Method and device for predicting creep deformation of nickel-based single crystal superalloy under creep-oxidation interaction

Abstract

The invention discloses a method and a device for predicting creep deformation of a nickel-based single-crystal high-temperature alloy under creep-oxidation interaction, and belongs to the technical field of material engineering and computational mechanics, and the method is based on microstructure distribution characteristics of the nickel-based single-crystal high-temperature alloy after a creep test in vacuum and atmospheric environments. According to the method, a dynamic growth multilayer geometric model considering oxidation influence is established, and a method capable of predicting alloy creep deformation in different environments is developed by combining a creep constitutive model considering microstructure evolution based on a test observation result. The method mainly comprises the following steps: providing a multilayer geometric model considering oxidation influence; establishing growth kinetic models of different layers; obtaining microstructure evolution laws at different depths; building a multi-scale creep deformation prediction framework considering microstructure evolution; and acquiring model parameters and predicting creep deformation. The invention provides a set of method capable of accurately predicting the creep deformation of the alloy in different environments.

Description

Technical Field

[0001] This invention belongs to the field of materials engineering and computational mechanics, specifically relating to a method and apparatus for predicting creep deformation of nickel-based single-crystal superalloys under creep-oxidation interaction. Background Technology

[0002] Nickel-based single-crystal superalloys are widely used in hot-end components such as turbine blades in aero-engines due to their excellent high-temperature mechanical properties. Although nickel-based single-crystal superalloys are usually used in the state of thermal barrier coating, once the thermal barrier coating fails, the exposed nickel-based single-crystal superalloy will inevitably face creep and oxidation damage under long-term high-temperature service loads. The synergistic effect of these two factors will significantly accelerate the deterioration of the mechanical properties of turbine blades. Therefore, studying the creep-oxidation interaction in nickel-based single-crystal superalloys is crucial to ensuring the reliability and service life of turbine blades.

[0003] Current predictions of creep deformation behavior of nickel-based single-crystal superalloys under the influence of oxidation have the following shortcomings: existing creep deformation behavior predictions usually do not take into account the influence mechanism of oxidation, such as the distribution of microstructure in the near-surface region of nickel-based single-crystal superalloys with depth caused by oxidation and the evolution of this distribution over time; and the established models are lacking in physical interpretability, failing to reveal the influence of oxidation on creep from the perspective of creep deformation mechanism. Summary of the Invention

[0004] To solve the above-mentioned technical problems, the present invention adopts the following technical solution:

[0005] A method for predicting creep deformation of nickel-based single-crystal superalloys under creep-oxidation interaction includes:

[0006] Step 1: Based on the microscopic observation results of creep tests in atmospheric and vacuum environments, a multi-layer geometric model considering the effects of oxidation is proposed.

[0007] Step 2: During the creep oxidation process, the thickness of each layer of the multi-layered geometric model inside the sample changes with time. By statistically analyzing the thickness of each layer at different times, a corresponding growth kinetic model is established.

[0008] Step 3: Based on the statistical results of the microstructure evolution at different depths within the alloy during creep under different temperature loads in vacuum and atmospheric environments, a semi-phenomenological microstructure evolution model is established, and the microstructure geometric parameters are calculated as inputs to the creep constitutive model.

[0009] Step 4, based on the γ′ precipitate volume fraction at different depths obtained in Step 3 With the γ matrix phase channel width W iCombining crystal plasticity theory and comprehensively considering various dislocation strengthening mechanisms in the γ / γ′ two-phase structure, a multi-scale creep deformation prediction framework considering the microstructure evolution is constructed.

[0010] Step 5: Based on the multi-layer geometric model established in Step 1 and the growth kinetic model established in Step 2, combined with the multi-scale creep deformation prediction framework considering microstructure evolution constructed in Step 4, the parameters of the growth kinetic model in Step 2, the semi-phenomenological microstructure evolution model in Step 3, and the creep constitutive model in Step 4 are fitted and calibrated using creep test data in atmospheric and vacuum environments. The creep process is then simulated and calculated on the ABAQUS platform.

[0011] A device for predicting creep deformation of nickel-based single-crystal superalloys under creep-oxidation interaction includes:

[0012] The multi-layer geometric model construction module proposes a multi-layer geometric model that considers the effects of oxidation, based on the microscopic observation results of creep tests in atmospheric and vacuum environments.

[0013] The growth kinetics model construction module establishes a corresponding growth kinetics model by statistically analyzing the thickness of each layer in the multi-layered geometric model inside the sample during the creep oxidation process.

[0014] The microstructure evolution model construction module establishes a semi-phenomenological microstructure evolution model based on the statistical results of microstructure evolution at different depths within the alloy during creep under different temperature loads in vacuum and atmospheric environments. The microstructure geometric parameters are calculated as inputs to the creep constitutive model.

[0015] The multi-scale creep deformation prediction framework construction module, based on the microstructure evolution model, establishes the γ′ precipitate volume fraction at different depths. With the γ matrix phase channel width W i Combining crystal plasticity theory and comprehensively considering various dislocation strengthening mechanisms in the γ / γ′ two-phase structure, a multi-scale creep deformation prediction framework considering the microstructure evolution is constructed.

[0016] The fitting module, based on the multi-layer geometric model established by the multi-layer geometric model establishment module and the growth kinetic model established by the growth kinetic model establishment module, combined with the multi-scale creep deformation prediction framework construction module, constructs a multi-scale creep deformation prediction framework that considers microstructure evolution. It completes the fitting and calibration of parameters of the growth kinetic model, the semi-phenomenological microstructure evolution model, and the creep constitutive model using creep test data in atmospheric and vacuum environments, and realizes the simulation calculation of the creep process on the ABAQUS platform.

[0017] An electronic device includes a memory, a processor, and a computer program stored in the memory and executable on the processor, wherein the processor executes the program to implement the steps of the method for predicting creep deformation of nickel-based single-crystal superalloys under creep-oxidation interaction.

[0018] A non-transitory computer-readable storage medium storing a computer program that, when executed by a processor, implements the steps of the method for predicting creep deformation of nickel-based single-crystal superalloys under creep-oxidation interaction.

[0019] The present invention has the following beneficial effects:

[0020] This invention provides a method for predicting creep deformation of nickel-based single-crystal superalloys under creep-oxidation interaction. Based on the microstructure distribution characteristics of nickel-based single-crystal superalloys after creep tests in vacuum and atmospheric environments, a dynamic growth multilayer geometric model considering the effects of oxidation is established. Based on experimental observation results and combined with physical mechanisms, a creep constitutive model considering the evolution of microstructure is established. This invention develops a method that can predict the creep deformation of alloys under different environments, and can be extended to the performance prediction and life assessment of other environmental corrosion creep problems.

[0021] This invention, based on the microstructure distribution characteristics of nickel-based single-crystal superalloys after creep tests in vacuum and atmospheric environments, establishes a dynamic growth multilayer geometric model considering the influence of oxidation. This reveals the mechanism by which oxidation affects nickel-based single-crystal superalloys, and achieves characterization and modeling of the microstructure distribution with depth in the near-surface region of nickel-based single-crystal superalloys induced by oxidation, as well as the evolution of this distribution over time. Furthermore, based on observations from creep tests in atmospheric and vacuum environments, and considering the dislocation strengthening mechanism driven by microstructure, this invention constructs a multi-scale creep deformation prediction framework and proposes a method for accurately predicting the creep deformation of alloys under different environments (a creep deformation prediction method for nickel-based single-crystal superalloys under creep-oxidation interaction). This method not only fills the gaps in related research fields but can also be extended to the performance prediction and life assessment of other environmental corrosion creep problems. It has good engineering application prospects and promotional value in the refined life management of heavy components in aero-engines and gas turbines. Attached Figure Description

[0022] Figure 1 This is a flowchart illustrating the implementation of the method for predicting creep deformation of nickel-based single-crystal superalloys under creep-oxidation interaction according to the present invention.

[0023] Figure 2 This is a schematic diagram of a multilayer geometric model for characterizing the depth distribution characteristics of microstructures under oxidation, as presented in this invention.

[0024] Figure 3This is a schematic diagram of a quarter-finite element model of the creep hollow circular tube specimen of the present invention. Detailed Implementation

[0025] To make the objectives, technical solutions, and advantages of this invention clearer, the invention will be further described in detail below with reference to the accompanying drawings and embodiments. It should be understood that the specific embodiments described herein are merely illustrative and not intended to limit the invention. Furthermore, the technical features involved in the various embodiments of this invention described below can be combined with each other as long as they do not conflict with each other.

[0026] like Figure 1 As shown, the specific implementation steps of this invention are as follows:

[0027] Step 1: Based on the microscopic observation results of creep tests in atmospheric and vacuum environments, a multi-layer geometric model considering the effects of oxidation is proposed.

[0028] like Figure 2 As shown, for atmospheric environment samples, the outer layer of the sample is exposed to air. Due to oxidation, an oxide layer forms on the outer surface of the sample. The multilayer geometric model includes a γ′ phase depletion layer, a γ′ phase reduction layer, and an intermediate region, which are sequentially formed adjacent to the oxide layer in the direction perpendicular to the external stress (sample thickness direction). For atmospheric environment samples, the multilayer geometric model is symmetrical about the intermediate surface (i.e., the symmetry plane, the contact surface between the two intermediate regions of the multilayer geometric model) in the sample thickness direction (hollow circular tube sample, both inner and outer surfaces are exposed to the atmosphere). For vacuum environment samples, since there is no oxidation, there is no oxide layer, γ′ phase depletion layer, or γ′ phase reduction layer. The entire sample can be considered as an intermediate region. Vacuum environment samples can be considered a special case of atmospheric environment samples (i.e., the thickness of all layers except the intermediate layer is 0).

[0029] Total thickness of atmospheric environmental sample It can be viewed as the sum of the thicknesses of different layers:

[0030] ;

[0031] In the formula, , , and The thicknesses are respectively the oxide layer, the γ′ phase depletion layer, the γ′ phase reduction layer, and the intermediate region.

[0032] Step 2: During the creep oxidation process, the thickness of each layer of the multi-layered geometric model inside the sample changes with time. By statistically analyzing the thickness of each layer at different times, a corresponding growth kinetic model is established.

[0033] Default total thickness constant, and Because the oxidation process is ongoing and changes occur, the data needs to be obtained by fitting the measured values. The transition region is defined as 50 μm. Then it can be derived from The definition of calculation.

[0034] Oxide layer thickness It is generally considered to be related to time Power law:

[0035] ;

[0036] The parabolic velocity constant It conforms to the Arrhenius equation:

[0037] ;

[0038] In the formula, For material constants, The activation energy for oxidation. Let be the ideal gas constant. For temperature.

[0039] Studies have shown that the thickness of the γ′ phase depletion layer increases logarithmically with time.

[0040] ;

[0041] In the formula, These are temperature-dependent material constants.

[0042] The experimental data points used for fitting were from different temperature and stress conditions. The results show that the growth law of oxide layer and γ′ phase depletion layer thickness is only related to temperature and not to stress. Experimental data points under the same temperature but different stresses can be described by the same fitting curve.

[0043] Step 3: Based on the statistical results of the microstructure evolution at different depths within the alloy during creep under different temperature loads in vacuum and atmospheric environments, a semi-phenomenological microstructure evolution model is established, and the microstructure geometric parameters (γ′ precipitate phase volume fraction and γ matrix phase channel width) are calculated as inputs to the creep constitutive model.

[0044] The oxide layer contains no γ / γ′ phase, and the γ′ phase-depleted layer contains only the γ phase. Therefore, the volume fraction of the γ′ phase and the width of the γ matrix phase channel in the γ′ phase-depleted layer are set to limit values ​​(which do not represent any physical meaning) to remove their influence in the microstructure evolution model.

[0045] For the γ′ phase reduction layer and the intermediate region, the microstructure evolution behavior is related to both time and depth. For vacuum environment samples, the microstructure evolution behavior of the intermediate region can be considered similar to that of atmospheric environment samples. A semi-phenomenological microstructure evolution model is established by combining experimental patterns and physical mechanisms:

[0046] Volume fraction of γ′ precipitate phase in vacuum and atmospheric environment samples Represented as:

[0047]

[0048]

[0049] In the formula, and It is a material constant. With temperature, depth All are related. It is only related to temperature. It is the initial γ′ phase volume fraction; , , It is a temperature-dependent material constant, in the parameter In the power function fitting equation, As a scale factor, The power exponent, This is a constant term.

[0050] The width of the γ matrix phase channel in the vacuum environment sample is expressed as:

[0051] ;

[0052] In the formula, and Each represents a certain variable At any moment and The possible values ​​of , where, Substitute , , , , General parameters. Variables The width of the γ-matrix phase channel perpendicular to the external loading direction during the rafting process (taking N-type rafting as an example); variable and These are before and after rafting begins. The corresponding value. Variable The length of the periodic cell model is defined as... When a certain value is taken, the width of the γ matrix phase channel ( =1, 2, 3) and the length of the γ′ precipitate phase ( =1, 2, 3). and Here are temperature-dependent material constants, where This is the scale factor in the power function expression. It is a power exponent. It is the internal equivalent stress in the γ phase matrix channel parallel to the (001) crystal plane, which can be obtained by the internal stress analysis method of the cell model.

[0053] The above model parameters , , , , , It is necessary to combine microscopic observation results for fitting. The γ matrix phase channel width of the atmospheric environment sample can be directly derived from the γ′ precipitate phase volume fraction of the atmospheric environment sample and the γ matrix phase channel width of the vacuum environment sample, and can be compared with the experimental observation results as a means of verifying the effectiveness of the model.

[0054] Step 4, based on the γ′ precipitate volume fraction at different depths obtained in Step 3 With γ matrix phase channel width By combining crystal plasticity theory and comprehensively considering various dislocation strengthening mechanisms in the γ / γ′ two-phase structure, a multi-scale creep deformation prediction framework considering the microstructure evolution is constructed.

[0055] Oxide layers are typically considered to lack creep bearing capacity and cannot withstand loads; therefore, their influence is ignored in predictions of creep deformation behavior. Furthermore, the differences between the γ′ phase depletion layer, the γ′ phase reduction layer, and the intermediate region mainly lie in the different γ′ phase volume fractions. To describe the creep deformation behavior of these three types of regions, a creep constitutive model reflecting the microstructure evolution is established. The shear strain on the slip system... for:

[0056] ;

[0057] ;

[0058] ;

[0059] ;

[0060] in, For shear stress, For isotropic hardening stress, and The material constants for the flow law, This is creep damage. External stress, For slip system Orientation factor.

[0061] The resistive stress that hinders dislocation movement, including dislocation hardening stress. Orovan dislocation stress and dislocation-induced shear precipitation response forces . The relative ratio of dislocation bypass to dislocation pair shear is related to stress.

[0062] This represents the creep damage growth rate, and its variation follows a creep damage evolution model. and These are the parameters of the creep damage evolution model.

[0063] Dislocation hardening stress It can be represented as:

[0064] ;

[0065] ;

[0066] In the formula, For dislocation interaction coefficients; and For slip system Dislocation density and cumulative shear strain on the surface (where the dot above the figure indicates the first derivative). These are material parameters used to define the relationship between dislocation hardening stress and dislocation density. It is a material constant characterizing the rate of dislocation density accumulation.

[0067] Orovan dislocation over-stress The calculation method is related to the slip system, and... , , and Taking a slip system as an example, it can be represented as:

[0068] ;

[0069] In the formula, For material constants, Shear modulus For the Bergman vector, , and These represent the matrix channel volumes within the single-crystal alloy that are parallel to the three crystal planes (100), (010), and (001). for , and The sum of; ( , , The material constant that describes the strain inhomogeneity in the corresponding region is related to the rafting state.

[0070] Based on the relative size of the dislocation pair spacing and the precipitate phase, dislocation pairs in shear-precipitated phases can be classified into two categories: weakly coupled dislocation pairs and strongly coupled dislocation pairs. If the diameter of the precipitate phase is smaller than the dislocation pair spacing, it is a weakly coupled dislocation pair; otherwise, it is a strongly coupled dislocation pair. In the multilayer geometric model, for the intermediate region and the γ′ phase reduction layer, the diameter of the γ′ phase is much larger than the dislocation pair spacing, therefore it is a strongly coupled dislocation pair, and the shear stress of the precipitate phase is high. It can be represented as:

[0071] ;

[0072] In the formula, For the antiphase domain boundary energy, For material constants, The equivalent diameter of the γ′ phase.

[0073] In the γ′ phase depletion layer, the γ′ phase is absent, therefore it consists of weakly coupled dislocation pairs, and the precipitated phase shear stress is low. It can be represented as:

[0074] .

[0075] Step 5: Based on the multi-layer geometric model established in Step 1 and the growth kinetic model established in Step 2 (the two combined form a dynamic growth multi-layer geometric model), and combined with the multi-scale creep deformation prediction framework considering microstructure evolution constructed in Step 4, the parameters of the growth kinetic model in Step 2, the semi-phenomenological microstructure evolution model in Step 3, and the creep constitutive model in Step 4 are fitted and calibrated using creep test data in atmospheric and vacuum environments. The creep process is then simulated and calculated on the ABAQUS (commercial finite element software) platform.

[0076] For the parameters of dynamically growing multi-layered geometric models and multi-scale creep deformation prediction frameworks, most can be obtained by fitting creep deformation data under vacuum conditions. The parameters of creep damage evolution models can be obtained from creep life data (creep test data includes creep life data). Some parameters, such as... , and This information needs to be obtained from literature, but it is important to note that the material parameters of the creep constitutive model flow rule for the γ′ phase depleted layer are crucial. and Correction is required using creep test data under atmospheric conditions. A dynamically growing multi-layered geometric model and a multi-scale creep deformation prediction framework are integrated into ABAQUS software via a user-defined UMAT (Material Subroutine). Finite element simulations of the creep process are performed in ABAQUS. Considering computational cost and specimen symmetry, a quarter-finite element model of the creep-induced hollow cylindrical specimen is established, such as... Figure 3 As shown. Symmetrical boundary conditions were applied to the side and bottom surfaces of the quarter-finite element model of the creep hollow cylindrical tube specimen, and a tensile load was applied to the top surface. To account for the evolution of the oxide layer and the γ′ phase depletion layer, the mesh near the surface of the quarter-finite element model of the creep hollow cylindrical tube specimen was refined, as shown. Figure 3 As shown, creep deformation behavior simulation was carried out accordingly.

[0077] Those skilled in the art will understand that embodiments of the present invention can be provided as methods, systems, or computer program products. Therefore, the present invention can take the form of a completely hardware embodiment, a completely software embodiment, or an embodiment combining software and hardware aspects. Furthermore, the present invention can take the form of a computer program product implemented 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. The embodiments of the present invention can be implemented using various computer languages.

[0078] This invention is described with reference to flowchart illustrations and / or block diagrams of methods, apparatus (systems), and computer program products according to embodiments of the invention. 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 illustrations and / or block diagrams. Figure 1 One or more processes and / or boxes Figure 1 A device that provides the functions specified in one or more boxes.

[0079] 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.

[0080] 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.

[0081] Although preferred embodiments of the invention have been described, those skilled in the art, upon learning the basic inventive concept, can make other changes and modifications to these embodiments. Therefore, the appended claims are intended to be interpreted as including both the preferred embodiments and all changes and modifications falling within the scope of the invention.

[0082] Obviously, those skilled in the art can make various modifications and variations to this invention without departing from its spirit and scope. Therefore, if these modifications and variations fall within the scope of the claims of this invention and their equivalents, this invention also intends to include these modifications and variations.

[0083] The above description is merely an embodiment of the present invention and does not limit the scope of the present invention. Any equivalent structural or procedural transformations made based on the content of the present invention specification and drawings, or direct or indirect applications in other related system fields, are similarly included within the protection scope of the present invention.

[0084] The contents not described in detail in this specification are existing technologies known to those skilled in the art.

Claims

1. A method for predicting creep deformation of nickel-based single-crystal superalloys under creep-oxidation interaction, characterized in that, include: Step 1: Based on the microscopic observation results of creep tests in atmospheric and vacuum environments, a multi-layer geometric model considering the effects of oxidation is proposed. Step 2: During the creep oxidation process, the thickness of each layer of the multi-layered geometric model inside the sample changes with time. By statistically analyzing the thickness of each layer at different times, a corresponding growth kinetic model is established. Step 3: Based on the statistical results of the microstructure evolution at different depths within the alloy during creep under different temperature loads in vacuum and atmospheric environments, a semi-phenomenological microstructure evolution model is established, and the microstructure geometric parameters are calculated as inputs to the creep constitutive model. Step 4, based on the γ′ precipitate volume fraction at different depths obtained in Step 3 With the γ matrix phase channel width W i Combining crystal plasticity theory and comprehensively considering various dislocation strengthening mechanisms in the γ / γ′ two-phase structure, a multi-scale creep deformation prediction framework considering the microstructure evolution is constructed. Step 5: Based on the multi-layer geometric model established in Step 1 and the growth kinetic model established in Step 2, combined with the multi-scale creep deformation prediction framework considering microstructure evolution constructed in Step 4, the parameters of the growth kinetic model in Step 2, the semi-phenomenological microstructure evolution model in Step 3, and the creep constitutive model in Step 4 are fitted and calibrated using creep test data in atmospheric and vacuum environments. The creep process is then simulated and calculated on the ABAQUS platform.

2. The method for predicting creep deformation of nickel-based single-crystal superalloys under creep-oxidation interaction according to claim 1, characterized in that, In step 3, the microstructure geometric parameters include the volume fraction of the γ′ precipitate phase and the width of the γ matrix phase channel.

3. The method for predicting creep deformation of nickel-based single-crystal superalloys under creep-oxidation interaction according to claim 2, characterized in that, In step 1, for atmospheric environment samples, the multilayer geometric model includes a γ′ phase depletion layer, a γ′ phase reduction layer, and an intermediate region formed sequentially adjacent to the oxide layer in the sample thickness direction. The multilayer geometric model is symmetrical about the intermediate surface in the sample thickness direction. For vacuum environment samples, the entire sample is regarded as the intermediate region. The intermediate surface is the contact surface between the two intermediate regions of the multilayer geometric model. Total thickness of atmospheric environmental sample The sum of the thicknesses of different layers: ； In the formula, , , and The thicknesses are respectively the oxide layer, the γ′ phase depletion layer, the γ′ phase reduction layer, and the intermediate region.

4. The method for predicting creep deformation of nickel-based single-crystal superalloys under creep-oxidation interaction according to claim 3, characterized in that, Step 2, establishing the corresponding growth kinetic model, includes: default total thickness. constant, and Obtained by fitting measured values The transition region is defined as 50 μm. Depend on Definition and calculation; Oxide layer thickness With time Power law: ； Among them, the parabolic velocity constant It conforms to the Arrhenius equation: ； In the formula, For material constants, The activation energy for oxidation. Let be the ideal gas constant. For temperature; The thickness of the γ′ phase depletion layer increases logarithmically with time. ； In the formula, These are temperature-dependent material constants; The experimental data points used for fitting were from different temperature and stress conditions.

5. The method for predicting creep deformation of nickel-based single-crystal superalloys under creep-oxidation interaction according to claim 4, characterized in that, In step 3, a semi-phenomenological microstructure evolution model is established, and the calculation of microstructure geometric parameters includes: Volume fraction of γ′ precipitate phase in vacuum and atmospheric environment samples Represented as: ； In the formula, and For material constants, With temperature, depth All are related. It is only related to temperature; The initial γ′ phase volume fraction; , , For temperature-dependent material constants, in the parameters In the power function fitting equation, As a scale factor, The power exponent, For constant terms; The width of the γ matrix phase channel in the vacuum environment sample is expressed as: ； in, and Each represents a certain variable At any moment and The possible values ​​of , where, Substitute , , , , General parameters; variables Taking N-type rafting as an example, this refers to the width of the γ-phase matrix channel perpendicular to the external load direction during the rafting process; variable and These are before and after rafting begins. Corresponding value; variable The length of the periodic cell model is defined as... When a certain value is taken, the width of the γ matrix phase channel With γ′ precipitate phase length The sum of, among which, =1, 2, 3; and These are temperature-dependent material constants. This is the scale factor in the power function expression. It is a power exponent; The internal equivalent stress in the γ-phase matrix channel parallel to the (001) crystal plane is obtained by the internal stress analysis method of the cell model.

6. The method for predicting creep deformation of nickel-based single-crystal superalloys under creep-oxidation interaction according to claim 5, characterized in that, Step 4 includes: establishing a creep constitutive model reflecting the evolution of microstructures, and the partial shear strain on the slip system. for: ； ； ； ； in, For shear stress, For isotropic hardening stress, and The material constants for the flow law, This is creep damage. External stress, For slip system Orientation factor; The resistive stress that hinders dislocation movement, including dislocation hardening stress. Orovan dislocation stress and dislocation-induced shear precipitation response forces ; The relative ratio of dislocation bypass to dislocation pair shear is related to stress. This represents the creep damage growth rate, and its variation follows a creep damage evolution model. and These are the parameters for the creep damage evolution model; Dislocation hardening stress Represented as: ； ； In the formula, For dislocation interaction coefficients; and For slip system Dislocation density and cumulative shear strain on the surface; These are material parameters used to define the relationship between dislocation hardening stress and dislocation density. A material constant characterizing the rate of dislocation density accumulation; Orovan dislocation over-stress The calculation method is related to the slip system, and... , , and Taking a slip system as an example, it can be represented as follows: ； In the formula, For material constants, Shear modulus For the Bergman vector, , and These represent the matrix channel volumes within the single-crystal alloy that are parallel to the three crystal planes (100), (010), and (001). for , and The sum of; , , Material constants that describe the strain inhomogeneity in the corresponding region; Based on the relative size of the dislocation pair spacing and the precipitate phase, the dislocation pairs of the shear precipitate phase are divided into two categories: weakly coupled dislocation pairs and strongly coupled dislocation pairs. If the diameter of the precipitate phase is smaller than the dislocation pair spacing, it is a weakly coupled dislocation pair; otherwise, it is a strongly coupled dislocation pair. In the multilayer geometric model, for the intermediate region and the γ′ phase reduction layer, the precipitate phase shear stress Represented as: ； In the formula, For the antiphase domain boundary energy, For material constants, The equivalent diameter of the γ′ phase; In the γ′ phase depletion layer, the precipitate phase shear stress Represented as: 。 7. The method for predicting creep deformation of nickel-based single-crystal superalloys under creep-oxidation interaction according to claim 6, characterized in that, The multi-layer geometric model established in step 1, the growth kinetic model established in step 2, and the multi-scale creep deformation prediction framework constructed in step 4 are integrated into the ABAQUS software through the user-defined UMAT. Finite element simulation of the creep process is performed in ABAQUS. A quarter-finite element model of the creep hollow tube specimen is established. Symmetrical boundary conditions are applied to the side and lower surfaces of the quarter-finite element model of the creep hollow tube specimen, and tensile load is applied to the upper surface. The mesh near the surface of the quarter-finite element model of the creep hollow tube specimen is refined. Based on this, the creep deformation behavior is simulated.

8. A device for predicting creep deformation of nickel-based single-crystal superalloys under creep-oxidation interaction, characterized in that, include: The multi-layer geometric model construction module proposes a multi-layer geometric model that considers the effects of oxidation, based on the microscopic observation results of creep tests in atmospheric and vacuum environments. The growth kinetics model construction module establishes a corresponding growth kinetics model by statistically analyzing the thickness of each layer in the multi-layered geometric model inside the sample during the creep oxidation process. The microstructure evolution model construction module establishes a semi-phenomenological microstructure evolution model based on the statistical results of microstructure evolution at different depths within the alloy during creep under different temperature loads in vacuum and atmospheric environments. The microstructure geometric parameters are calculated as inputs to the creep constitutive model. The multi-scale creep deformation prediction framework construction module, based on the microstructure evolution model, establishes the γ′ precipitate volume fraction at different depths. With the γ matrix phase channel width W i Combining crystal plasticity theory and comprehensively considering various dislocation strengthening mechanisms in the γ / γ′ two-phase structure, a multi-scale creep deformation prediction framework considering the microstructure evolution is constructed. The fitting module, based on the multi-layer geometric model established by the multi-layer geometric model establishment module and the growth kinetic model established by the growth kinetic model establishment module, combined with the multi-scale creep deformation prediction framework construction module, constructs a multi-scale creep deformation prediction framework that considers microstructure evolution. It completes the fitting and calibration of parameters of the growth kinetic model, the semi-phenomenological microstructure evolution model, and the creep constitutive model using creep test data in atmospheric and vacuum environments, and realizes the simulation calculation of the creep process on the ABAQUS platform.

9. An electronic device comprising a memory, a processor, and a computer program stored in the memory and executable on the processor, characterized in that, When the processor executes the program, it implements the steps of the method for predicting creep deformation of nickel-based single-crystal superalloys under creep-oxidation interaction as described in any one of claims 1 to 7.

10. A non-transitory computer-readable storage medium having a computer program stored thereon, characterized in that, When executed by a processor, the computer program implements the steps of the method for predicting creep deformation of nickel-based single-crystal superalloys under creep-oxidation interaction as described in any one of claims 1 to 7.

Images