameters. In the second iteration, the locked optimal fracture strength parameters are used to further traverse the fracture pressure hardening parameters, which can finely characterize the rate of increase in the strength of the fractured material in the high-pressure region with pressure, thereby determining the optimal fracture pressure hardening parameters. Through this phased optimization mechanism with the minimum global waveform error as the convergence criterion, not only can the physical rationality and numerical stability of the fracture branch parameters be significantly improved, but also the constitutive model can be guaranteed to highly restore the real stress wave propagation characteristics and energy dissipation behavior when describing the dynamic response of the material from intact to fractured, thereby greatly enhancing the prediction confidence of laminated iron-based amorphous alloys in impact simulation.

[0049] It should be noted that the optimal crushing strength parameter refers to the parameter at JH. In the fracture (failure) strength branch formula of the constitutive model, the optimal value of the fracture strength parameter is determined by benchmarking the particle velocity curves of the free surface of the plate impact numerical simulation and the physical experiment, with the minimum error between the two as the convergence target; the optimal fracture pressure hardening parameter refers to the optimal value of the fracture pressure hardening index determined by continuing to traverse the pressure hardening index and using the minimum error between the simulation and the experimental free surface particle velocity curves as the criterion in the same JH-2 fracture strength branch, under the premise that the optimal fracture strength parameter has been locked.

[0050] As an example, assuming the parameters of the iron-based amorphous alloy strip are already known, such as Young's modulus... 165 Intrinsic Poisson's ratio The density of the material is 0.28. It is 7.18 g / cm 3 Impact mechanics parameters and first strength parameters, in explicit finite element software (such as LS). A one-dimensional impact model of the flying plate and target plate was established in DYNA, and the target plate material was given the above-mentioned JH Two parameters (state equation + first intensity parameter) completely replicate the physical plate impact experiment conditions of the flyer plate and target geometry, impact velocity, and boundary conditions, and output the particle velocity history of the free surface at the center node on the back of the target plate. Subsequently, the hardening parameter M of the crushing pressure is fixed to a preset initial value (e.g., M=0.3), and within a reasonable range (e.g., B=0.05~0.6, with a step size of 0.02), values ​​are assigned sequentially and the simulation is run. The difference between each set of simulation curves and the experimentally measured free surface velocity curves (e.g., root mean square error) is calculated, and the crushing strength parameter corresponding to the smallest difference (i.e., the smallest error) is selected as the optimal crushing strength parameter. Then, the crushing strength parameter was fixed at the optimal crushing strength parameter. The simulation is iterated within a reasonable range (e.g., M=0.1~0.6, step size 0.02), and the difference between each set of simulated curves and experimentally measured free surface velocity curves is calculated. The crushing pressure hardening parameter corresponding to the smallest difference (i.e., the smallest error) is selected as the optimal crushing pressure hardening parameter. .

[0051] Step 106: Based on the first strength parameter and the second strength parameter, perform regression processing on the ultimate plastic strain evolution data in the numerical simulation model to obtain the damage evolution parameters of the constitutive model of the laminated iron-based amorphous alloy matrix, so as to complete the construction of the constitutive model of the laminated iron-based amorphous alloy matrix.

[0052] It should be noted that the ultimate plastic strain evolution data refers to the JH strain with pre-assigned calibration parameters (elastic parameters, equation of state, first strength parameters A, N, C, and second strength parameters B, M). In the numerical simulation model, multiple sets of binary data are obtained by post-processing and extracting the damage accumulation (or the sudden increase in equivalent plastic strain / the last convergence step before element failure) that occurs for the first time during the impact loading process. The damage evolution parameters refer to the two coefficients in the JH-2 constitutive model that describe the change of equivalent plastic strain with hydrostatic pressure that is allowed for material failure.

[0053] In some embodiments, the damage evolution parameters include plastic failure strain parameters and damage pressure-sensitive parameters. The step 106 above, which involves regressing the ultimate plastic strain evolution data in the numerical simulation model based on the first strength parameter and the second strength parameter to obtain the damage evolution parameters of the constitutive model of the laminated iron-based amorphous alloy matrix, can be achieved as follows: Simulate the numerical simulation model based on the first strength parameter and the second strength parameter, and extract the equivalent plastic strain and corresponding hydrostatic pressure at the moment the material first accumulates damage, obtaining ultimate plastic strain evolution data; perform dimensionless processing on the hydrostatic pressure in the ultimate plastic strain evolution data based on the elastic limit parameter to obtain dimensionless hydrostatic pressure; perform logarithmic domain linear regression on the ultimate plastic strain evolution data and the dimensionless hydrostatic pressure based on the initial damage formula of the constitutive model of the laminated iron-based amorphous alloy matrix to obtain a fitting function; use the intercept of the fitting function as the plastic failure strain parameter, and use the slope of the fitting function as the damage pressure-sensitive parameter.

[0054] Thus, by strictly locking the first and second strength parameters obtained through precise inversion and iteration, it can be ensured that the simulation model can realistically reproduce the dynamic response path of the material from elasticity and strengthening to damage initiation, thereby guaranteeing the physical credibility of the ultimate plastic strain evolution data extracted from it. Furthermore, by using the elastic limit parameter to perform dimensionless processing on hydrostatic pressure, the difference in the magnitude of material strength can be eliminated, allowing the failure plastic strain under different pressure levels to be regressed under a unified physical benchmark. By using logarithmic domain linear regression to process the initial damage formula, the complex power-law relationship is transformed into a linear equation, which not only simplifies the parameter solution process and avoids the uncertainty of nonlinear optimization, but also allows for the direct and accurate analysis of damage pressure-sensitive parameters and plastic failure strain parameters by using the slope and intercept of the fitted line. Moreover, this scheme can cleverly transform the calibration of damage parameters into simulation data mining of the already constructed complete model without relying on additional fracture toughness or fatigue experiments. While ensuring the physical self-consistency of the parameters, it significantly reduces the calibration cost, ultimately achieving full parameter coverage from total elasticity and strength to damage and failure, and enabling the complete construction of the constitutive model of the laminated iron-based amorphous alloy matrix.

[0055] It should be noted that the plastic failure strain parameter is a pre-coefficient in the JH-2 initial damage formula, used to represent the ultimate equivalent plastic strain that the material can withstand under the reference dimensionless hydrostatic pressure; the damage pressure sensitivity parameter is the power-law exponent in the JH-2 damage initiation formula that describes the change of ultimate plastic strain with dimensionless hydrostatic pressure; hydrostatic pressure refers to the spherical part of the stress tensor at a certain point that causes volume change; and the equivalent plastic strain is a scalar quantity that describes the cumulative irreversible deformation of the material during loading.

[0056] As an example, assume that the JH-2 constitutive model of the laminated iron-based amorphous alloy matrix has been completed and calibrated, including the elastic parameters of the strip ( , , Impact dynamic parameters () , ), first strength parameters (A, N, C, ) and the second strength parameter ( , First, in explicit finite element software, a simulation model of a plate impact or representative volume element (RVE) is constructed based on the complete parameter set mentioned above. A strong impact load (e.g., a flying plate velocity of 500 m / s) is applied. During the simulation calculation, the response of the integration points inside the target plate is monitored. When the loss variable D of a certain element first increases from 0 to 0.01 (or a set small threshold), it is determined that the element has first experienced damage accumulation, and the equivalent plastic strain of the element at that moment is extracted. and its corresponding hydrostatic pressure As a data point, by changing the impact velocity or adjusting the boundary constraints, the equivalent plastic strain under different pressure levels is repeatedly simulated and extracted in batches. and its corresponding hydrostatic pressure This constitutes a dataset of the evolution of limit plastic strain; subsequently, the elastic limit parameters are used... Calculate dimensionless hydrostatic pressure for Subsequently, based on the initial damage formula of the JH-2 model (Formula (14)), logarithmic domain linear regression was performed on the ultimate plastic strain evolution data and dimensionless hydrostatic pressure to obtain the fitted straight line equation (i.e., the fitted function y=kx+b), and the intercept b of the fitted straight line was used as the plastic failure strain parameter. The slope k of the fitted straight line is used as a pressure-sensitive parameter for damage. .

[0057] (14) In some embodiments, after performing step 106 above, the following processing may also be performed: inputting the working condition parameters of abrasive impact into the constitutive model of the laminated iron-based amorphous alloy matrix, and obtaining the stress cloud map, damage distribution cloud map and spalling morphology prediction results of the laminated iron-based amorphous alloy under abrasive impact through numerical simulation calculation.

[0058] Thus, by directly inputting specific operating parameters into the numerical simulation model, the precise constitutive relations established in the preceding steps can be used to reproduce the stress wave propagation, local adiabatic shear, and interlaminar crack propagation processes at the moment of contact between the abrasive grains and the target material with high fidelity. This results in the output of high-resolution stress cloud maps and damage distribution cloud maps. The visualization results can not only intuitively reveal the stress concentration areas and damage accumulation paths inside the material, but also restore the geometry of the impact crater and the characteristics of the spalled fragments through element deletion or section subdivision techniques. This effectively solves the problem that traditional empirical formulas cannot describe complex dynamic failure mechanisms. In addition, this solution can establish a closed loop from microscopic parameter calibration to macroscopic performance prediction, enabling researchers to quickly evaluate the contribution of different lamination processes to the resistance to erosion and wear without consuming a large number of physical samples. This provides a powerful digital simulation tool for optimizing material structure design and extending the service life of key components.

[0059] As an example, assuming the completed constitutive model of the JH-2 laminated iron-based amorphous alloy matrix is ​​obtained, including the elastic parameters of the strip ( , , Impact dynamic parameters () , ), first strength parameters (A, N, C, ), second strength parameter ( , ) and damage evolution parameters ( , In explicit finite element software (such as LS), A 3D model is created using DYNA or ABAQUS / Explicit, where the target is a stacked iron-based amorphous bulk, and the iron-based amorphous alloy strip layer imparts the aforementioned complete JH 2. Constitutive model, epoxy resin layer imparts corresponding elasticity Crisp or springy The plastic damage model uses spherical or angular silica or alumina particles as abrasives, which are set as rigid or deformable bodies and assigned corresponding density and elastic parameters. The abrasive impact parameters include a particle size of 50~200 mm. The incident velocity was 30–800 m / s, the impact angle was 15°–90°, and the ambient temperature was room temperature. Subsequently, the bottom surface of the target was fixed, and abrasive particles flew towards the target surface at a set velocity and angle. Erosion contact and element deletion were enabled, allowing material to be removed after severe damage to simulate spalling. Simulation results (stress tensor, equivalent plastic strain, and damage variables) were output. The simulation results were then analyzed to obtain corresponding simulation analysis results. For example, the von Willeness of the target surface / subsurface at the moment of impact was extracted. Mises or maximum principal stress distribution is used to identify stress concentration areas and shear zone initiation locations to obtain stress cloud maps; damage variables are used to display cloud maps, which intuitively show microcrack initiation, intralayer damage propagation, and interlayer debonding areas, resulting in damage distribution cloud maps; the contour of the impact crater is reconstructed based on the spatial distribution of damage variables ≥1 elements, and the volume / area of ​​deleted elements is statistically analyzed to predict the depth, diameter, and possible large-area spalling morphology of the erosion crater, resulting in spalling morphology prediction results.

[0060] The following will describe an exemplary application of the embodiments of this application in a real-world application scenario.

[0061] Iron-based amorphous alloys possess excellent soft magnetic properties and low iron loss characteristics, making them suitable as novel soft magnetic materials for manufacturing stator cores in high-speed, high-frequency motors. To meet the forming and service requirements of stator cores, a thickness of approximately 25 mm is typically required. Iron-based amorphous alloy strip with a thickness of approximately 2 A laminated iron-based amorphous alloy bulk was prepared by alternating layers of epoxy resin. Iron-based amorphous alloys typically exhibit a brittle-elastic response under quasi-static compression conditions, but under high-speed impact loads, they are prone to complex failure behaviors such as rapid crack initiation and propagation, interlayer delamination, interfacial debonding, brittle fracture, and powdering. To study interfacial debonding and delamination in laminated iron-based amorphous alloys through numerical simulation, the laminated iron-based amorphous alloy cannot be simply treated as a whole; it is necessary to model the iron-based amorphous alloy layers and epoxy resin layers separately. Therefore, to accurately describe the impact response process of iron-based amorphous alloys in numerical simulations, a material constitutive model that can comprehensively characterize pressure-related strength, strain rate effects, damage accumulation evolution, and state equation response is required.

[0062] Constitutive models of materials are typically used to describe the dynamic response of brittle materials such as ceramics, glass, and rocks under high pressure, high strain rate, and impact loads, from integrity to damage to fragmentation. In related technologies, the construction methods for constitutive models are mainly designed for bulk brittle materials or bulk amorphous alloys. Iron-based amorphous alloy strips in laminated iron-based amorphous alloys differ significantly from traditional bulk materials, exhibiting characteristics such as extremely thin thickness, significant interlayer constraints, complex stress states, and inconsistent dynamic response behavior compared to bulk materials. Directly applying parameters from bulk materials to construct constitutive models can easily lead to parameter distortion, resulting in significant discrepancies between numerical simulation results and actual material responses. This makes it difficult to accurately reveal the damage evolution and material removal mechanisms under impact loads or high-speed particle erosion.

[0063] Based on this, this application provides a method for constructing a constitutive model of a laminated iron-based amorphous alloy matrix, which can accurately obtain the intrinsic elastic parameters, key strength and damage parameters of the strip, and construct a complete JH-2 parameter system suitable for its real dynamic response and failure behavior, thereby improving the accuracy and engineering applicability of numerical simulation results.

[0064] In some embodiments, see Figure 2 , Figure 2 This is a flowchart illustrating the constitutive model construction method for the iron-based amorphous alloy JH-2 provided in this application embodiment, as shown below. Figure 2 As shown, to establish a constitutive model for iron-based amorphous alloys over a wide strain rate range, this application, based on the theoretical framework of the JH-2 model, systematically calibrates the required parameters of the model by combining quasi-static compression experiments, nanoindentation experiments, Hopkinson bar experiments, and plate impact experiments. The acquisition of JH-2 model parameters follows a step-by-step determination approach of "basic material parameters—strength parameters—damage parameters—failure parameters." Specifically, the basic material parameters (including the material density of the iron-based amorphous alloy strip and epoxy resin) are first obtained through density testing, nanoindentation experiments, and quasi-static compression experiments. Young's modulusE and Poisson's ratio Based on this, and by fitting the state equation using the compression response data, the parameters of the JH-2 model are determined. (Corresponding to the parameters of the equation of state); subsequently, the mechanical response of the material under different strain rate conditions was obtained using quasi-static compression experiments and Hopkinson bar experiments, and the bond strength parameter, the first strength parameter in the JH-2 model parameters, was determined by fitting the complete material strength expression. Pressure hardening parameters Strain rate sensitive parameters For the optimal crushing strength parameter of the second strength parameter in the JH-2 model parameters under crushing conditions. The optimal fracture pressure hardening parameter M and related failure parameters in the JH-2 model. and σ * fmax The parameters are determined by combining impact test results, theoretical calculations, and numerical inversion. Finally, based on the dynamic damage and failure behavior of the material analyzed by plate impact tests, the damage parameters in the JH-2 model are determined. and Finally, based on the above experimental tests, parameter fitting and numerical correction, the calibration of all parameters of the iron-based amorphous alloy JH-2 model was completed.

[0065] In some embodiments, the Poisson's ratio of the laminated iron-based amorphous alloy as a whole is first determined by a quasi-static compression test, and the Young's modulus of the iron-based amorphous alloy strip is determined by a nanoindentation test. In the nanoindentation test, a nanoindenter is used to monitor the load and indentation depth, and a Berkovich indenter with an elastic modulus of 1140 is used. The Poisson's ratio is 0.07; the maximum load is set to 15 mN, the loading and unloading rates are both 30 mN / min, and the holding time is 10 s; in the nanoindentation experiment, the indentation depth is less than 0.3 μm, which is much smaller than the thickness of the iron-based amorphous alloy strip (25 μm). The indentation plastic zone is mainly limited to the interior of the iron-based amorphous alloy layer, and the influence of the epoxy resin layer can be ignored. Therefore, it can be considered that the measured mechanical response mainly reflects the properties of the iron-based amorphous alloy strip itself, so that its Young's modulus can be obtained more accurately. Among them, the relationship between the equivalent elastic model and the elastic modulus of the indenter and the elastic modulus of the measured material is shown in formula (15).

[0066] (15) in, The elastic modulus of the indenter. The Poisson's ratio of the pressure head. The elastic modulus of the material being tested. is the Poisson's ratio of the material being tested.

[0067] Following the above embodiments, based on the relationship between the overall Poisson's ratio of the laminated iron-based amorphous alloy and the Poisson's ratio, Young's modulus, and thickness of the iron-based amorphous alloy strip and epoxy resin, and combining the obtained overall Poisson's ratio of the laminated iron-based amorphous alloy and the Young's modulus of the iron-based amorphous alloy strip, the Poisson's ratio of the iron-based amorphous alloy strip is obtained by inversion using formulas (4)-(6). (Intrinsic Poisson's ratio); subsequently, a plate impact test was conducted (arranged as follows) Figure 3 As shown in (b), Figure 3 (a) Using a 105mm first-stage light gas gun for experimental setup, combined with PDV technology, the free-plane particle velocity history curves of the laminated iron-based amorphous alloy were obtained. Under the condition of plate impact loading, the sample was mainly under short-term high-pressure compressive stress. The interlayer interface tended to close under compression. The influence of interface debonding and delamination on the early wave propagation response was relatively small. Therefore, the stress wave propagation characteristics, Hugoniot elastic limit, and peak response of the sample were mainly controlled by the iron-based amorphous alloy strip body. Based on the plate impact test results, the Hugoniot elastic limit strength of the iron-based amorphous alloy was calculated. (Corresponding elastic limit parameters), Hugoniot parameters (Corresponding shock wave velocity parameters) )and (corresponding to slope s); subsequently, through quasi-static compression experiments and Hopkinson bar experiments, the strength response and strain evolution of the material under low and high strain rates were obtained (corresponding to stress-strain data over a wide strain rate range). Based on the JH-2 constitutive model and the JH-2 constitutive model construction method for iron-based amorphous alloys, combined with the calculated Hugoniot elastic limit strength... Hugoniot parameters , In addition, the strength response and strain evolution of the material under low and high strain rates were determined, and the material parameters B, M, and M were also analyzed. and Other constitutive parameters (corresponding to the first strength parameter) were then established. A numerical simulation model corresponding to the plate impact experiment was then developed, and LS-DYNA was used to simulate the plate impact experiment. To improve computational efficiency and simplify the model, the target ring used to fix the target plate was ignored without significantly affecting the research objectives. Only the process of copper flyer impacting the iron-based amorphous alloy sample was simulated, and the particle velocity history of the sample's free surface was used as the main indicator for evaluating the simulation results. For details, please refer to [reference needed]. Figure 4 As shown.

[0068] Following the above embodiments, based on the parameter distribution law of general brittle materials, the value ranges of parameters B and M are pre-defined; within the value range, coupled iterative analysis is performed on parameters B and M, and the optimal values ​​of parameters B and M are determined by comparing the error between the numerical simulation results and the plate impact test results; as shown in Table 1, firstly, M=0.5, and B takes values ​​of 0.1, 0.2, 0.3, 0.4, 0.5, 0.6, 0.7, 0.8, 0.9 (numbered 1-9); then, B=0.3, and M takes values ​​of 0.1, 0.2, 0.3, 0.4, 0.5, 0.6, 0.7, 0.8, 0.9 (numbered 10-18), and so on. Figure 5 For example, Figure 5 A schematic diagram comparing the numerical simulation results of particle velocities on the free surface of the sample with the results of the plate impact experiment when B=0.3 and M=0.25. Table 1 Numerical Simulation Calculation Parameters

[0069] Following the above embodiments, based on the calculated parameters B and M, the parameters are further determined. and Thus, all parameters of the JH-2 constitutive model are obtained.

[0070] In some embodiments, based on the constructed constitutive model of the iron-based amorphous alloy, numerical simulations of abrasive particle impact on the laminated iron-based amorphous alloy are performed, thereby revealing the material removal mechanism of abrasive waterjet processing of the laminated iron-based amorphous alloy; the model of a single abrasive particle (taking a spherical particle as an example) impacting the laminated iron-based amorphous alloy is as follows: Figure 6 As shown ( Figure 6 (a) is the corresponding geometric model structure diagram. Figure 6 (b) shows the corresponding finite element model structure diagram. The overall dimensions of the target material are 0.5 mm × 0.5 mm × 0.16 mm. To improve the calculation accuracy of the impact zone, the mesh is refined in the 0.3 mm × 0.3 mm × 0.16 mm area at the center of the target material. Based on the particle size characteristics of the selected 80-mesh abrasive, the diameter of the spherical abrasive particles is set to 180. ;for Figure 7 25 A thick iron-based amorphous alloy layer imparts a constitutive model to the iron-based amorphous alloy constructed using the method described in this application, which is used to reliably simulate the stress distribution, damage accumulation, and material removal responses of the iron-based amorphous alloy during abrasive particle impact. Subsequently, numerical simulations are performed to obtain results such as... Figure 7 The numerical simulation results shown are as follows: Figure 7As shown in (a), at t = 2.0142 × 10⁻⁵ ms, the abrasive particles first contact the target material, resulting in slight plastic deformation of the target surface and the formation of significant concentrated compressive stress in the contact area. The compressive stress wave in the abrasive particles originates from the contact point and propagates inward along a near-semi-circular path. At this time, the compressive stress in the target material has not yet propagated to the interlayer interface; the compressive stress wave is confined within the first layer of iron-based amorphous alloy and exhibits a relatively uniform semi-circular expansion characteristic. Figure 7 As shown in (b), when the impact reaches t = 3.0214 × 10⁻⁵ ms, the units on both sides of the abrasive particle impact contact area are destroyed and removed, and the compressive stress wave continues to propagate inward in a similar manner to the previous moment. Simultaneously, the plastic deformation of the impacted area of ​​the target material further increases. Observing the evolution of stress along the interlayer direction reveals that the stress state at the edge of the impact crater changes from compressive stress to tensile stress. This tensile stress causes local uplift and accumulation of the crater edge material, making its height exceed the original surface, thus forming a typical "crater-stacking" morphology. Further analysis of stress propagation along the stack direction reveals that the compressive stress wave has already penetrated the epoxy resin layer, causing the destruction and removal of some resin units in this area; corresponding to the actual processing process, this indicates that the interlayer resin first collapses under strong impact load, and its stress transmission capacity is essentially lost. Due to the destruction of the resin layer, the stress propagation in the target material no longer exhibits a strictly radial characteristic; a large amount of compressive stress remains trapped in the first layer of iron-based amorphous alloy and fails to be effectively transmitted to the second layer; only a small portion of the stress enters the second layer and continues to diffuse radially. Damage to the resin layer significantly weakens the continuous transmission of stress along the thickness of the laminate, making this area a weak point for subsequent damage, and thus more prone to the initiation and propagation of delamination damage. For example... Figure 7 As shown in (c), at t = 4.0285 × 10⁻⁵ ms, the compressive stress wave inside the abrasive particles continues to propagate radially inward. Some unremoved units remain in the impact contact area. Although these units have reached the energy required for destruction, further deformation accumulation is needed for complete removal. Simultaneously, the tensile stress at the edge of the first layer of iron-based amorphous alloy impact area further develops along the interlayer direction, and the accumulation morphology at the impact area edge becomes more pronounced. In the stacking direction, the first layer of iron-based amorphous alloy, after crushing the resin layer, continues to deform, forming contact with the second layer of iron-based amorphous alloy and transferring compressive stress to it. At this point, stress waves can also be observed to have propagated to the third layer of iron-based amorphous alloy. Although the resin layer between the second and third layers is not completely destroyed, due to the significant differences in stiffness and wave impedance between epoxy resin and iron-based amorphous alloy, the stress distribution in the second and third layers does not exhibit the typical regular radial propagation characteristic inside the abrasive particles, but rather a more complex interlayer non-uniform diffusion morphology. For example... Figure 7(d) The cross-sectional view in the middle and the isometric view on the right show that the destruction of spherical abrasive particles exhibits a clear "inside-out" characteristic. Figure 7 (d) In the intermediate cross-sectional view, many internal units of the abrasive particles have been removed, while in the right-hand isometric view, the external units of the abrasive particles are relatively intact. This indicates that the failure of the abrasive particles at this stage is not a simple surface peeling, but rather a fragmentation pattern of internal instability followed by outer shell cracking. Corresponding to the actual processing, spherical abrasive particles may first form cracks internally and allow them to propagate, subsequently extending to the surface and ultimately leading to overall fragmentation. Further observation of the stress evolution in the target material reveals that the compressive stress in the first layer of iron-based amorphous alloy has significantly decreased, indicating that the stress has been partially released through local plastic deformation and unit damage, after which the units in this region will be further destroyed and removed. Simultaneously, observation... Figure 7 (d) A magnified view reveals significant interfacial debonding in the epoxy resin layer between the first and second layers of the iron-based amorphous alloy. Figure 7 Similar to the crushing failure of the resin layer in (b), this interfacial debonding also weakens the interlayer load transfer capacity and induces or exacerbates the formation and propagation of delamination damage.

[0071] Therefore, from the perspective of the overall evolution process, when a single abrasive particle impacts a multilayer iron-based amorphous alloy, the target damage is not simply limited to local removal in the contact area, but rather involves a continuous evolution process of "contact compressive stress concentration—resin layer crushing / debonding—interlayer stress transmission obstruction—delamination damage propagation." This result can well explain the typical phenomena observed in the experiment, such as local delamination, interface opening, and pit edge accumulation.

[0072] In some embodiments, the finite element model of multiple abrasive particles impacting a laminated iron-based amorphous alloy is as follows: Figure 8 As shown, the overall dimensions of the target material are 2.4 mm × 2.4 mm × 0.7 mm, with a 2.0 mm × 2.0 mm × 0.7 mm region in the middle using a finer mesh. Numerical simulations were then performed, yielding the following results: Figure 9 The numerical simulation results of multiple abrasive particles impacting a laminated iron-based amorphous alloy are shown below. Figure 9 As shown in (a), at t=6.05×10⁻⁴ ms, after the first few abrasive particles impact the target, they mainly cause localized plastic deformation on the target surface, leading to damage or debonding of the interlayer epoxy resin. This means that the removal of the multilayered iron-based amorphous alloy material does not begin directly from the iron-based amorphous alloy layer, but follows a progressive damage pattern of "resin layer damage—interface delamination—removal of the iron-based amorphous alloy layer." Figure 9As shown in (b), as more abrasive particles impact different locations on the target, multiple independent pits and localized deformation zones gradually form on the target surface. Although the surface pits are not yet connected, the damaged areas of the interlayer resin phase show clear connections, indicating that the development of interlayer damage precedes the connection of the macroscopic surface pits, meaning that the evolution of internal damage precedes the significant connection of the surface morphology. Due to the combined effects of the destruction of the first and second interlayer resin phases and the impact of abrasive particles on adjacent areas, the first layer of iron-based amorphous alloy undergoes localized flaking, forming flaky fragments approximately 150 μm in length. This indicates that under continuous multi-particle impact conditions, the weakening of the interlayer support significantly reduces the stability of the surface iron-based amorphous alloy, thus promoting its removal through localized buckling instability and flaking. Figure 9 As shown in (c), with continued impact, delamination damage and the removal of iron-based amorphous alloy units accumulate, and the number of lamellar regions connected to the matrix by only a few units gradually increases. These regions are in an unstable connection state, and may subsequently peel off as a whole in the form of lamellar debris, or they may gradually undergo unit destruction and eventually be removed under the continuous impact of subsequent abrasive particles. This indicates that the material removal process under multi-particle impact conditions is not only characterized by a continuous damage mode of unit-by-unit erosion, but also by obvious lamellar peeling and local overall failure characteristics. In other words, material removal has a composite characteristic of "local erosion" and "lamellar peeling," the latter of which is particularly significant in layered materials. Figure 9 As shown in (d), the pit formed at this point has a certain depth. Due to the randomness in the shape, impact angle, and local quantity distribution of the abrasive particles involved in the impact, a relatively obvious undulating morphology is formed on the pit bottom surface. This undulating feature reflects the strong non-uniformity of local energy input during multi-particle impact. The local impact pits formed by different abrasive particles superimpose in space, ultimately shaping the pit bottom surface morphology with random fluctuation characteristics. Therefore, the rough undulation at the bottom of the pit is essentially the result of the combined effect of multi-particle discrete impact and the non-uniform evolution of local damage. Figure 9 As shown in (e), the pit depth continues to increase with the further increase in the number of impact abrasive particles. Simultaneously, the surface morphology dispersion caused by early variations in abrasive particle shape and fluctuations in the number of local impacts gradually weakens, specifically manifested in a decrease in the undulation of the pit bottom and a relatively smoother overall morphology. This indicates that when the number of impacting particles reaches a certain scale, the influence of the random impact effect of a single particle on the overall removal behavior is gradually averaged by the statistical cumulative effect of a large number of impact events, thus transforming the material removal behavior from an initial local random response to a more statistically stable removal process. Figure 9As shown in (f), at t = 167.65 × 10⁻⁴ ms, the abrasive particles have essentially completed the impact process, but some residual stress remains inside the target material that has not been fully released. Therefore, during the subsequent unloading process, local elements may continue to deform and be removed, and debonding and delamination damage at the interlayer interfaces will further develop. Thus, the damage evolution caused by multi-particle impact does not immediately end with the termination of the external impact load, but continues to develop for a period of time driven by residual stress.

[0073] Comprehensive analysis reveals that the damage evolution of laminated iron-based amorphous alloys under multi-particle abrasive impact exhibits distinct stage characteristics: in the initial stage of impact, damage is mainly concentrated in the interlayer resin phase and interface region; as the impact continues, the interlayer damage gradually connects, inducing localized lamellar delamination of the surface iron-based amorphous alloy; in the later stage of impact, the pits deepen continuously, and material removal gradually transforms from a localized random response to a statistically stable removal process. Overall, the material removal mechanism under multi-particle impact is not a simple layer-by-layer surface erosion, but rather the result of the coupled and synergistic evolution of interlayer damage, interface debonding, lamellar delamination, and localized overall failure.

[0074] The above are embodiments of the method proposed in this application. Based on the same inventive concept, embodiments of this application also provide a system for constructing a constitutive model of a multilayer iron-based amorphous alloy matrix, the structure of which is as follows: Figure 10 As shown.

[0075] Figure 10 This is a schematic diagram of the internal structure of a system for constructing a constitutive model of a layered iron-based amorphous alloy matrix, as provided in an embodiment of this application. Figure 10 As shown, the system includes: At least one processor 201; And a memory 202 that is communicatively connected to at least one processor; The memory 202 stores instructions that can be executed by at least one processor. The instructions are executed by at least one processor 201 to enable at least one processor 201 to perform the steps of the method corresponding to any of the above embodiments.

[0076] Some embodiments of this application provide corresponding to Figure 1 A non-volatile computer storage medium stores computer-executable instructions configured to perform the steps of the method corresponding to any of the above embodiments.

[0077] The various embodiments in this application are described in a progressive manner. Similar or identical parts between embodiments can be referred to mutually. Each embodiment focuses on describing the differences from other embodiments. In particular, the embodiments for IoT devices and media are basically similar to the method embodiments, so the description is relatively simple; relevant parts can be referred to the descriptions of the method embodiments.

[0078] The systems, media, and methods provided in this application are one-to-one correspondences. Therefore, the systems and media also have similar beneficial technical effects as their corresponding methods. Since the beneficial technical effects of the methods have been described in detail above, the beneficial technical effects of the systems and media will not be repeated here.

[0079] Those skilled in the art will understand that embodiments of this application can be provided as methods, systems, or computer program products. Therefore, this application can take the form of a completely hardware embodiment, a completely software embodiment, or an embodiment combining software and hardware aspects. Furthermore, this application can take the form of a computer program product embodied on one or more computer-usable storage media (including but not limited to disk storage, CD-ROM, optical storage, etc.) containing computer-usable program code.

[0080] This application is described with reference to flowchart illustrations and / or block diagrams of methods, apparatus (systems), and computer program products according to embodiments of this application. It will be understood that each block of the flowchart illustrations and / or block diagrams, and combinations of blocks in the flowchart illustrations and / or block diagrams, can be implemented by computer program instructions. These computer program instructions can be provided to a processor of a general-purpose computer, special-purpose computer, embedded processor, or other programmable data processing apparatus to produce a machine, such that the instructions, which execute via the processor of the computer or other programmable data processing apparatus, generate instructions for implementing the flowchart... Figure 1 One or more processes and / or boxes Figure 1 A device that provides the functions specified in one or more boxes.

[0081] These computer program instructions may also be stored in a computer-readable storage medium that can direct a computer or other programmable data processing device to function in a particular manner, such that the instructions stored in the computer-readable storage medium produce an article of manufacture including instruction means, which are implemented in a process Figure 1 One or more processes and / or boxes Figure 1 The function specified in one or more boxes.

[0082] These computer program instructions may also be loaded onto a computer or other programmable data processing equipment to cause a series of operational steps to be performed on the computer or other programmable equipment to produce a computer-implemented process, thereby providing instructions that execute on the computer or other programmable equipment for implementing the process. Figure 1 One or more processes and / or boxes Figure 1 The steps of the function specified in one or more boxes.

[0083] In a typical configuration, a computing device includes one or more processors (CPU), input / output interfaces, network interfaces, and memory.

[0084] Memory may include non-persistent storage in computer-readable media, such as random access memory (RAM) and / or non-volatile memory, such as read-only memory (ROM) or flash RAM. Memory is an example of computer-readable media.

[0085] Computer-readable media include both permanent and non-permanent, removable and non-removable media that can store information by any method or technology. Information can be computer-readable instructions, data structures, modules of programs, or other data. Examples of computer storage media include, but are not limited to, phase-change memory (PRAM), static random access memory (SRAM), dynamic random access memory (DRAM), other types of random access memory (RAM), read-only memory (ROM), electrically erasable programmable read-only memory (EEPROM), flash memory or other memory technologies, CD-ROM, digital versatile optical disc (DVD) or other optical storage, magnetic tape, magnetic magnetic disk storage or other magnetic storage devices, or any other non-transferable medium that can be used to store information accessible by a computing device. As defined herein, computer-readable media does not include transient computer-readable media, such as modulated data signals and carrier waves.

[0086] It should also be noted that the terms "comprising," "including," or any other variations thereof are intended to cover non-exclusive inclusion, such that a process, method, article, or apparatus that comprises a list of elements includes not only those elements but also other elements not expressly listed, or elements inherent to such a process, method, article, or apparatus. Without further limitation, an element defined by the phrase "comprising one..." does not exclude the presence of other identical elements in the process, method, article, or apparatus that includes said element.

[0087] The above description is merely an embodiment of this application and is not intended to limit the scope of this application. Various modifications and variations can be made to this application by those skilled in the art. Any modifications, equivalent substitutions, improvements, etc., made within the spirit and principles of this application should be included within the scope of the claims of this application.

Claims

1. A method for constructing a constitutive model of a layered iron-based amorphous alloy matrix, characterized in that, The method includes: Obtain the overall Poisson's ratio of the laminated iron-based amorphous alloy and the Young's modulus of the iron-based amorphous alloy strip; Based on the mechanical coupling relationship of the stacked structure, the overall Poisson's ratio of the stacked iron-based amorphous alloy, the Young's modulus of the iron-based amorphous alloy strip, and the prior parameters of the epoxy resin are inverted and calculated to obtain the intrinsic Poisson's ratio of the iron-based amorphous alloy strip. Based on the Young's modulus, intrinsic Poisson's ratio, and material density of the iron-based amorphous alloy strip, the velocity history of free-surface particles is parametrically inverted to obtain the impact dynamics parameters of the iron-based amorphous alloy strip. Based on the impact dynamics parameters of the iron-based amorphous alloy strip, the strength formula regression fitting process is performed on the stress-strain data with a wide strain rate to obtain the first strength parameter of the constitutive model of the laminated iron-based amorphous alloy matrix. Based on the Young's modulus of the iron-based amorphous alloy strip, the intrinsic Poisson's ratio of the iron-based amorphous alloy strip, and the first strength parameter, the constitutive model of the laminated iron-based amorphous alloy matrix is ​​iteratively optimized to obtain the second strength parameter of the constitutive model of the laminated iron-based amorphous alloy matrix. Based on the first strength parameter and the second strength parameter, regression processing is performed on the ultimate plastic strain evolution data in the numerical simulation model to obtain the damage evolution parameters of the constitutive model of the laminated iron-based amorphous alloy matrix, so as to complete the construction of the constitutive model of the laminated iron-based amorphous alloy matrix.

2. The method according to claim 1, characterized in that, The process of obtaining the overall Poisson's ratio of the laminated iron-based amorphous alloy and the Young's modulus of the iron-based amorphous alloy strip includes: The laminated iron-based amorphous alloy was subjected to static compression to obtain the transverse strain and axial strain of the laminated iron-based amorphous alloy. The negative of the ratio of the transverse strain to the axial strain is taken as the overall Poisson's ratio of the laminated iron-based amorphous alloy; Nanoindentation was performed on the iron-based amorphous alloy strip to obtain a load-displacement curve, and the Young's modulus of the iron-based amorphous alloy strip was obtained by fitting analysis of the load-displacement curve.

3. The method according to claim 1, characterized in that, The mechanical coupling relationship based on the stacked structure is used to invert the overall Poisson's ratio of the stacked iron-based amorphous alloy, the Young's modulus of the iron-based amorphous alloy strip, and the prior parameters of the epoxy resin to obtain the intrinsic Poisson's ratio of the iron-based amorphous alloy strip, including: The stiffness weight of the iron-based amorphous alloy layer is obtained by multiplying the Young's modulus of the iron-based amorphous alloy strip by the thickness of a single layer of the iron-based amorphous alloy layer in the laminated iron-based amorphous alloy. The stiffness weight of the epoxy resin layer is obtained by multiplying the Young's modulus in the prior parameters of the epoxy resin by the single-layer thickness of the epoxy resin layer in the laminated iron-based amorphous alloy. Based on the stiffness weight of the iron-based amorphous alloy layer, the stiffness weight of the epoxy resin layer, the overall Poisson's ratio of the laminated iron-based amorphous alloy, and the intrinsic Poisson's ratio in the prior parameters of the epoxy resin, the mechanical coupling relationship of the laminated structure is solved to obtain the intrinsic Poisson's ratio of the iron-based amorphous alloy strip.

4. The method according to claim 1, characterized in that, Based on the Young's modulus, intrinsic Poisson's ratio, and material density of the iron-based amorphous alloy strip, the free-plane particle velocity history is parametrically inverted to obtain the impact dynamic parameters of the iron-based amorphous alloy strip, including: Based on one-dimensional strain theory, the inflection point of the elastic precursor wave in the velocity history of free-surface particles is identified. Based on the Young's modulus, intrinsic Poisson's ratio, and material density of the iron-based amorphous alloy strip, the velocity amplitude of the elastic precursor wave inflection point is mapped to obtain the elastic limit parameter in the impact dynamics parameters. Based on the linear relationship between shock wave velocity and particle velocity, the shock wave velocity and particle velocity in the impact experiment are fitted to obtain the shock wave velocity parameter in the shock wave mechanical parameters. Based on the elastic limit parameter, the Young's modulus of the iron-based amorphous alloy strip, the intrinsic Poisson's ratio of the iron-based amorphous alloy strip, and the material density of the iron-based amorphous alloy strip, the relationship between impact pressure and volumetric strain is fitted to obtain the state equation parameters in the shock wave mechanical parameters.

5. The method according to claim 4, characterized in that, The first strength parameter includes the bond strength parameter, the pressure hardening parameter, the strain rate sensitive parameter, and the dimensionless maximum breaking strength parameter; The first strength parameters of the constitutive model of the laminated iron-based amorphous alloy matrix are obtained by performing strength formula regression fitting on the stress-strain data with a wide strain rate based on the impact dynamic parameters of the iron-based amorphous alloy strip, including: Based on the elastic limit parameter in the impact dynamics parameters, the stress-strain data with wide strain rate is processed to be dimensionless to obtain dimensionless strength value, dimensionless hydrostatic pressure and dimensionless strain rate. Based on the strength formula, the dimensionless strength value, the dimensionless hydrostatic pressure, and the dimensionless strain rate are subjected to multiple regression fitting to obtain the bond strength parameter, the pressure hardening parameter, and the strain rate sensitive parameter. The maximum value among the dimensionless strength values ​​is taken as the dimensionless maximum breaking strength parameter.

6. The method according to claim 1, characterized in that, The second strength parameter includes the optimal crushing strength parameter and the optimal crushing pressure hardening parameter; The method involves iteratively optimizing the constitutive model of the laminated iron-based amorphous alloy matrix based on the Young's modulus of the iron-based amorphous alloy strip, the intrinsic Poisson's ratio of the iron-based amorphous alloy strip, and the first strength parameter of the constitutive model of the laminated iron-based amorphous alloy matrix to obtain the second strength parameter of the constitutive model of the laminated iron-based amorphous alloy matrix, including: Based on the Young's modulus of the iron-based amorphous alloy strip, the intrinsic Poisson's ratio of the iron-based amorphous alloy strip, and the first strength parameter, a numerical simulation model consistent with the plate impact test conditions is constructed. The crushing pressure hardening parameter in the numerical simulation model is set to a preset value, and the simulation calculation is performed within the preset range of the crushing strength parameter. The crushing strength parameter corresponding to the minimum error between the free surface particle velocity curve output by the numerical model and the physical experimental measured curve is taken as the optimal crushing strength parameter. The crushing strength parameter in the numerical simulation model is set as the optimal crushing strength parameter. Simulation calculations are performed within the range of the crushing pressure hardening parameter. The crushing pressure hardening parameter corresponding to the minimum error between the free surface particle velocity curve output by the numerical model and the measured curve in the physical experiment is taken as the optimal crushing pressure hardening parameter.

7. The method according to claim 4, characterized in that, The damage evolution parameters include plastic failure strain parameters and damage pressure-sensitive parameters; The method involves regressing the ultimate plastic strain evolution data in the numerical simulation model based on the first strength parameter and the second strength parameter to obtain the damage evolution parameters of the constitutive model of the laminated iron-based amorphous alloy matrix, including: Based on the first strength parameter and the second strength parameter, the numerical simulation model is simulated, and the equivalent plastic strain and corresponding hydrostatic pressure at the moment when the material first shows damage accumulation are extracted to obtain the ultimate plastic strain evolution data. Based on the elastic limit parameter, the hydrostatic pressure in the ultimate plastic strain evolution data is dimensionlessly processed to obtain the dimensionless hydrostatic pressure. Based on the initial damage formula of the constitutive model of the laminated iron-based amorphous alloy matrix, logarithmic domain linear regression is performed on the ultimate plastic strain evolution data and the dimensionless hydrostatic pressure to obtain the fitting function; The intercept of the fitted function is used as the plastic failure strain parameter, and the slope of the fitted function is used as the damage pressure sensitive parameter.

8. The method according to claim 1, characterized in that, The method further includes: The working parameters of abrasive impact are input into the constitutive model of the laminated iron-based amorphous alloy matrix. The stress cloud map, damage distribution cloud map and spalling morphology prediction results of the laminated iron-based amorphous alloy under abrasive impact are obtained through numerical simulation calculation.

9. A system for constructing a constitutive model of a layered iron-based amorphous alloy matrix, characterized in that, The system includes: At least one processor; And, a memory communicatively connected to the at least one processor; The memory stores instructions that can be executed by the at least one processor to enable the at least one processor to perform the method as described in any one of claims 1-8.

10. A computer storage medium storing computer-executable instructions, characterized in that, When the computer-executable instructions are executed, they implement the method as described in any one of claims 1-8.

Images