Composite board with multi-layer heterogeneous interface and preparation method thereof

Abstract

The invention belongs to a preparation method of a metal composite plate, and provides a composite plate with a multi-layer heterogeneous interface and a preparation method of the composite plate in order to solve the problems that according to an existing method for introducing heterogeneous distribution into a metal material, introduction is limited to partial areas of the surface layer of the material, cost is high, and the introduction form is single. And a multi-layer heterogeneous structure with component gradient isomerism, grain size isomerism and macroscopic performance isomerism is formed at the interface of the low-alloy element alloy plate and the corresponding aging strengthening type high-alloy element alloy composite plate and in adjacent areas on the two sides of the low-alloy element alloy plate and the corresponding aging strengthening type high-alloy element alloy composite plate. The obtained initial composite plate is heated, solute atoms are promoted to diffuse towards a low-alloy-element alloy plate area under the driving effect of a large concentration gradient near an interface, component gradient isomerism is directly formed, then the composite plate is subjected to cold deformation in the welding direction, high-temperature recrystallization heat treatment is conducted, and the composite plate is obtained. And the pinning effects of the solute atoms distributed according to the gradient on the crystal grains are also differently distributed in space, so that the crystal grain size isomerism is formed.

Description

Technical Field

[0001] The present application relates to a method for preparing a metal composite plate, and specifically to a composite plate with a multi-layered heterogeneous interface and a method for preparing the same. Background Art

[0002] Introducing heterogeneity inside metal materials makes the material strength differently distributed in space, thus forming inconsistent plastic strains and generating geometrically required dislocations during deformation, which helps to coordinate and improve the inverted relationship between strength and plasticity, and has great inspiration and application potential for future material design. Common methods for introducing heterogeneous distribution include surface deformation technology, torsion technology, and electrodeposition technology, which are usually limited to some areas of the material surface, have high cost, and can only introduce a single form of heterogeneity. Summary of the invention

[0003] The present application aims to provide a composite plate with a multi-level heterogeneous interface and a preparation method thereof in view of the technical problems that the introduction is limited to a part of the surface area of ​​the material, the cost is high, and the introduction form is single.

[0004] In order to achieve the above objectives, this application adopts the following technical solutions: In a first aspect, the present application proposes a method for preparing a composite plate having a multi-level heterogeneous interface, comprising: At least one first alloy plate and at least one second alloy plate are used as welding parent materials, and an explosion welding method is used for welding to obtain an initial composite plate; wherein the first alloy plate and the second alloy plate are arranged alternately; and the alloy element content of the first alloy plate is less than the alloy element content of the second alloy plate; heat-treating the composite plate to obtain a heat-treated plate; Cold deforming the heat-treated plate along the explosion welding direction to obtain a cold-deformed plate; Performing recrystallization annealing treatment on the cold deformed plate to obtain a recrystallized annealed plate; The annealed plate is subjected to thermomechanical treatment to obtain a composite plate with a multi-layered heterogeneous interface.

[0005] Furthermore, the composite plate is subjected to heat treatment, comprising: The temperature of the heat treatment is within the solution temperature range of the first alloy plate and the second alloy plate.

[0006] Further, the temperature of heat treatment is determined according to ASM Handbook Volume 4 Heat Treatment.

[0007] Furthermore, the heat treatment time is 1-2h.

[0008] Furthermore, the deformation amount of the cold-deformed plate is 0-80%.

[0009] Further, the cold deformed plate is subjected to a recrystallization annealing treatment, comprising: The temperature of the annealing treatment is higher than the recrystallization temperature of the first alloy plate and the second alloy plate.

[0010] Furthermore, the temperature of the annealing treatment is determined according to ASM Handbook Volume 4 Heat Treatment.

[0011] Furthermore, the annealing time is 1-2 hours.

[0012] Furthermore, the annealed sheet is subjected to thermomechanical treatment, including deformation treatment and aging treatment.

[0013] Furthermore, the deformation temperature and deformation amount of the deformation treatment are matched; and the aging temperature and aging time of the aging treatment are determined according to ASM Handbook Volume 4 Heat Treatment.

[0014] Furthermore, the first alloy plate is a pure metal plate, and the second alloy plate is a metal plate containing alloy elements; the content of the alloy elements in the second alloy plate is equal to the content of the alloy elements in any aging-hardened alloy with the same base material; Furthermore, the first alloy plate is a metal plate containing alloying elements, and the second alloy plate is a metal plate containing alloying elements; the content of alloying elements in the first alloy plate is lower than the content of alloying elements in any aging-hardened alloy with the same matrix material; the content of alloying elements in the second alloy plate is higher than the content of alloying elements in the aforementioned aging-hardened alloy, so that the main precipitate phase forming elements can be completely dissolved back into the matrix during annealing treatment, and the second phase can be precipitated during aging treatment.

[0015] In a second aspect, the present application proposes a composite plate having a multi-level heterogeneous interface, which is prepared by using the above-mentioned method for preparing a composite plate having a multi-level heterogeneous interface.

[0016] Compared with the prior art, this application has the following beneficial effects: The present application proposes a method for preparing a composite plate with a multi-level heterogeneous interface, using two alloy plates with different alloy element contents as welding parent materials, and adopting an explosive welding method for welding. The explosive welding composite technology can use the energy released instantly by high-energy explosives to achieve metallurgical bonding of metal materials, and retain the parent material properties to a large extent, so that there is almost no heat-affected zone at the interface. Multiple plates of the same system and different types are welded into a multi-layer primary heterogeneous composite plate by the explosive welding method. Then, heat treatment, cold deformation, annealing treatment and thermomechanical treatment are carried out in sequence to finally obtain a composite plate with a multi-level heterogeneous interface. Through the regulation of subsequent thermomechanical treatment parameters, solute atoms can diffuse under the drive of concentration gradient, and composition gradient isomerism can be formed at the same time, and multi-level isomerism with grain size isomerism and macroscopic mechanical property isomerism can be obtained.

[0017] The present application also proposes a composite plate prepared by the above-mentioned method for preparing a composite plate with a multi-level heterogeneous interface, which has all the advantages of the above-mentioned method for preparing a composite plate with a multi-level heterogeneous interface. BRIEF DESCRIPTION OF THE DRAWINGS

[0018] In order to more clearly illustrate the technical solutions of the embodiments of the present application, the drawings required for use in the embodiments will be briefly introduced below. It should be understood that the following drawings only show certain embodiments of the present application and therefore should not be regarded as limiting the scope. For ordinary technicians in this field, other related drawings can be obtained based on these drawings without creative work.

[0019] Figure 1 A schematic diagram of a process for preparing a composite plate with a multi-layered heterogeneous interface according to the present application; Figure 2 Schematic diagram of the processing process using three-layer composite plates (the upper and lower outer layers are the second alloy plates, and the middle layer is the first alloy plate). DETAILED DESCRIPTION

[0020] In order to make the purpose, technical solution and advantages of the embodiments of the present application clearer, the technical solution in the embodiments of the present application will be clearly and completely described below in conjunction with the drawings in the embodiments of the present application. Obviously, the described embodiments are part of the embodiments of the present application, rather than all the embodiments. The components of the embodiments of the present application described and shown in the drawings here can be arranged and designed in various different configurations.

[0021] Therefore, the following detailed description of the embodiments of the present application provided in the accompanying drawings is not intended to limit the scope of the present application for which protection is sought, but merely represents selected embodiments of the present application. Based on the embodiments in the present application, all other embodiments obtained by ordinary technicians in the field without creative work are within the scope of protection of the present application.

[0022] It should be noted that similar reference numerals and letters denote similar items in the following drawings, and therefore, once an item is defined in one drawing, further definition and explanation thereof is not required in subsequent drawings.

[0023] In the description of the embodiments of the present application, it should be noted that if the terms "upper", "lower", "horizontal", "inner", etc. appear, the orientation or position relationship indicated is based on the orientation or position relationship shown in the drawings, or the orientation or position relationship in which the invented product is usually placed when used. It is only for the convenience of describing the present application and simplifying the description, and does not indicate or imply that the device or element referred to must have a specific orientation, be constructed and operated in a specific orientation, and therefore cannot be understood as a limitation on the present application. In addition, the terms "first", "second", etc. are only used to distinguish the description, and cannot be understood as indicating or implying relative importance.

[0024] In addition, if the term "horizontal" appears, it does not mean that the component must be absolutely horizontal, but can be slightly tilted. For example, "horizontal" only means that its direction is more horizontal than "vertical", which does not mean that the structure must be completely horizontal, but can be slightly tilted.

[0025] In the description of the embodiments of the present application, it is also necessary to explain that, unless otherwise clearly specified and limited, the terms "set", "install", "connect", and "connect" should be understood in a broad sense. For example, it can be a fixed connection, a detachable connection, or an integral connection; it can be a mechanical connection or an electrical connection; it can be a direct connection, or it can be indirectly connected through an intermediate medium, or it can be the internal connection of two components. For ordinary technicians in this field, the specific meanings of the above terms in this application can be understood according to specific circumstances.

[0026] Heterogeneous metals refer to microstructure units with large strength differences inside the material. These microstructure units may have differences in strength (soft and hard) due to differences in grain size, crystal structure or material composition. Due to the difference in strength in space, during the deformation of the material, there will be great strain inconsistency between these soft-hard units. Therefore, a large back stress will be generated between the soft-hard unit domains (back stress refers to the interaction force generated by the inconsistent deformation of the soft-hard units inside the material during the deformation process). In general, soft units provide deformation and hard units provide strength. Heterogeneous metals benefit from the strengthening / hardening effect of this back stress, which enables the material to have both high strength and high plasticity, thereby achieving a perfect match between strength and plasticity.

[0027] At present, the method of introducing heterogeneous distribution by applying deformation on the surface of the material is usually limited to some areas of the surface layer of the material, and it is difficult to affect the overall performance of the material. The method of introducing heterogeneous distribution by twisting the material is usually limited to some areas of the surface layer of the material, and has certain requirements on the shape and size of the material. In addition, the method of introducing heterogeneous distribution by forming a coating with different properties on the surface of the material through the electrodeposition process is costly, and there may be problems with the bonding strength between the coating and the substrate. These complex processing methods are either limited to small-scale laboratory research or can only produce heterostructure samples on the micron scale, and it is difficult or impossible to achieve large-scale heterostructure alloys in large-scale commercial production.

[0028] Based on the above situation, it is necessary to develop a method that can introduce large-scale, deep-thickness, multi-level gradient heterogeneity using only a simple processing process. Therefore, the present application proposes a composite plate with a multi-level heterogeneous interface and a preparation method thereof, which is described in detail below in conjunction with the embodiments and drawings.

[0029] like Figure 1 As shown, it is a first schematic flow chart of a method for preparing a composite plate with a multi-level heterogeneous interface of the present application, which may include: S101, using at least one first alloy plate and at least one second alloy plate as welding parent materials, and performing explosion welding to obtain an initial composite plate; wherein the first alloy plates and the second alloy plates are alternately arranged; and the alloy element content of the first alloy plate is less than the alloy element content of the second alloy plate.

[0030] This application uses at least one first alloy plate and at least one second alloy plate as welding parent materials, and realizes a multi-level heterogeneous interface of the composite plate through a combination of different alloy elements. It should be noted that explosion welding is a method of using the energy generated by the explosion of explosives to make two or more metal plates reach high-speed collision in a very short time, thereby realizing welding. This method can form high-quality welded joints and is suitable for a combination of various metal materials. The obtained initial composite plate has a multi-level heterogeneous interface, which provides a basis for subsequent processing and treatment.

[0031] S102, heat-treating the composite plate to obtain a heat-treated plate.

[0032] Heat treatment of the initial composite plate can eliminate the stress and defects generated during the explosive welding process, improve the structure and performance of the material, and promote the diffusion of solute atoms from the high-alloy element plate to the low-alloy element plate. In practical applications, the heat treatment process may include steps such as heating, insulation, and cooling. Specific heat treatment parameters, such as temperature, time, cooling rate, etc., can be determined according to the material composition and performance requirements of the composite plate. The heat-treated plate obtained after heat treatment has its stress and defects eliminated, and its structure and performance have also been improved. At the interface, a composition gradient is formed due to the diffusion of solute driven by the concentration difference.

[0033] S103, cold deforming the heat-treated plate along the explosion welding direction to obtain a cold-deformed plate.

[0034] Cold deformation of the heat-treated plate along the explosive welding direction aims to further improve the structure and properties of the material through plastic deformation, introduce deformation distortion energy to prepare for subsequent recrystallization annealing treatment, and may form more heterogeneous interfaces. Cold deformation can be carried out by cold rolling, cold forging or cold heading rolling, and parameters such as deformation amount and deformation rate can also be controlled to ensure the deformation effect. After cold deformation, the structure and properties of the cold-deformed plate are further improved, a large amount of elastic distortion energy is stored inside the grains, and more heterogeneous interfaces may be formed.

[0035] S104, performing recrystallization annealing treatment on the cold deformed sheet to obtain a recrystallized annealed sheet.

[0036] Recrystallization annealing of cold-deformed plates can eliminate stress and defects generated during cold deformation, while restoring the plasticity and toughness of the material, and changing the structure from deformed grains to new equiaxed grains. In practical applications, annealing can be carried out using steps such as heating, heat preservation and cooling. Specific annealing parameters can be determined based on the composition and performance requirements of the material.

[0037] S105, performing thermomechanical treatment on the annealed plate to obtain a composite plate with a multi-layered heterogeneous interface.

[0038] Thermomechanical treatment of the annealed sheet can further improve the organization and performance of the material through the combined action of heating and mechanical deformation, and form a stable multi-level heterogeneous interface. The specific thermomechanical treatment parameters can be determined according to the composition and performance requirements of the material.

[0039] In the present application, a multi-level heterogeneous structure is formed near the interface area of ​​the composite plate through a heat treatment and a recrystallization annealing heat treatment process after cold deformation of the welded composite plate, which mainly includes the following three types of isomerism: (1) controlled by the heat environment and the solute concentration gradient, the solute atoms spontaneously diffuse from the second alloy plate area with a high alloy element content to the first alloy plate area with a low alloy element content, forming a chemical composition gradient isomerism within a certain depth; (2) after cold deformation and recrystallization annealing heat treatment, the grain size isomerism is formed under the influence of the solute atom distribution; (3) due to the combined effect of the chemical composition gradient isomerism and the grain size isomerism, the macroscopic mechanical property isomerism is formed.

[0040] The preparation method of the present application is described in more detail below through other embodiments of the method for preparing a composite plate with a multi-level heterogeneous interface of the present application.

[0041] In some embodiments of the present application, the heat treatment of the composite plate is carried out within the solution temperature range of the alloy plate, and the time is determined according to ASM Handbook volume 4 Heat Treatment, and the time is 1-2 h. Among them, the solution treatment is a heat treatment process in which the alloy is heated to a high temperature single-phase region and maintained at a constant temperature, so that the excess phase is fully dissolved into the solid solution and then rapidly cooled. The solution temperature range is usually high and is suitable for occasions where a supersaturated solid solution is required. The purpose in the embodiments of the present application is to promote the diffusion of solute atoms at the interface. In authoritative materials such as ASM Handbook volume 4 Heat Treatment, the recommended solution time ranges for different materials at different solution temperatures are given.

[0042] In some embodiments of the present application, cold deformation can be performed by cold rolling, cold forging or cold heading. Among them, cold rolling is the process of rolling metal materials at room temperature, which can improve the hardness and strength of the material while maintaining good surface quality and dimensional accuracy. Cold forging is the process of applying external force to a metal material at room temperature or near room temperature to cause it to undergo plastic deformation to achieve the desired shape and size. Cold forging can improve the mechanical properties and surface quality of the material while reducing material consumption and processing costs. Cold heading is the process of cold extruding a metal material using a mold to cause its head to undergo plastic deformation to form the desired shape. Heading is mainly used to produce various fasteners, such as bolts, screws, etc., and has the advantages of high production efficiency, high material utilization rate and good product quality. Cold deformation introduces crystal defects such as dislocations through plastic deformation, thereby further adjusting the microstructure of the material, improving the mechanical properties of the material or achieving specific physical properties. In some embodiments of the present application, the deformation amount of cold deformation is 0-80%, and the purpose is to introduce elastic deformation energy inside the grains. When determining the deformation amount, the characteristics of the material, the microstructure of the heat-treated plate, and the final required material properties can be considered.

[0043] In some embodiments of the present application, the recrystallization annealing treatment of the composite plate is above the recrystallization temperature of the alloy plate, and the time is determined according to ASM Handbook volume 4 Heat Treatment, and the time is 1-2 h. Among them, the recrystallization annealing treatment is a process in which the alloy is heated to a certain temperature, the material work hardening is completely eliminated, the performance is restored to the annealing state before deformation, and the microstructure is changed from elongated deformed grains to new equiaxed grains. In authoritative materials such as ASM Handbook volume 4 Heat Treatment, the recommended annealing time range for different materials at different recrystallization annealing temperatures is given.

[0044] It should be noted that ASM Handbook Volume 4: Heat Treating is one of the best reference guides on heat treatment, covering many aspects such as heat treatment and surface hardening of steel, heat treatment equipment, processes and quality control.

[0045] In some embodiments of the present application, the thermomechanical treatment includes a deformation and aging process, wherein the deformation temperature and the deformation amount are matched so that the composite plate does not recrystallize, and the different solute atoms dissolved in the alloy plate are combined in a certain proportion to form a second phase and precipitate by aging, and the aging temperature and time are determined according to ASM Handbook volume 4 Heat Treatment. By controlling parameters such as deformation temperature, deformation amount, aging temperature and time, the microstructure and performance of the material are optimized. In thermomechanical treatment, the matching of deformation temperature and deformation amount is crucial. For the composite plate, the goal is to prevent recrystallization during the deformation process, promote the aging precipitation of the second phase, and achieve the aging strengthening effect. Generally, the deformation temperature should be selected below the recrystallization temperature of the material. However, the specific deformation temperature can also be determined according to the type of material, alloy composition and required performance. Deforming at a lower temperature helps to inhibit the occurrence of recrystallization, but it may also increase the difficulty and energy consumption of deformation. The size of the deformation amount also affects the occurrence of recrystallization. Generally speaking, a larger deformation amount helps to introduce more dislocations and substructures, but it may also increase the residual stress and work hardening degree of the material. Aging treatment is another key step in thermomechanical treatment. Heating is used to rearrange and combine the dislocations and substructures generated during the deformation process, thereby further optimizing the microstructure and properties of the material. The solute atoms precipitate in proportion as the second phase dispersed distribution, which can greatly improve the strength of the material. The selection of aging temperature should be determined according to the type of material, alloy composition and required performance. In authoritative materials such as ASM Handbook volume 4 Heat Treatment, performance change curves or data tables of different materials at different aging temperatures may be given for reference by researchers and engineers. The length of aging time will also affect the final performance of the material. Generally speaking, a longer aging time is conducive to the full precipitation of solid solution atoms, but it may also cause the precipitated second phase to coarsen, thereby reducing the strength of the material.

[0046] When making a selection between the first alloy plate and the second alloy plate, the following solutions may be specifically adopted: When the first alloy plate is a pure metal plate, the second alloy plate can be any aging-strengthening alloy with the same matrix material. Age-strengthening alloys refer to alloys that can significantly improve mechanical properties such as strength and hardness through aging treatment (i.e., keeping warm at a certain temperature for a period of time). Alternatively, the first alloy plate is a metal plate containing alloy elements, and the second alloy plate is a metal plate containing alloy elements. The content of alloy elements in the first alloy plate is lower than the content of alloy elements in any aging-strengthening alloy with the same matrix material, and the content of alloy elements in the second alloy plate is higher than the content of alloy elements in the aforementioned aging-strengthening alloy, so that the main precipitation phase forming elements can be completely dissolved back into the matrix during annealing treatment, and the second phase can be precipitated during aging treatment. The main precipitation phase forming elements refer to elements that can form a strengthening phase in the alloy. These elements will precipitate and form a second phase during the aging treatment, thereby enhancing the performance of the alloy. The content of each main precipitation phase forming element in the second alloy plate should ensure that it can be completely dissolved back into the matrix during annealing, and can be re-precipitated to form a second phase during aging treatment. This is also to optimize the microstructure and performance of the alloy, and ensure that good interface bonding and overall performance can be obtained during the preparation of the composite plate. In practical applications, low-alloy element alloy plates and solid solution aging-strengthened high-alloy element alloy plates with slightly excessive solute atoms added to the metal can be used as parent materials, and the welding window can be theoretically calculated and explosive welding parameters can be designed to implement welding and composite to obtain composite plates.

[0047] It should also be noted that the number of layers of the composite board can be adjusted according to actual needs, for example, the number of layers of the composite board is not less than three. The multi-layer structure can bring better comprehensive performance, such as better uniformity, higher strength, better toughness, etc.

[0048] Macroscopically, the first alloy plate and the second alloy plate constituting the composite plate, as two initial parent materials, have a wide range of composition and thickness selection, and the structure (such as the number of layers, etc.) can be designed, forming the basis of the heterogeneous hierarchy of the composite plate. For example, adjacent plates can be a combination of single metals and age-hardened alloys of the same system (such as pure copper and Cu-Ni-Si alloy), or alloys of the same type but different alloying element contents (such as Cu-Ni-Si alloys with the same ratio of Ni and Si elements but different contents), or alloys with the same or different main precipitate phase-forming elements but different other micro-alloying elements. For example, in Cu-Ni-Si and Cu-Ni-Si-Cr alloys, the main precipitate phase forming elements Ni and Si in the two alloys can be the same, or compared with Cu-Ni-Si alloy, the ratio of Ni and Si in Cu-Ni-Si-Cr alloy is the same but the content is higher, but the content of microalloying element Cr is different, the content of Ni and Si is higher, and Cr and Si form Cr3Si phase, which can prevent the coarsening of the intralayer structure at high temperature. This high-temperature structure stability caused by different microalloying element contents is also common in aluminum alloys, such as aluminum alloys containing Sc. Due to the differences in the content and type of alloying elements in the parent materials, the above combinations will show different response behaviors such as structure coarsening rate (affected by the concentration and type of solid solution elements and microstructure), chemical potential of alloying elements (affecting the diffusion rate of elements) and corresponding mechanical properties during thermomechanical treatment. At the microscopic level, the aforementioned differentiated response behavior can be utilized through thermomechanical treatment processes such as deformation and heat treatment to promote the formation of gradient isomerism of chemical composition, grain size and mechanical properties in the interface region, and regulating the high-temperature heat treatment time can effectively control the gradient depth of the interface region, and can achieve the above-mentioned multi-level heterogeneous design only through the composition design and distribution of the two parent materials when the overall composition of the composite plate is the same as that of a single target alloy. Under the condition of the basic heterogeneity of the composite plate, the cold deformation is unevenly distributed inside it. When the cold deformation heating treatment is continued, the above-mentioned gradient structure in the interface region will accelerate the formation and deepening under the coupling promotion of the composition, strain and organizational gradient of the previous structure. The preparation method of the present application can not increase the cost of raw materials, but the multi-level macro-micro multi-level heterogeneous system formed helps the composite plate to obtain more comprehensive comprehensive performance.

[0049] In addition, this application selects a pure metal plate without solute atoms or a low-alloy element alloy plate containing only a small amount of solute, and uses the metal as a matrix to add a corresponding aging-strengthening alloy plate with an appropriate ratio of solute atoms as a carrier, and uses explosive welding technology to achieve direct composite, which can retain the inherent characteristics of the parent material to the greatest extent, forming an interface with a clear difference in chemical composition, and providing a good platform for subsequent regulation and treatment. On the one hand, the parameters of the heat treatment temperature and duration of the welded composite plate material are scientifically designed, and the solute atom ratio of the aging-strengthening alloy is modified to make it slightly excessive to the typical composition ratio, where the increment of specific atoms can be adjusted as needed according to the difference in their diffusion coefficients, so that the diffusion depth of solute atoms into the pure metal area can be controlled, thereby forming a composition gradient heterogeneous layer on both sides of the interface. On the other hand, the composite plate can be subjected to a certain degree of cold deformation along the welding direction, so that the welding interface is extended and bridged and a large amount of distortion energy is stored in the matrix plate, and then recrystallization annealing treatment is performed to cause the matrix plates on both sides to recrystallize. Under the same deformation degree, heating temperature and time, the presence of solute atoms pins the grain boundary and affects the movement of the grain boundary, thereby hindering the growth of recrystallized grains. The composition heterogeneous layer area on both sides of the interface will form a heterogeneous distribution due to the gradient distribution of the solute atoms contained. The chemical composition gradient layer and the grain size heterogeneous layer formed on both sides of the interface will have a significant impact on the mechanical properties of the material, that is, they also constitute a macroscopic mechanical property heterogeneous region. In summary, in fact, a multi-level heterogeneous effect of composition gradient, grain size heterogeneity and macroscopic mechanical property heterogeneity can be achieved in the interface area of ​​the low-alloy element alloy plate and its corresponding aging-strengthened alloy plate. This heterogeneous distribution feature can improve the mechanical properties of the interface area of ​​the composite plate, and its excellent back stress strengthening ability helps to coordinate the simultaneous improvement of the strength and plasticity of the composite plate material.

[0050] like Figure 2 The figure shows a schematic diagram of the treatment process using a three-layer composite plate (the upper and lower outer layers are the second alloy plate, and the middle is the first alloy plate). Among them, (a) represents the placed first alloy plate and the second alloy plate, and the two alloy plates with different compositions are placed alternately; (b) represents the initial composite plate after explosive welding, and the three-layer plate is welded and composited twice from bottom to top to obtain a composite plate with good interface bonding; (c) represents the heat-treated plate after heat treatment, under the combined action of the concentration difference at the interface of the first and second alloy plates and heating, the solute atoms diffuse from the high alloy plate to the low alloy plate, thereby forming a composition gradient at the interface; (d) represents the cold-deformed plate after cold deformation, and the distortion energy is stored inside the composite plate through cold deformation; (e) represents the recrystallization annealed plate after recrystallization annealing treatment, and the grain size of the composite plate shows an obvious gradient distribution due to the gradient distribution of the solute concentration.

[0051] The present application also proposes a composite plate with a multi-level heterogeneous interface, which is prepared by using the above-mentioned method for preparing a composite plate with a multi-level heterogeneous interface.

[0052] It should be noted that the composite board with multi-level heterogeneous interfaces of the present application can adopt the relevant embodiments of the method for preparing a composite board with multi-level heterogeneous interfaces, which will not be described in detail here.

[0053] The above are only preferred embodiments of the present application and are not intended to limit the present application. For those skilled in the art, the present application may have various modifications and variations. Any modification, equivalent replacement, improvement, etc. made within the spirit and principle of the present application shall be included in the protection scope of the present application.

Claims

1. A method for preparing a composite plate with a multi-level heterogeneous interface, characterized in that: include: At least one first alloy plate and at least one second alloy plate are used as welding parent materials, and an explosion welding method is used for welding to obtain an initial composite plate; wherein the first alloy plate and the second alloy plate are arranged alternately; and the alloy element content of the first alloy plate is less than the alloy element content of the second alloy plate; heat-treating the composite plate to obtain a heat-treated plate; Cold deforming the heat-treated plate along the explosion welding direction to obtain a cold-deformed plate; Performing recrystallization annealing treatment on the cold deformed plate to obtain a recrystallized annealed plate; The annealed plate is subjected to thermomechanical treatment to obtain a composite plate with a multi-layered heterogeneous interface.

2. The method for preparing a composite plate having a multi-level heterogeneous interface according to claim 1, characterized in that: The temperature of heat treatment on the composite plate is within the solid solution temperature range of the first alloy plate and the second alloy plate.

3. The method for preparing a composite plate having a multi-level heterogeneous interface according to claim 1, characterized in that: The temperature of heat treatment was determined according to ASM Handbook Volume 4 Heat Treatment; The heat treatment time is 1-2 h.

4. The method for preparing a composite plate having a multi-level heterogeneous interface according to claim 1, characterized in that: The deformation amount of the cold-deformed plate is 0-80%.

5. The method for preparing a composite plate having a multi-layered heterogeneous interface according to claim 1, characterized in that: The cold deformed plate is subjected to a recrystallization annealing treatment, comprising: The temperature of the recrystallization annealing treatment is higher than the recrystallization temperature of the first alloy plate and the second alloy plate.

6. The method for preparing a composite plate having a multi-layered heterogeneous interface according to claim 1, characterized in that: The temperature of annealing treatment was determined according to ASM Handbook Volume 4 Heat Treatment; The annealing time is 1-2h.

7. The method for preparing a composite plate having a multi-layer heterogeneous interface according to claim 1, characterized in that: The annealed sheet is subjected to thermomechanical treatment, including deformation treatment and aging treatment.

8. The method for preparing a composite plate having a multi-layered heterogeneous interface according to claim 7, characterized in that: The deformation temperature and deformation amount of the deformation treatment are matched; the aging temperature and aging time of the aging treatment are determined according to ASM Handbook Volume 4 Heat Treatment.

9. The method for preparing a composite plate having a multi-layered heterogeneous interface according to claim 8, characterized in that: The first alloy plate is a pure metal plate, and the second alloy plate is a metal plate containing alloy elements; the content of the alloy elements in the second alloy plate is equal to the content of the alloy elements in any aging-hardened alloy with the same base material; Alternatively, the first alloy plate is a metal plate containing alloying elements, and the second alloy plate is a metal plate containing alloying elements; the content of alloying elements in the first alloy plate is lower than the content of alloying elements in any aging-hardened alloy with the same matrix material; the content of alloying elements in the second alloy plate is higher than the content of alloying elements in the aforementioned aging-hardened alloy, so that the main precipitate phase forming elements can be completely dissolved back into the matrix during annealing treatment, and the second phase can be precipitated during aging treatment.

10. A composite plate having a multi-layer heterogeneous interface, characterized in that: The composite plate having a multi-layered heterogeneous interface is prepared by the method for preparing the composite plate according to any one of claims 1 to 9.

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