Structural member, preparation method thereof and electronic equipment

Abstract

The invention provides a structural component, a preparation method thereof and electronic equipment. The structural part of the embodiment of the invention comprises an ultra-high-strength part, a first reinforcing part and a second reinforcing part, wherein the ultra-high-strength part is made of first ultra-high-strength steel; the ultra-high-strength part is connected with the base, the abrasion-resistant part is connected with the ultra-high-strength part, the tensile strength of the ultra-high-strength part is larger than that of the abrasion-resistant part, the abrasion resistance of the abrasion-resistant part is larger than that of the ultra-high-strength part, and the tensile bonding strength between the ultra-high-strength part and the abrasion-resistant part is larger than that of the abrasion-resistant part. The structural part disclosed by the invention has relatively high strength and relatively high wear resistance.

Description

Technical Field

[0001] This application relates to the field of electronics, specifically to a structural component, its manufacturing method, and an electronic device. Background Technology

[0002] Ultra-high strength steel has good yield strength and ductility. However, it contains very few or almost no hard phases. Therefore, ultra-high strength steel has poor wear resistance and is difficult to use as structural components with high wear resistance requirements. Summary of the Invention

[0003] This application provides a structural component that has high strength and high wear resistance.

[0004] In a first aspect, embodiments of this application provide a structural component, the structural component comprising:

[0005] The ultra-high strength section, wherein the material of the ultra-high strength section is a first ultra-high strength steel; and

[0006] The wear-resistant part is connected to the ultra-high strength part. The tensile strength of the ultra-high strength part is greater than that of the wear-resistant part. The wear resistance of the wear-resistant part is greater than that of the ultra-high strength part. The tensile bond strength between the ultra-high strength part and the wear-resistant part is greater than that of the wear-resistant part.

[0007] Secondly, embodiments of this application also provide a method for manufacturing a structural component, comprising:

[0008] Provide first alloy steel powder;

[0009] Provide wear-resistant powder or wear-resistant components;

[0010] The first alloy steel powder is brought into contact with the wear-resistant powder or the first alloy steel powder is brought into contact with the wear-resistant part; and

[0011] Hot isostatic pressing is performed to form an ultra-high strength section from the first alloy steel powder and a wear-resistant section from the wear-resistant powder, resulting in a structural component. The structural component includes a connected ultra-high strength section and a wear-resistant section. The ultra-high strength section is made of first ultra-high strength steel. The tensile strength of the ultra-high strength section is greater than the tensile strength of the wear-resistant section. The wear resistance of the wear-resistant section is greater than the wear resistance of the ultra-high strength section. The tensile bond strength between the ultra-high strength section and the wear-resistant section is greater than the tensile strength of the wear-resistant section.

[0012] Thirdly, embodiments of this application also provide an electronic device, which includes:

[0013] Display screen;

[0014] A processor, electrically connected to the display screen, is used to control the display screen to perform a display; and

[0015] The structural component described in the first aspect of this application or the structural component prepared by the method described in the second aspect of this application is a structural component.

[0016] The structural component of this application includes an ultra-high strength section and a wear-resistant section. The ultra-high strength section is made of first ultra-high strength steel. The wear-resistant section is connected to the ultra-high strength section. The tensile strength of the ultra-high strength section is greater than that of the wear-resistant section, and the wear resistance of the wear-resistant section is greater than that of the ultra-high strength section. The tensile bond strength between the ultra-high strength section and the wear-resistant section is greater than that of the wear-resistant section. Therefore, the ultra-high strength section has high tensile strength, resulting in high strength for the structural component, and the wear-resistant section has high wear resistance. Through structural design, the ultra-high strength section can be placed where high strength is required, and the wear-resistant section can be placed where high wear resistance is required, allowing the structural component to simultaneously possess both ultra-high strength and high wear resistance. This is better suited for scenarios where both strength and wear resistance are highly demanding. Furthermore, compared to related technologies that use ultra-high strength steel for the main body and wear-resistant parts, the structural component of this application has higher tensile bond strength. Attached Figure Description

[0017] To more clearly illustrate the technical solutions of the embodiments of this application, the drawings used in the embodiments will be briefly introduced below. Obviously, the drawings described below are only some embodiments of this application. For those skilled in the art, other drawings can be obtained based on these drawings without creative effort.

[0018] Figure 1 This is a structural schematic diagram of a structural component according to an embodiment of this application.

[0019] Figure 2 A structural component according to an embodiment of this application is along Figure 1 A schematic diagram of the cross-sectional structure along the AA direction.

[0020] Figure 3 This is a cross-sectional structural schematic diagram of a structural component according to another embodiment of this application.

[0021] Figure 4 This is a schematic flowchart illustrating a method for preparing a structural component according to an embodiment of this application.

[0022] Figure 5 This is a schematic diagram of the filling process of the first alloy steel powder and the wear-resistant powder or the first alloy steel powder and the wear-resistant part in a structural component according to an embodiment of this application.

[0023] Figure 6 This is a schematic diagram of the structure of a mold according to an embodiment of this application.

[0024] Figure 7 This is a schematic diagram of the structure of the mold and the casing after assembly according to an embodiment of this application.

[0025] Figure 8 This is a schematic diagram of the structure of a mold according to another embodiment of this application.

[0026] Figure 9 This is a schematic diagram of the structure after the mold and the casing are assembled according to another embodiment of this application.

[0027] Figure 10 This is a schematic flowchart illustrating a method for preparing a structural component according to another embodiment of this application.

[0028] Figure 11 This is a schematic diagram of the heat treatment process according to an embodiment of this application.

[0029] Figure 12 This is a schematic diagram of the solution treatment process according to an embodiment of this application.

[0030] Figure 13 This is a schematic flowchart of the time-related processing according to an embodiment of this application.

[0031] Figure 14 This is a structural schematic diagram of a structural component according to another embodiment of this application.

[0032] Figure 15 This is a schematic diagram of the structure of an electronic device according to an embodiment of this application.

[0033] Figure 16 This is a circuit block diagram of an electronic device according to an embodiment of this application.

[0034] Explanation of reference numerals in the attached figures:

[0035] 100 - Structural component, 10 - Ultra-high strength part, 20 - Wear-resistant part, 10a - Mold, 11a - Base plate, 111a - Limiting groove, 12a - Side plate, 13a - Top plate, 14a - Mold cavity, 20a - Sheath, 300 - Electronic equipment, 310 - Display screen, 320 - Foldable mechanism, 321 - Shaft, 330 - Processor, 350 - Memory, 370 - Camera module. Detailed Implementation

[0036] To enable those skilled in the art to better understand the present application, the technical solutions in the embodiments of the present application will be clearly and completely described below with reference to the accompanying drawings. Obviously, the described embodiments are only some embodiments of the present application, and not all embodiments. Based on the embodiments in the present application, all other embodiments obtained by those of ordinary skill in the art without creative effort are within the scope of protection of the present application.

[0037] The terms "first," "second," etc., in the specification, claims, and accompanying drawings of this application are used to distinguish different objects, not to describe a specific order. Furthermore, the terms "comprising" and "having," and any variations thereof, are intended to cover non-exclusive inclusion. For example, a process, method, system, product, or apparatus that includes a series of steps or units is not limited to the listed steps or units, but may optionally include steps or units not listed, or may optionally include other steps or units inherent to these processes, methods, products, or apparatuses.

[0038] The technical solutions in the embodiments of this application will now be described with reference to the accompanying drawings.

[0039] It should be noted that, for ease of explanation, the same reference numerals denote the same components in the embodiments of this application, and for the sake of brevity, detailed descriptions of the same components are omitted in different embodiments.

[0040] Ultra-high strength steel is a type of alloy steel used to manufacture structural components that withstand high stress. It typically has a yield strength greater than 1180 MPa and a tensile strength greater than 1380 MPa. This type of steel generally possesses sufficient toughness, high specific strength and yield strength ratio, as well as good weldability and formability. Based on the degree of alloying and microstructure, it can be divided into three categories: low-alloy, medium-alloy, and high-alloy ultra-high strength steel. Ultra-high strength structural steel can also be divided into: low-alloy ultra-high strength steel, maraging steel, and precipitation-hardening stainless steel. As the strength increases, the material's ductility decreases significantly.

[0041] Ultra-high strength steel has good yield strength and ductility. However, it contains very few or almost no hard phases. Therefore, ultra-high strength steel has poor wear resistance and is difficult to use as structural components with high wear resistance requirements.

[0042] In related technologies, when structural components require high wear resistance and high strength, ultra-high strength steel can be used as the main component, and a wear-resistant coating (such as diamond-like carbon (DLC)) can be applied to its surface. However, the coating thickness is very thin, generally less than 3 μm, and some are even at the nanometer level. Under strong stress conditions, and due to the internal stress of the coating itself, the coating is easily worn away. Once the coating is removed, the wear resistance of the structural component will decrease significantly.

[0043] In addition, ultra-high strength steel main components and wear-resistant components can be assembled into a single unit. However, this method is not suitable for precision parts. Assembly requires more space and is not applicable to small or precision parts. Furthermore, the bond strength of this assembly method is relatively weaker compared to the strength of the integrally formed part itself.

[0044] Please see Figure 1 and Figure 2 This application provides a structural component 100, which includes an ultra-high strength part 10 and a wear-resistant part 20. The ultra-high strength part 10 is made of first ultra-high strength steel. The wear-resistant part 20 is connected to the ultra-high strength part 10. The tensile strength of the ultra-high strength part 10 is greater than the tensile strength of the wear-resistant part 20, the wear resistance of the wear-resistant part 20 is greater than the wear resistance of the ultra-high strength part 10, and the tensile bonding strength between the ultra-high strength part 10 and the wear-resistant part 20 is greater than the tensile strength of the wear-resistant part 20.

[0045] The structural component 100 in this application embodiment can be, but is not limited to, a pivot (e.g., the pivot of a foldable device), a housing, a mid-frame, a button, a hinge, a gear, or other force-bearing component. In the following description and accompanying drawings of this application, the structural component 100 is exemplified by a pivot and should not be construed as a limitation on the structural component 100 of this application.

[0046] The structural component 100 of this application embodiment can be applied to electronic devices. These electronic devices can be, but are not limited to, mobile phones, tablets, laptops, desktop computers, smart bracelets, smartwatches, e-readers, game consoles, etc. The electronic devices can also be foldable electronic devices, candybar electronic devices, etc.

[0047] In ultra-high strength steel, martensite is a microstructure of ferrous metals, a supersaturated solid solution of carbon in α-Fe. Martensite possesses high strength and Vickers hardness. Austenite is a lamellar microstructure of steel, typically a non-magnetic solid solution of a small amount of carbon dissolved in γ-Fe. Austenite exhibits good plasticity, lower strength, and some toughness.

[0048] It should be noted that the ultra-high strength part 10 and the wear-resistant part 20 are an integral structure.

[0049] Optionally, the toughness of the ultra-high strength portion 10 is greater than that of the wear-resistant portion 20. The hardness of the ultra-high strength portion 10 is less than that of the wear-resistant portion 20.

[0050] The structural component 100 of this application embodiment includes an ultra-high strength part 10 and a wear-resistant part 20. The ultra-high strength part 10 is made of first ultra-high strength steel. The wear-resistant part 20 is connected to the ultra-high strength part 10. The tensile strength of the ultra-high strength part 10 is greater than the tensile strength of the wear-resistant part 20. The wear resistance of the wear-resistant part 20 is greater than the wear resistance of the ultra-high strength part 10. The tensile bonding strength between the ultra-high strength part 10 and the wear-resistant part 20 is greater than the tensile strength of the wear-resistant part 20. Therefore, the ultra-high strength part 10 has high tensile strength, resulting in high strength for the structural component 100, while the wear-resistant part 20 has high wear resistance. Through this structural design, the ultra-high strength part 10 can be positioned where high strength is required in the structural component 100, and the wear-resistant part 20 can be positioned where high wear resistance is required. This allows the structural component 100 to simultaneously possess both ultra-high strength and high wear resistance, making it better suited for scenarios where both strength and wear resistance of the structural component 100 are highly demanding. Furthermore, compared to related technologies that use ultra-high strength steel for the main body and wear-resistant parts, the structural component 100 of this application has a higher tensile bonding strength.

[0051] In some embodiments, the ultra-high strength portion 10 comprises, by mass fraction:

[0052] 16% to 19% nickel (Ni);

[0053] 14% to 17% cobalt (Co);

[0054] 5% to 8% molybdenum (Mo);

[0055] 0.2% to 0.4% chromium (Cr);

[0056] Less than or equal to 1% vanadium (V); and

[0057] The balance of iron (Fe).

[0058] In other words, the first ultra-high strength steel comprises, by mass fraction: 16% to 19% nickel (Ni); 14% to 17% cobalt (Co); 5% to 8% molybdenum (Mo); 0.2% to 0.4% chromium (Cr); less than or equal to 1% vanadium (V); and the balance iron (Fe).

[0059] In the embodiments of this application, when the numerical range a to b is involved, unless otherwise specified, the numerical value can be any value between a and b, including the endpoint value a and the endpoint value b.

[0060] Specifically, the mass fraction of nickel in the ultra-high strength section 10 can be, but is not limited to, 16 wt%, 16.5 wt%, 17 wt%, 17.5 wt%, 18 wt%, 18.5 wt%, 19 wt%, etc. Nickel is an austenite-forming element, which can lower the onset temperature of martensite transformation and promote martensite transformation and formation. Nickel can strengthen ferrite and refine and increase pearlite, thereby improving the strength of the ultra-high strength section 10, while having little impact on the plasticity of the ultra-high strength section 10. When the mass fraction of nickel is too low, it is difficult to form a single austenite, reducing the content of retained austenite in the ultra-high strength section 10, which is not conducive to improving the ductility of the ultra-high strength section 10; when the mass fraction of nickel is too high, it is not conducive to the formation of martensite, increasing the content of retained austenite in the ultra-high strength section 10, which is not conducive to improving the strength and Vickers hardness of the ultra-high strength section 10.

[0061] Specifically, the mass fraction of cobalt in the ultra-high strength section 10 can be, but is not limited to, 14 wt%, 14.5 wt%, 15 wt%, 15.5 wt%, 16 wt%, 16.5 wt%, 17 wt%, etc. Cobalt is an austenite-forming element and can promote the formation of intermetallic compounds. Within a certain range, increasing the cobalt content can improve the tensile strength and yield strength of the ultra-high strength section 10 and give it better plasticity. In addition, cobalt can also promote the formation of more reinforcing phases of molybdenum, thereby improving the tensile strength and yield strength of the ultra-high strength section 10. Therefore, if the cobalt content is too low, it is not conducive to improving the tensile strength and yield strength of the ultra-high strength section 10, but it can give the ultra-high strength section 10 better plasticity; however, if the cobalt content is too high (i.e., exceeding a certain value), although the ultra-high strength section 10 still has high tensile strength and yield strength, its plasticity and elongation decrease.

[0062] Specifically, the mass fraction of molybdenum in the ultra-high strength section 10 can be, but is not limited to, 5 wt%, 5.5 wt%, 6 wt%, 6.5 wt%, 7 wt%, 7.5 wt%, 8 wt%, etc. Molybdenum is a reinforcing element of the first ultra-high strength steel, and it can increase the tensile strength, yield strength, Vickers hardness, and wear resistance of the ultra-high strength section 10. Mo can form various alloys with elements such as carbon, chromium, and nickel in the ultra-high strength section 10. These alloys can enhance the grain boundary strength and grain boundary stability of the ultra-high strength section 10, thereby improving its strength and Vickers hardness. In addition, Mo can also improve the grain refinement of the ultra-high strength section 10, making its microstructure more uniform, thereby improving its toughness and tensile properties. However, a high molybdenum content is not conducive to decarburization, thus resulting in a high carbon content in the ultra-high strength section 10, which reduces its plasticity and elongation.

[0063] Specifically, the mass fraction of chromium in the ultra-high strength section 10 can be, but is not limited to, 0.2 wt%, 0.25 wt%, 0.3 wt%, 0.35 wt%, 0.4 wt%, etc. Chromium can play a role in solid solution strengthening and alloy carbide strengthening. In addition, it can control the carbon content in the ultra-high strength section 10, thereby reducing the carbon content in the ultra-high strength section 10 and improving the mechanical properties of the ultra-high strength section 10, such as tensile strength, yield strength, and wear resistance. If the chromium content is too low, the improvement on the tensile strength and yield strength of the ultra-high strength section 10 will be limited; if the chromium content is too high, the plasticity of the ultra-high strength section 10 will be easily affected, reducing the elongation of the ultra-high strength section 10.

[0064] Specifically, the mass fraction of vanadium in the ultra-high strength section 10 can be, but is not limited to, 0.1%, 0.2%, 0.3%, 0.4%, 0.5%, 0.6%, 0.7%, 0.8%, 0.7%, 1.0%, etc. Vanadium is a strengthening element of ultra-high strength steel, which can refine the grain and improve the tensile strength and yield strength of the ultra-high strength section 10; however, excessive vanadium content will reduce the plasticity and elongation of the ultra-high strength section 10. In addition, vanadium readily combines with oxygen, and the oxygen combined with vanadium can promote decarburization, thereby further reducing the carbon content in the ultra-high strength section 10, resulting in higher tensile strength and yield strength of the ultra-high strength section 10. Vanadium is a strengthening element in the ultra-high strength section 10. It can refine the grain size and improve the tensile strength and yield strength of the ultra-high strength section 10. In addition, vanadium readily combines with oxygen, and the oxygen combined with vanadium can promote decarburization, thereby further reducing the carbon content in the ultra-high strength section 10, resulting in even higher tensile strength and yield strength. If the mass fraction of vanadium is too low, the strengthening phase formed in the ultra-high strength section 10 will be insufficient, limiting the improvement of the ultra-high strength section 10; if the mass fraction of vanadium is too high, it will also reduce the plasticity and elongation of the ultra-high strength section 10.

[0065] Furthermore, in the ultra-high strength section 10, the mass fraction of vanadium is 0.2% to 0.8%. This allows the ultra-high strength section 10 to have both high tensile strength and yield strength, as well as good plasticity and elongation.

[0066] In some embodiments, the ultra-high strength portion 10 further includes at least one of impurity elements such as carbon (C), sulfur (S), silicon (Si), and manganese (Mn). In other words, the first ultra-high strength steel further includes at least one of impurity elements such as carbon (C), sulfur (S), silicon (Si), and manganese (Mn) by mass fraction.

[0067] Optionally, in the ultra-high strength section 10, the mass fraction of carbon is less than or equal to 0.3%. Specifically, in the ultra-high strength section 10, the mass fraction of carbon can be, but is not limited to, less than or equal to 0.3%, less than or equal to 0.2%, less than or equal to 0.1%, less than or equal to 0.08%, less than or equal to 0.05%, less than or equal to 0.03%, less than or equal to 0.02%, less than or equal to 0.01%, etc. A higher carbon content in the ultra-high strength section 10 can improve its Vickers hardness and wear resistance, but it will reduce its plasticity and elongation.

[0068] Optionally, in the ultra-high strength section 10, the mass fraction of sulfur is less than or equal to 0.05%. Specifically, in the ultra-high strength section 10, the mass fraction of sulfur can be, but is not limited to, less than or equal to 0.05%, less than or equal to 0.04%, less than or equal to 0.03%, less than or equal to 0.02%, less than or equal to 0.01%, etc. Sulfur is a harmful element in the ultra-high strength section 10. Excessive sulfur content makes the ultra-high strength section 10 prone to brittleness during high-temperature pressure processing, reducing the ductility and toughness of the ultra-high strength section 10.

[0069] Optionally, in the ultra-high strength section 10, the mass fraction of silicon is less than or equal to 0.5%. Specifically, in the ultra-high strength section 10, the mass fraction of silicon can be, but is not limited to, less than or equal to 0.5%, less than or equal to 0.45%, less than or equal to 0.4%, less than or equal to 0.35%, less than or equal to 0.3%, less than or equal to 0.25%, etc. Silicon can improve the Vickers hardness of the ultra-high strength section 10; however, silicon readily reacts with oxygen to form ceramic phase particles, creating defects and reducing the plasticity and elongation of the ultra-high strength section 10. When the mass fraction of silicon in the ultra-high strength section 10 is controlled within a certain range, the ultra-high strength section 10 can possess both high Vickers hardness and high plasticity and elongation.

[0070] Optionally, in the ultra-high strength section 10, the mass fraction of manganese is less than or equal to 0.1%. Specifically, in the ultra-high strength section 10, the mass fraction of manganese can be, but is not limited to, less than or equal to 0.1%, less than or equal to 0.09%, less than or equal to 0.08%, less than or equal to 0.07%, less than or equal to 0.05%, less than or equal to 0.03%, less than or equal to 0.04%, etc. Manganese can improve the strength of the ultra-high strength section 10, weaken or eliminate the adverse effects of sulfur, and improve the hardenability of the ultra-high strength section 10. However, manganese easily adsorbs carbon, thereby reducing the plasticity and elongation of the ultra-high strength section 10.

[0071] Optionally, the first ultra-high strength steel is lath martensite, and the mass fraction of lath martensite in the first ultra-high strength steel is greater than or equal to 99 wt%. Further, the mass fraction of lath martensite in the first ultra-high strength steel is greater than or equal to 99.5 wt%. Specifically, the mass fraction of lath martensite in the first ultra-high strength steel can be, but is not limited to, 99 wt%, 99.1 wt%, 99.2 wt%, 99.3 wt%, 99.4 wt%, 99.5 wt%, 99.6 wt%, 99.7 wt%, and 99.8 wt%. This allows the first ultra-high strength steel to have higher strength and Vickers hardness, and also better toughness and elongation. If the mass fraction of lath martensite in the first ultra-high strength steel is too low, it will reduce the strength and Vickers hardness of the first ultra-high strength steel.

[0072] In some embodiments, the tensile strength of the ultra-high strength portion 10 ranges from 1900 MPa to 2200 MPa. Specifically, the tensile strength of the ultra-high strength portion 10 can be, but is not limited to, 1900 MPa, 1950 MPa, 2000 MPa, 2050 MPa, 2100 MPa, 2150 MPa, 2200 MPa, 2250 MPa, 2300 MPa, 2350 MPa, etc. The ultra-high strength portion 10 of this application embodiment has high tensile strength, thereby it can be better applied to structural components 100 with high requirements for tensile and impact resistance.

[0073] Optionally, the yield strength of the ultra-high strength portion 10 ranges from 1600 MPa to 1800 MPa. Specifically, the yield strength of the ultra-high strength portion 10 can be, but is not limited to, 1600 MPa, 1650 MPa, 1700 MPa, 1750 MPa, 1800 MPa, etc. The ultra-high strength portion 10 of this embodiment has a good yield strength, and therefore can be better applied to structural components 100 with high requirements for yield strength, impact resistance, and other performance characteristics.

[0074] Optionally, the elongation of the ultra-high strength portion 10 ranges from 4% to 10%. Specifically, the elongation of the ultra-high strength portion 10 can be, but is not limited to, 4%, 4.3%, 4.5%, 4.8%, 5%, 5.3%, 5.5%, 5.8%, 6%, 6.3%, 6.5%, 6.8%, 7%, 7.1%, 7.3%, 7.5%, 8%, 8.5%, 9%, 9.5%, and 10%. The ultra-high strength portion 10 of this application has high plasticity and elongation, which is beneficial for its application.

[0075] Optionally, the modulus E of the ultra-high strength portion 10 ranges from 170 GPa to 200 GPa. Specifically, the modulus E of the ultra-high strength portion 10 of this application can be, but is not limited to, 170 GPa, 175 GPa, 180 GPa, 185 GPa, 190 GPa, 195 GPa, 200 GPa, etc. The ultra-high strength portion 10 of this application has a high modulus.

[0076] Optionally, the microhardness of the ultra-high strength portion 10 ranges from 560 HV to 650 HV. Specifically, the microhardness of the ultra-high strength portion 10 can be, but is not limited to, 560 HV, 570 HV, 580 HV, 590 HV, 600 HV, 610 HV, 620 HV, 630 HV, 640 HV, 650 HV, etc. The ultra-high strength steel of this application has a high Vickers hardness, thereby exhibiting good wear resistance.

[0077] In summary, the ultra-high strength part 10 of this application has high tensile strength and yield strength, high microhardness and modulus, and high elongation.

[0078] In some embodiments, the tensile strength of the wear-resistant portion 20 ranges from 300 MPa to 1500 MPa.

[0079] Specifically, the tensile strength of the wear-resistant part 20 can be, but is not limited to, 300 MPa, 350 MPa, 380 MPa, 400 MPa, 450 MPa, 500 MPa, 600 MPa, 700 MPa, 800 MPa, 900 MPa, 1000 MPa, 1100 MPa, 1200 MPa, 1300 MPa, 1400 MPa, 1500 MPa, etc.

[0080] In some embodiments, the wear-resistant part 20 is made of ceramic material, and the tensile strength of the wear-resistant part 20 ranges from 300 MPa to 500 MPa. In other embodiments, the wear-resistant part 20 is made of a second ultra-high strength steel and ceramic material, and the tensile strength of the wear-resistant part 20 ranges from 900 MPa to 1500 MPa.

[0081] In this embodiment, if the tensile strength of the wear-resistant part 20 is too low, the overall tensile strength of the structural component 100 will be reduced; if the tensile strength of the wear-resistant part 20 is too high, it will be difficult to achieve in terms of manufacturing process, or a solution that can achieve higher tensile strength would sacrifice the wear resistance of the wear-resistant part 20. In this embodiment, the wear-resistant part 20 has both high wear resistance and high tensile strength.

[0082] like Figure 1 As shown, in some embodiments, the wear-resistant portion 20 is disposed around the outer periphery of the ultra-high strength portion 10.

[0083] In some other embodiments, the wear-resistant portion 20 is partially embedded in the ultra-high strength portion 10.

[0084] Please see Figure 3 In some other embodiments, the wear-resistant portion 20 is disposed on one side of the ultra-high strength portion 10.

[0085] It should be noted that when the wear-resistant part 20 is arranged around the outer periphery of the ultra-high strength part 10, it can be arranged around only a portion of the outer periphery of the ultra-high strength part 10; or it can be arranged around the entire outer periphery of the ultra-high strength part 10. The arrangement position of the wear-resistant part 20 can be designed according to actual needs. This allows the structural component 100 to have high strength in the middle and high wear resistance at the outer contact friction positions, thus simultaneously possessing ultra-high strength and good wear resistance.

[0086] It should be noted that the wear-resistant part 20 is partially embedded in the ultra-high strength part 10. Understandably, the wear-resistant part 20 can be partially embedded in the ultra-high strength part 10 and partially protrude from the ultra-high strength part 10; or the main body of the wear-resistant part 20 can be embedded in the ultra-high strength part 10, but the surface is exposed in the ultra-high strength part 10 and the surface of the wear-resistant part 20 is flush with the surface of the ultra-high strength part 10.

[0087] In this embodiment, the wear-resistant portion 20 is disposed around the outer periphery of the ultra-high strength portion 10; or, the wear-resistant portion 20 is partially embedded in the ultra-high strength portion 10. This allows for better integration between the ultra-high strength portion 10 and the wear-resistant portion 20, with the wear-resistant portion 20 exposed, thus providing better wear resistance for the structural component 100.

[0088] Optionally, the minimum thickness of the wear-resistant part 20 is greater than or equal to 0.3 mm. Specifically, the minimum thickness of the wear-resistant part 20 can be, but is not limited to, greater than or equal to 0.3 mm, greater than or equal to 0.4 mm, greater than or equal to 0.5 mm, greater than or equal to 0.6 mm, greater than or equal to 0.8 mm, greater than or equal to 1.0 mm, greater than or equal to 1.5 mm, greater than or equal to 2.0 mm, greater than or equal to 3.0 mm, etc. The thickness of the wear-resistant part 20 can be designed according to actual needs. The thicker the wear-resistant part 20, the longer its service life.

[0089] In some embodiments, the wear-resistant part 20 is made of ceramic material.

[0090] In other embodiments, the wear-resistant part 20 is made of a second ultra-high strength steel and a ceramic material, wherein the mass fraction of the ceramic material in the wear-resistant part 20 ranges from 5% to 18%; and the mass fraction of the second ultra-high strength steel ranges from 82% to 95%.

[0091] In some embodiments, the ceramic material has a mass fraction of 5% to 18% in the wear-resistant portion 20.

[0092] Understandably, the mass fraction of ceramic material in the wear-resistant part 20 can be any value between 5% and 18%. Specifically, the mass fraction of ceramic material in the wear-resistant part 20 can be 5%, 6%, 7%, 8%, 9%, 10%, 11%, 12%, 13%, 14%, 15%, 16%, 17%, 18%, etc. If the mass fraction of ceramic material in the wear-resistant part 20 is too low, the wear resistance of the wear-resistant part 20 will be too low, reducing the wear resistance of the structural component 100; if the mass fraction of ceramic material in the wear-resistant part 20 is too high, although the wear resistance of the wear-resistant part 20 will increase, the overall brittleness of the wear-resistant part 20 will increase, reducing the tensile strength, yield strength, and toughness of the wear-resistant part 20. When the mass fraction of ceramic material in the wear-resistant part 20 is 5% to 18%, the second ultra-high strength steel and ceramic material in the wear-resistant part 20 can have a suitable ratio, so that the wear-resistant part 20 has good wear resistance, as well as high tensile strength, yield strength and toughness.

[0093] Optionally, the mass fraction of the second ultra-high strength steel in the wear-resistant part 20 is 82% to 95%. Understandably, the mass fraction of the second ultra-high strength steel in the wear-resistant part 20 can be any value between 82% and 95%. Specifically, the mass fraction of the second ultra-high strength steel in the wear-resistant part 20 can be 82%, 84%, 86%, 88%, 90%, 92%, 94%, 95%, etc. If the mass fraction of the second ultra-high strength steel in the wear-resistant part 20 is too low, the wear resistance of the wear-resistant part 20 increases, but the overall brittleness of the wear-resistant part 20 increases, reducing the tensile strength, yield strength, and toughness of the wear-resistant part 20; if the mass fraction of the second ultra-high strength steel in the wear-resistant part 20 is too high, the wear resistance of the wear-resistant part 20 is too low, reducing the wear resistance of the structural component 100. When the mass fraction of the second ultra-high strength steel in the wear-resistant part 20 is 82% to 95%, the second ultra-high strength steel and ceramic material in the wear-resistant part 20 can have a suitable ratio, so that the wear-resistant part 20 has good wear resistance, as well as high tensile strength, yield strength and toughness.

[0094] Optionally, the second ultra-high strength steel comprises, by mass fraction: 16% to 19% nickel (Ni); 14% to 17% cobalt (Co); 5% to 8% molybdenum (Mo); 0.2% to 0.4% chromium (Cr); less than or equal to 1% vanadium (V); and the balance iron (Fe).

[0095] Specifically, the mass fraction of nickel in the second ultra-high strength steel can be, but is not limited to, 16 wt%, 16.5 wt%, 17 wt%, 17.5 wt%, 18 wt%, 18.5 wt%, 19 wt%, etc. Nickel is an austenite-forming element, which can lower the onset temperature of martensite transformation and promote martensite transformation and formation. Nickel can strengthen ferrite and refine and increase pearlite, thereby improving the strength of the second ultra-high strength steel, while having little effect on its plasticity. When the mass fraction of nickel is too low, it is difficult to form single austenite, reducing the content of retained austenite in the second ultra-high strength steel, which is not conducive to improving the ductility of the second ultra-high strength steel; when the mass fraction of nickel is too high, it is not conducive to the formation of martensite, increasing the content of retained austenite in the second ultra-high strength steel, which is not conducive to improving the strength and Vickers hardness of the second ultra-high strength steel.

[0096] Specifically, the mass fraction of cobalt in the second ultra-high strength steel can be, but is not limited to, 14 wt%, 14.5 wt%, 15 wt%, 15.5 wt%, 16 wt%, 16.5 wt%, and 17 wt%. Cobalt is an austenite-forming element and can promote the formation of intermetallic compounds. Within a certain range, increasing the cobalt content can improve the tensile strength and yield strength of the second ultra-high strength steel and give it better plasticity. In addition, cobalt can also promote the formation of more molybdenum strengthening phases, thereby improving the tensile strength and yield strength of the second ultra-high strength steel. Therefore, if the cobalt content is too low, it is not conducive to improving the tensile strength and yield strength of the second ultra-high strength steel, but it can give the second ultra-high strength steel better plasticity; however, if the cobalt content is too high (i.e., exceeding a certain value), although the second ultra-high strength steel still has high tensile strength and yield strength, its plasticity and elongation decrease.

[0097] Specifically, the mass fraction of molybdenum in the second ultra-high strength steel can be, but is not limited to, 5 wt%, 5.5 wt%, 6 wt%, 6.5 wt%, 7 wt%, 7.5 wt%, and 8 wt%. Molybdenum is a reinforcing element in the second ultra-high strength steel, increasing its tensile strength, yield strength, Vickers hardness, and wear resistance. Mo can form various alloys with elements such as carbon, chromium, and nickel in the second ultra-high strength steel. These alloys enhance the grain boundary strength and stability of the second ultra-high strength steel, thereby improving its strength and Vickers hardness. Furthermore, Mo can improve the grain refinement of the second ultra-high strength steel, making its microstructure more uniform, thus improving its toughness and tensile properties. However, a high molybdenum content is detrimental to decarburization, resulting in a higher carbon content in the second ultra-high strength steel, which reduces its plasticity and elongation.

[0098] Specifically, the mass fraction of chromium in the second ultra-high strength steel can be, but is not limited to, 0.2 wt%, 0.25 wt%, 0.3 wt%, 0.35 wt%, 0.4 wt%, etc. Chromium can play a role in solid solution strengthening and alloy carbide strengthening. In addition, it can control the carbon content in the second ultra-high strength steel, thereby reducing the carbon content and improving the mechanical properties of the second ultra-high strength steel, such as tensile strength, yield strength, and wear resistance. If the chromium content is too low, the improvement on the tensile strength and yield strength of the second ultra-high strength steel will be limited; if the chromium content is too high, the plasticity of the second ultra-high strength steel will be easily affected, reducing the elongation of the second ultra-high strength steel.

[0099] Specifically, the mass fraction of vanadium in the second ultra-high strength steel can be, but is not limited to, 0.1%, 0.2%, 0.3%, 0.4%, 0.5%, 0.6%, 0.7%, 0.8%, 0.7%, and 1.0%. Vanadium is a strengthening element in the second ultra-high strength steel, which can refine the grain size and improve its tensile strength and yield strength. However, excessively high vanadium content will reduce the plasticity and elongation of the second ultra-high strength steel. Furthermore, vanadium readily combines with oxygen, and the oxygen formed by vanadium can promote decarburization, thereby further reducing the carbon content in the second ultra-high strength steel, resulting in higher tensile strength and yield strength. If the vanadium mass fraction is too low, the strengthening phase formed in the second ultra-high strength steel is insufficient, thus limiting its improvement; if the vanadium mass fraction is too high, it will also reduce the plasticity and elongation of the second ultra-high strength steel.

[0100] Furthermore, in the second ultra-high strength steel, the mass fraction of vanadium is 0.2% to 0.8%. This allows the second ultra-high strength steel to possess both high tensile strength and yield strength, as well as good plasticity and elongation.

[0101] In some embodiments, the second ultra-high strength steel further includes at least one of impurity elements such as carbon (C), sulfur (S), silicon (Si), and manganese (Mn).

[0102] Optionally, in the second ultra-high strength steel, the mass fraction of carbon is less than or equal to 0.3%. Specifically, in the second ultra-high strength steel, the mass fraction of carbon can be, but is not limited to, less than or equal to 0.3%, less than or equal to 0.2%, less than or equal to 0.1%, less than or equal to 0.08%, less than or equal to 0.05%, less than or equal to 0.03%, less than or equal to 0.02%, less than or equal to 0.01%, etc. In the second ultra-high strength steel, a higher carbon content can improve the Vickers hardness and wear resistance of the second ultra-high strength steel, but it will reduce the plasticity and elongation of the second ultra-high strength steel.

[0103] Optionally, in the second ultra-high strength steel, the mass fraction of sulfur is less than or equal to 0.05%. Specifically, the mass fraction of sulfur in the second ultra-high strength steel can be, but is not limited to, less than or equal to 0.05%, less than or equal to 0.04%, less than or equal to 0.03%, less than or equal to 0.02%, less than or equal to 0.01%, etc. Sulfur is a harmful element in the second ultra-high strength steel. Excessive sulfur content makes the second ultra-high strength steel prone to brittle fracture during high-temperature and high-pressure processing, reducing its ductility and toughness.

[0104] Optionally, in the second ultra-high strength steel, the mass fraction of silicon is less than or equal to 0.5%. Specifically, the mass fraction of silicon in the second ultra-high strength steel can be, but is not limited to, less than or equal to 0.5%, less than or equal to 0.45%, less than or equal to 0.4%, less than or equal to 0.35%, less than or equal to 0.3%, less than or equal to 0.25%, etc. Silicon can improve the Vickers hardness of the second ultra-high strength steel; however, silicon readily reacts with oxygen to form ceramic phase particles, creating defects and reducing the plasticity and elongation of the second ultra-high strength steel. When the mass fraction of silicon in the second ultra-high strength steel is controlled within a certain range, the second ultra-high strength steel can possess both high Vickers hardness and high plasticity and elongation.

[0105] Optionally, in the second ultra-high strength steel, the mass fraction of manganese is less than or equal to 0.1%. Specifically, in the second ultra-high strength steel, the mass fraction of manganese can be, but is not limited to, less than or equal to 0.1%, less than or equal to 0.09%, less than or equal to 0.08%, less than or equal to 0.07%, less than or equal to 0.05%, less than or equal to 0.03%, less than or equal to 0.04%, etc. Manganese can improve the strength of the second ultra-high strength steel, weaken or eliminate the adverse effects of sulfur, and improve the hardenability of the second ultra-high strength steel. However, manganese easily adsorbs carbon, thereby reducing the plasticity and elongation of the second ultra-high strength steel.

[0106] Optionally, the composition of the first ultra-high strength steel and the second ultra-high strength steel may be the same or different.

[0107] In some embodiments, the ceramic material includes at least one of silicon carbide, tungsten carbide, alumina, and zirconium oxide. These ceramic materials have high hardness, chemical stability, and wear resistance. Using these ceramic materials as the material for the wear-resistant part 20 can make the wear-resistant part 20 have higher wear resistance, thereby making the structural component 100 have higher wear resistance, allowing it to be used for a longer period of time without being easily worn, and thus having a longer service life.

[0108] In some embodiments, the wear-resistant part 20 is made of ceramic material, and the Mohs hardness of the wear-resistant part 20 ranges from 7.5 to 9.8.

[0109] Specifically, the Mohs hardness range of the wear-resistant part 20 is 7.5, 7.6, 7.7, 7.8, 7.9, 8.0, 8.1, 8.2, 8.3, 8.4, 8.5, 8.6, 8.7, 8.8, 8.9, 9.0, 9.1, 9.2, 9.3, 9.4, 9.5, 9.6, 9.7, and 9.8. If the Mohs hardness of the wear-resistant part 20 is too low, its wear resistance will be reduced, which is not conducive to improving the service life of the structural component 100; if the Mohs hardness of the wear-resistant part 20 is too high, the material will be difficult to achieve.

[0110] In one specific example, the wear-resistant part 20 is made of silicon carbide, and its Mohs hardness is 9.2 to 9.8. Silicon carbide has good wear resistance, but because silicon carbide itself is brittle, it is at risk of fracture when subjected to a large impact.

[0111] In a specific example, the wear-resistant part 20 is made of zirconia ceramic, and its Mohs hardness is 7.5 to 9.0. The hardness of zirconia ceramic is related to the zirconia content; 95% zirconia ceramic has a Mohs hardness of 9.0, 80% zirconia ceramic has a Mohs hardness of 8.0, and 65% zirconia ceramic has a Mohs hardness of 7.5.

[0112] In one specific example, the wear-resistant part 20 is made of alumina ceramic, and its Mohs hardness is 9.0 to 9.5. The hardness of alumina ceramic is related to its alumina content; when the Mohs hardness of the alumina ceramic is high, its brittleness is also high, which is unfavorable for applications subjected to large impact fields. Optionally, the alumina content in the alumina ceramic is 85% to 95% by mass, and its hardness can approach that of diamond.

[0113] In a specific example, the wear-resistant part 20 is made of tungsten carbide, and its Mohs hardness is 8.9 to 9.0. Using tungsten carbide as the wear-resistant part 20 allows it to possess both good corrosion resistance and wear resistance.

[0114] In other embodiments, the wear-resistant part 20 is made of a second ultra-high strength steel and ceramic material, and the microhardness of the wear-resistant part 20 ranges from 560HV to 650HV.

[0115] Specifically, the microhardness of the wear-resistant part 20 can be, but is not limited to, 560HV, 570HV, 575HV, 580HV, 585HV, 590HV, 595HV, 600HV, 605HV, 610HV, 615HV, 620HV, 625HV, 630HV, 635HV, 640HV, 645HV, 650HV, etc. If the microhardness of the wear-resistant part 20 is too low, its wear resistance will be reduced, which is not conducive to improving the service life of the structural component 100; if the microhardness of the wear-resistant part 20 is too high, the material will be difficult to achieve.

[0116] In some embodiments, the raw material composition of the ultra-high strength part 10 includes a first alloy steel powder, and the raw material composition of the wear-resistant part 20 includes ceramic powder or ceramic powder and a second alloy steel powder, wherein the average particle size of the first alloy steel powder is greater than the average particle size of the ceramic powder.

[0117] Understandably, the raw material composition of the wear-resistant part 20 may be only ceramic powder; the raw material composition of the wear-resistant part 20 may also be ceramic powder and second alloy steel powder.

[0118] It should be noted that the first alloy steel powder is used to form the first ultra-high strength steel, the second alloy steel powder is used to form the second ultra-high strength steel, and the ceramic powder is used to form ceramic materials.

[0119] Optionally, the first alloy steel powder can be an ultra-high strength steel based on 18Ni (18Ni) martensite, and the first alloy steel powder can be prepared by water vapor combined atomization.

[0120] In this embodiment, when the average particle size of the first alloy steel powder is greater than the average particle size of the ceramic powder, it is beneficial for the ceramic powder to be embedded in the first alloy steel powder during the preparation of the structural component 100. This allows the ceramic phase of the wear-resistant part 20 of the structural component 100 to be better embedded in the steel phase of the ultra-high strength part 10, thereby improving the bonding strength between the ultra-high strength part 10 and the wear-resistant part 20.

[0121] In some embodiments, the D10 range of the first alloy steel powder is: 3μm≤D10≤10μm, the median particle size D50 range of the first alloy steel powder is: 15μm≤D50≤75μm, and the D90 range of the first alloy steel powder is: 50μm≤D90≤90μm.

[0122] "D10" refers to the particle size corresponding to a cumulative particle size distribution percentage of 10% for the first alloy steel powder.

[0123] "D50" refers to the particle size corresponding to a cumulative particle size distribution percentage of 50% for the first alloy steel powder.

[0124] "D90" refers to the particle size corresponding to a cumulative particle size distribution percentage of 50% for the first alloy steel powder.

[0125] Specifically, the D10 of the first alloy steel powder can be, but is not limited to, 3μm, 4μm, 5μm, 6μm, 7μm, 8μm, 9μm, 10μm, etc. When the D10 particle size of the first alloy steel powder is within this range, the first alloy steel powder can be packed more tightly, and the small particles in the first alloy steel powder can better fill the gaps between the large particles, thereby making the obtained ultra-high strength part 10 have higher density.

[0126] Specifically, the median particle size D50 of the first alloy steel powder can be, but is not limited to, 15μm, 20μm, 25μm, 30μm, 35μm, 40μm, 45μm, 50μm, 55μm, 60μm, 65μm, 70μm, 75μm, etc. In this embodiment, if the median particle size D50 of the first alloy steel powder is too small, the austenite grain size in the resulting ultra-high strength section 10 will be too large, reducing the tensile strength and yield strength of the ultra-high strength section 10. In addition, the larger grain size makes the grains more prone to slippage, reducing the plasticity of the ultra-high strength section 10. If the median particle size D50 of the first alloy steel powder is too large, the compactness of the ultra-high strength section 10 will be reduced, the porosity of the ultra-high strength section 10 will increase, and the brittleness will increase, which will also reduce the tensile strength and yield strength of the ultra-high strength section 10.

[0127] Specifically, the D90 of the first alloy steel powder can be, but is not limited to, 50μm, 55μm, 60μm, 65μm, 70μm, 75μm, 80μm, 85μm, 90μm, etc. When the D90 particle size of the first alloy steel powder is within this range, the gaps formed by the accumulation of large particles in the first alloy steel powder can be better filled by small particles, the first alloy steel powder is more compactly packed, and the resulting ultra-high strength part 10 has higher density.

[0128] In some embodiments, the range of D10' of the ceramic powder is: 3μm≤D10'≤5μm, the range of the median particle size D50' of the ceramic powder is: 8μm≤D50'≤15μm, and the range of D90' of the ceramic powder is: 18μm≤D90'≤25μm.

[0129] "D10" refers to the particle size corresponding to a cumulative particle size distribution percentage of 10% for ceramic powder.

[0130] "D50" refers to the particle size corresponding to a cumulative particle size distribution percentage of 50% for ceramic powder.

[0131] "D90" refers to the particle size corresponding to a cumulative particle size distribution percentage of 50% for ceramic powder.

[0132] Specifically, the D10' of the ceramic powder can be, but is not limited to, 3μm, 3.5μm, 4μm, 4.5μm, 5μm, etc. When the D10 particle size of the ceramic powder is within this range, the ceramic powder can be packed more tightly, and the small particles in the ceramic powder can better fill the gaps between the large particles, thereby making the obtained ultra-high strength part 10 have higher density.

[0133] Specifically, the median particle size D50' of the ceramic powder can be, but is not limited to, 8μm, 9μm, 10μm, 11μm, 12μm, 13μm, 14μm, 15μm, etc. In this embodiment, if the median particle size D50' of the ceramic powder is too small, it increases the cost of the ceramic powder and the manufacturing cost of the structural component 100. If the median particle size D50' of the ceramic powder is too large, it is not conducive to the embedding of the ceramic powder into the first alloy steel powder (i.e., the ceramic phase embedding into the steel phase) during the manufacturing of the structural component 100, thus reducing the bonding strength between the ultra-high strength part 10 and the wear-resistant part 20.

[0134] Specifically, the D90' of the ceramic powder can be, but is not limited to, 18μm, 19μm, 20μm, 21μm, 22μm, 23μm, 24μm, 25μm, etc. When the D90 particle size of the ceramic powder is within this range, the gaps formed by the accumulation of large particles in the ceramic powder can be better filled by small particles, the first alloy steel powder is more compactly packed, and the resulting ultra-high strength part 10 has higher density.

[0135] The structural component 100 of this application embodiment can be prepared by the methods described in the following embodiments of this application. In addition, it can also be prepared by other methods. The preparation methods of this application embodiment are merely one or more preparation methods of the structural component 100 of this application and should not be construed as limiting the structural component 100 provided in the embodiments of this application.

[0136] Please see Figure 4 This application provides a method for manufacturing a structural component 100, which includes:

[0137] S201 provides the first alloy steel powder;

[0138] In some embodiments, the D10 range of the first alloy steel powder is: 3μm≤D10≤10μm, the median particle size D50 range of the first alloy steel powder is: 15μm≤D50≤75μm, and the D90 range of the first alloy steel powder is: 50μm≤D90≤90μm.

[0139] Specifically, the D10 of the first alloy steel powder can be, but is not limited to, 3μm, 4μm, 5μm, 6μm, 7μm, 8μm, 9μm, 10μm, etc. When the D10 particle size of the first alloy steel powder is within this range, the first alloy steel powder can be packed more tightly, and the small particles in the first alloy steel powder can better fill the gaps between the large particles, thereby making the obtained ultra-high strength part 10 have higher density.

[0140] Specifically, the median particle size D50 of the first alloy steel powder can be, but is not limited to, 15μm, 20μm, 25μm, 30μm, 35μm, 40μm, 45μm, 50μm, 55μm, 60μm, 65μm, 70μm, 75μm, etc. In this embodiment, if the median particle size D50 of the first alloy steel powder is too small, the austenite grain size in the resulting ultra-high strength section 10 will be too large, reducing the tensile strength and yield strength of the ultra-high strength section 10. In addition, the larger grain size makes the grains more prone to slippage, reducing the plasticity of the ultra-high strength section 10. If the median particle size D50 of the first alloy steel powder is too large, the compactness of the ultra-high strength section 10 will be reduced, the porosity of the ultra-high strength section 10 will increase, and the brittleness will increase, which will also reduce the tensile strength and yield strength of the ultra-high strength section 10.

[0141] Specifically, the D90 of the first alloy steel powder can be, but is not limited to, 50μm, 55μm, 60μm, 65μm, 70μm, 75μm, 80μm, 85μm, 90μm, etc. When the D90 particle size of the first alloy steel powder is within this range, the gaps formed by the accumulation of large particles in the first alloy steel powder can be better filled by small particles, the first alloy steel powder is more compactly packed, and the resulting ultra-high strength part 10 has higher density.

[0142] For a detailed description of other aspects of the first alloy steel powder, please refer to the description of the corresponding section of the above embodiments, which will not be repeated here.

[0143] S202, providing wear-resistant powder or wear-resistant part 20;

[0144] In some embodiments, the wear-resistant powder is ceramic powder. In other embodiments, the wear-resistant powder includes ceramic powder and a second alloy steel powder.

[0145] In some embodiments, the range of D10' of the ceramic powder is: 3μm≤D10'≤5μm, the range of the median particle size D50' of the ceramic powder is: 8μm≤D50'≤15μm, and the range of D90' of the ceramic powder is: 18μm≤D90'≤25μm.

[0146] Specifically, the D10' of the ceramic powder can be, but is not limited to, 3μm, 3.5μm, 4μm, 4.5μm, 5μm, etc. When the D10 particle size of the ceramic powder is within this range, the ceramic powder can be packed more tightly, and the small particles in the ceramic powder can better fill the gaps between the large particles, thereby making the obtained ultra-high strength part 10 have higher density.

[0147] Specifically, the median particle size D50' of the ceramic powder can be, but is not limited to, 8μm, 9μm, 10μm, 11μm, 12μm, 13μm, 14μm, 15μm, etc. In this embodiment, if the median particle size D50' of the ceramic powder is too small, it increases the cost of the ceramic powder and the manufacturing cost of the structural component 100. If the median particle size D50' of the ceramic powder is too large, it is not conducive to the embedding of the ceramic powder into the first alloy steel powder (i.e., the ceramic phase embedding into the steel phase) during the manufacturing of the structural component 100, thus reducing the bonding strength between the ultra-high strength part 10 and the wear-resistant part 20.

[0148] Specifically, the D90' of the ceramic powder can be, but is not limited to, 18μm, 19μm, 20μm, 21μm, 22μm, 23μm, 24μm, 25μm, etc. When the D90 particle size of the ceramic powder is within this range, the gaps formed by the accumulation of large particles in the ceramic powder can be better filled by small particles, the first alloy steel powder is more compactly packed, and the resulting ultra-high strength part 10 has higher density.

[0149] Optionally, the average particle size of the first alloy steel powder is larger than the average particle size of the ceramic powder. In this embodiment, when the average particle size of the first alloy steel powder is larger than the average particle size of the ceramic powder, it is beneficial for the ceramic powder to embed into the first alloy steel powder during the preparation of the structural component 100. This allows the ceramic phase of the wear-resistant part 20 of the prepared structural component 100 to be better embedded into the steel phase of the ultra-high strength part 10, thereby improving the bonding strength between the ultra-high strength part 10 and the wear-resistant part 20.

[0150] For a detailed description of the wear-resistant powder and the wear-resistant part 20, please refer to the description of the corresponding part of the above embodiment, which will not be repeated here.

[0151] Understandably, when the wear-resistant part 20 is used for preparation, the wear-resistant part 20 is first prepared by ceramic powder, and then the wear-resistant part 20 is combined with the first alloy steel powder (that is, the wear-resistant part 20 is embedded in the first alloy steel powder in the form of an insert) to obtain the structural part 100.

[0152] Compared to the method of using wear-resistant powder, the method of preparing the wear-resistant part 20 by combining it with the first alloy steel powder can reduce the processing cost of the structural part 100 and improve the processing accuracy of the wear-resistant part 20. In addition, the wear-resistant part 20 undergoes densification once during sintering and hot isostatic pressing again when it is combined with the first alloy steel powder, that is, it undergoes two densification processes, thus having higher tensile strength.

[0153] S203, bringing the first alloy steel powder into contact with the wear-resistant powder or the first alloy steel powder with the wear-resistant part 20; and

[0154] Optionally, when the first alloy steel powder and the wear-resistant powder are used for preparation, the first alloy steel powder and the wear-resistant powder are placed together, with the first alloy steel powder on one side and the wear-resistant powder on the other side. That is, the first alloy steel powder and the wear-resistant powder are layered or laid in contact, but the first alloy steel powder and the wear-resistant powder are not mixed, and there will be some interlocking at the contact surface.

[0155] Optionally, when the first alloy steel powder and the wear-resistant part 20 are used for preparation, the first alloy steel powder is laid first, and then the wear-resistant part 20 is placed on one side of the first alloy steel powder, or the wear-resistant part 20 is partially embedded in the first alloy steel powder, that is, the wear-resistant part 20 is embedded in the first alloy steel powder in the form of an insert.

[0156] S204, hot isostatic pressing is performed to form an ultra-high strength part 10 from the first alloy steel powder and a wear-resistant part 20 from the wear-resistant powder, resulting in a structural component 100. The structural component 100 includes the connected ultra-high strength part 10 and the wear-resistant part 20. The ultra-high strength part 10 is made of first ultra-high strength steel. The tensile strength of the ultra-high strength part 10 is greater than the tensile strength of the wear-resistant part 20. The wear resistance of the wear-resistant part 20 is greater than the wear resistance of the ultra-high strength part 10. The tensile bonding strength between the ultra-high strength part 10 and the wear-resistant part 20 is greater than the tensile strength of the wear-resistant part 20.

[0157] Hot isostatic pressing (HIP) is a method that uses high-pressure gas as a medium to apply uniform pressure in all directions to powder or sintered blanks (or parts) to be compacted in a high-temperature, high-pressure sealed container, thereby forming a high-density blank (or part).

[0158] The densification process of the first alloy steel powder and wear-resistant powder (or the first alloy steel powder and wear-resistant part 20) in hot isostatic pressing can be divided into three stages: powder approach and rearrangement (first stage), plastic deformation (second stage), and diffusion creep (point stage). The powder particle rearrangement in the first stage plays a crucial role in the final densification of the powder. It should be noted that the thicker the sheath, the lower the degree and rate of powder densification in the first stage, and the more significant the shielding effect of the sheath on powder rearrangement. In the first stage, due to the low temperature and pressure, the yield strength of the powder particles is insufficient to induce plastic deformation. Only the pressure transmitted through the sheath causes rigid motion similar to that of a rigid body, resulting in translation or rotation of the powder particles. This causes larger bridging pores to collapse or squeezes some powder particles into adjacent voids. Because the porosity is relatively high (around 35%) in the initial stage of powder densification, the effective contact area between powder particles is small, the deformation resistance is low, and the densification rate and degree are highly dependent on the pressure transmitted by the sheath.

[0159] The structural component 100 of this application embodiment is prepared by hot isostatic pressing of a first alloy steel powder and wear-resistant powder or a first alloy steel powder and a wear-resistant part 20. The resulting structural component 100 includes an ultra-high strength part 10 and a wear-resistant part 20. The ultra-high strength part 10 and the wear-resistant part 20 are fused together during the isostatic pressing process, resulting in a high bonding strength between them. Furthermore, the size and position of the wear-resistant part 20 can be designed according to actual needs, providing better design flexibility. Moreover, the ultra-high strength part 10 and the wear-resistant part 20 of the structural component 100 can be positioned where higher wear resistance is required and where ultra-high strength is required, thereby enabling the structural component 100 to meet both ultra-high strength and good wear resistance requirements. Furthermore, by using hot isostatic pressing to prepare the structural component 100, internal defects and residual stresses in the structural component 100 during the molding process can be better eliminated. The structural component 100 can achieve nearly 100% densification, eliminating the inherent defects of conventional metal powder injection molded parts (MIM parts). At the same time, the wear-resistant powder and the first alloy steel powder are tightly bonded together through interatomic diffusion, so that the tensile bond strength between the ultra-high strength part 10 and the wear-resistant part 20 can exceed the strength of the wear-resistant part 20.

[0160] Please see Figures 5 to 8 In some embodiments, in S203, contacting the first alloy steel powder with the wear-resistant powder or with the wear-resistant part 20 includes:

[0161] S2031, a mold 10a and a sleeve 20a are provided, the mold 10a having a cavity 14a, the mold 10a being disposed within the sleeve 20a, and a first release agent being disposed between the mold 10a and the sleeve 20a, wherein the first release agent is boron nitride; and

[0162] Understandably, the sleeve 20a is arranged around the outer periphery of the mold 10a. The sleeve 20a can be, but is not limited to, a stainless steel sleeve 20a, such as a 316L stainless steel sleeve 20a.

[0163] Optionally, the thickness of the sheath 20a can range from 1 mm to 3 mm. Specifically, the thickness of the sheath 20a can be, but is not limited to, 1 mm, 1.2 mm, 1.5 mm, 1.8 mm, 2 mm, 2.2 mm, 2.5 mm, 2.8 mm, 3 mm, etc.

[0164] Optionally, a mold 10a can be set within a package 20a (e.g., Figure 8 (as shown) or multiple sets of molds 10a (e.g.) Figure 9 (As shown). For example, three to five sets of molds 10a can be set within a package 20a. Setting multiple sets of molds 10a within a package 20a simultaneously can improve the efficiency of structural component 100 fabrication and reduce the cost of structural component 100 fabrication.

[0165] S2032, the first alloy steel powder and the wear-resistant powder or the first alloy steel powder and the wear-resistant part 20 are disposed in the mold cavity, and the inner side wall of the mold 10a is provided with a second release agent, wherein the second release agent is boron nitride.

[0166] It should be noted that there is no difference in the order of S2031 and S2032. The order of S2031 and S2032 can be interchanged. In addition, other orders can be used, as long as the first alloy steel powder and the wear-resistant powder or the first alloy steel powder and the wear-resistant part 20 can be placed in the mold cavity and the mold 10a can be placed in the sleeve 20a.

[0167] In hot isostatic pressing, the sleeve 20a is a single-use product, while the mold 10a needs to be reused. In this embodiment, boron nitride is used as a release agent between the mold 10a and the sleeve 20a, and between the mold 10a and the product. This facilitates the demolding of the structural component 100 from the mold 10a, and the demolding of the mold 10a from the sleeve 20a. Removing the sleeve 20a is also easier, less likely to damage the mold 10a, and extends the service life of the mold 10a. Furthermore, boron nitride has excellent demolding properties, making demolding of the structural component 100, the mold 10a, and the sleeve 20a easier.

[0168] Please see Figure 6 and Figure 7 In some embodiments, the mold 10a includes a base plate 11a, a side plate 12a, and a top plate 13a. The side plate 12a is arranged around the outer periphery of the base plate 11a and is limitedly connected to the base plate 11a. The top plate 13a is spaced apart from the base plate 11a and is movably connected to the side plate 12a. The top plate 13a can move toward the base plate 11a. The base plate 11a, the side plate 12a, and the top plate 13a form the mold cavity 14a.

[0169] Optionally, the base plate 11a has a limiting groove 111a, and the side plate 12a is disposed in the limiting groove 111a, so that the base plate 11a and the side plate 12a are limitedly connected, and the size of the product will not change along the extension plane (i.e., X and Y directions) of the base plate 11a during hot isostatic pressing.

[0170] Optionally, the thickness of the side plate 12a is greater than the thickness of the bottom plate 11a, and the thickness of the side plate 12a is greater than the thickness of the top plate 13a. This can better prevent the side plate 12a from moving in the X and Y directions, and improve the accuracy of the structural component 100 in the X and Y directions.

[0171] Optionally, the base plate 11a, side plate 12a and top plate 13a are all made of stainless steel.

[0172] In this embodiment, the side plate 12a and the bottom plate 11a are connected in a limiting manner. This ensures that the position between the bottom plate 11a and the side plate 12a remains fixed during hot isostatic pressing, and the product dimensions do not change along the extension plane of the bottom plate 11a (i.e., the X and Y directions). Furthermore, the top plate 13a can move towards the bottom plate 11a. In the direction perpendicular to the extension plane of the bottom plate 11a (i.e., the Z direction), the product dimensions gradually decrease as the density of the product increases during hot isostatic pressing. This results in more precise dimensions of the manufactured structural component 100 in the X and Y directions, providing better design flexibility. Moreover, in subsequent processing, only the Z direction needs to be processed to obtain the structural component 100 of the preset dimensions, reducing the area to be processed later, improving the processing efficiency of the structural component 100, and lowering the processing cost of the structural component 100.

[0173] In one specific embodiment, the step of bringing the first alloy steel powder into contact with the wear-resistant powder or the first alloy steel powder into contact with the wear-resistant part 20 includes: assembling the sleeve 20a with the bottom plate 11a and side plate 12a of the mold 10a; adding the first alloy steel powder into the mold cavity 14a; filling and compacting the first alloy steel powder by ultrasonic vibration; placing the top plate 13a (the top plate 13a has a feeding channel) on the first alloy steel powder; and filling the wear-resistant powder through the feeding channel of the top plate 13a; and welding the sleeve 20a shut around its perimeter.

[0174] In another specific embodiment, the step of bringing the first alloy steel powder into contact with the wear-resistant powder or the first alloy steel powder into contact with the wear-resistant part 20 includes: assembling the bottom plate 11a and side plate 12a of the mold 10a; adding the first alloy steel powder into the mold cavity 14a; filling and compacting the first alloy steel powder by ultrasonic vibration; placing the top plate 13a (which has a feeding channel) on the first alloy steel powder; and filling the wear-resistant powder through the feeding channel of the top plate 13a; and placing the mold 10a containing the first alloy steel powder and the wear-resistant powder into the sleeve 20a, and welding the sleeve 20a shut around its perimeter.

[0175] In another specific embodiment, the step of bringing the first alloy steel powder into contact with the wear-resistant powder or the first alloy steel powder into contact with the wear-resistant part 20 includes: assembling the bottom plate 11a and side plate 12a of the mold 10a; adding the first alloy steel powder into the mold cavity 14a; filling and compacting the first alloy steel powder by ultrasonic vibration; placing the wear-resistant part 20 on the first alloy steel powder or partially embedding the wear-resistant part 20 in the first alloy steel powder; and setting the top plate 13a and placing the mold 10a inside the sleeve 20a, and welding the sleeve 20a shut around its perimeter.

[0176] In some embodiments, before hot isostatic pressing, the preparation method further includes: placing the casing 20a in a vacuum state, wherein the gas pressure inside the casing 20a is less than 0.005 Pa.

[0177] Specifically, the air inside the casing 20a is removed by vacuuming, controlling the pressure inside the casing 20a to <0.005 Pa, and the evacuation port is then welded shut to completely seal the entire casing 20a. After sealing, the casing 20a, containing the mold 10a and raw materials, is placed in water for an airtightness test. If no bubbles are generated, the casing 20a is completely sealed; if bubbles are present, rework is required. After sealing and testing, the casing is then placed in a hot isostatic pressing furnace for hot isostatic pressing.

[0178] In some embodiments, S204, the hot isostatic pressing includes:

[0179] The temperature is increased to the preset temperature T1 at a preset heating rate of 1000℃≤T1≤1200℃, and the pressure is increased to the preset pressure P at a preset pressure rate of 65Mpa≤P≤125Mpa, and then the temperature and pressure are maintained.

[0180] Understandably, the temperature T1 of hot isostatic pressing is in the range of 1000℃≤T1≤1200℃, and the pressure P of hot isostatic pressing is 65MPa≤P≤85MPa.

[0181] Optionally, during hot isostatic pressing, argon (Ar) gas is used for protection.

[0182] Specifically, the preset temperature T1 can be, but is not limited to, 1000℃, 1020℃, 1040℃, 1060℃, 1080℃, 1100℃, 1120℃, 1140℃, 1160℃, 1180℃, 1200℃, etc. If the hot isostatic pressing temperature is too low, the densification degree of the ultra-high strength part 10 and the wear-resistant part 20 of the resulting structural part 100 will be insufficient, reducing the mechanical strength of the ultra-high strength part 10 and the wear resistance of the wear-resistant part 20; if the hot isostatic pressing temperature is too high, the grain size of the steel phase of the ultra-high strength part 10 and the ceramic phase of the wear-resistant part 20 will be too large, reducing the mechanical strength of the ultra-high strength part 10 and the wear-resistant part 20.

[0183] Specifically, the preset pressure P can be, but is not limited to, 65 MPa, 68 MPa, 70 MPa, 73 MPa, 75 MPa, 78 MPa, 80 MPa, 83 MPa, 85 MPa, 90 MPa, 95 MPa, 100 MPa, 105 MPa, 110 MPa, 115 MPa, 120 MPa, 125 MPa, etc. If the hot isostatic pressing pressure is too low, the densification degree of the ultra-high strength part 10 and the wear-resistant part 20 of the structural component 100 will be insufficient, reducing the mechanical strength of the ultra-high strength part 10 and the wear resistance of the wear-resistant part 20; if the hot isostatic pressing pressure is too high, the requirements for the hot isostatic pressing furnace will increase, and may even make the hot isostatic pressing furnace unable to withstand the pressure, increasing the manufacturing cost of the structural component 100.

[0184] Optionally, the heat preservation and pressure holding time is 1 hour to 5 hours. That is, the hot isostatic pressing time is 1 hour to 5 hours. Specifically, the heat preservation and pressure holding time can be, but is not limited to, 1 hour, 1.5 hours, 2 hours, 2.5 hours, 3 hours, 3.5 hours, 4 hours, 4.5 hours, 5 hours, etc. If the hot isostatic pressing time is too short, the densification degree of the ultra-high strength part 10 and the wear-resistant part 20 of the resulting structural part 100 will be insufficient, reducing the mechanical strength of the ultra-high strength part 10 and the wear resistance of the wear-resistant part 20; if the hot isostatic pressing time is too long, the grain size of the steel phase of the ultra-high strength part 10 and the ceramic phase of the wear-resistant part 20 will be too large, reducing the mechanical strength of the ultra-high strength part 10 and the wear-resistant part 20.

[0185] In some embodiments, the preset heating rate VT1 is in the range of 2℃ / min ≤ VT1 ≤ 8℃ / min; the preset pressure rate VP1 is in the range of 0.5Mpa / min ≤ VP1 ≤ 2Mpa / min.

[0186] Specifically, the preset heating rate VT1 can be, but is not limited to, 2℃ / min, 2.5℃ / min, 3℃ / min, 3.5℃ / min, 4℃ / min, 4.5℃ / min, 5℃ / min, 5.5℃ / min, 6℃ / min, 6.5℃ / min, 7℃ / min, 7.5℃ / min, 8℃ / min, etc. If the preset heating rate VT1 is too slow, it increases the time and energy consumption of hot isostatic pressing, reduces the efficiency of the fabrication of structural component 100, and increases the fabrication cost of structural component 100. If the preset heating rate VT1 is too fast, the temperature in the hot isostatic pressing furnace is prone to unevenness, resulting in poor uniformity of performance of different parts of the manufactured product, thus reducing the performance of structural component 100. In addition, when the temperature rises too quickly, only a local area may reach the preset temperature, and the entire hot isostatic pressing furnace may not reach the preset temperature. Therefore, it is easy to stop heating before the hot isostatic pressing furnace reaches the preset temperature, resulting in hot isostatic pressing not being carried out at the set temperature, which reduces the mechanical strength of the manufactured structural component 100.

[0187] Specifically, the preset pressure increase rate VP1 can be, but is not limited to, 0.5 MPa / min, 0.6 MPa / min, 0.7 MPa / min, 0.8 MPa / min, 0.9 MPa / min, 1.0 MPa / min, 1.2 MPa / min, 1.4 MPa / min, 1.6 MPa / min, 1.8 MPa / min, 2.0 MPa / min, etc. If the preset pressure increase rate VP1 is too slow, it will reduce the efficiency of the structural component 100 and increase the manufacturing cost of the structural component 100; if the preset pressure increase rate VP1 is too fast, the pressure inside the hot isostatic pressing furnace will be uneven, and the pressure increase may stop before the preset pressure is reached, which will reduce the density of the manufactured structural component 100, or the local pressure may be too fast, exceeding the pressure limit of the hot isostatic pressing furnace, which will increase the risk of manufacturing the structural component 100.

[0188] Optionally, the heating and pressurization phases may take 200 minutes or more.

[0189] In one specific embodiment, the preset heating rate VT1 is 5℃ / min, heating to 1100℃, and the preset pressure rate VP1 is 0.5Mpa / min, pressurizing to 75Mpa, and then maintaining the temperature and pressure for 3h.

[0190] In some embodiments, after heat preservation and pressure holding, the hot isostatic pressing further includes: cooling at a preset cooling rate and depressurizing at a preset depressurization rate, wherein the preset cooling rate VT2 is in the range of 2.5℃ / min≤VT2≤6℃ / min; and the preset depressurization rate VP2 is in the range of 0.5Mpa / min≤VP2≤1Mpa / min.

[0191] Specifically, the preset cooling rate VT2 can be, but is not limited to, 2.5℃ / min, 3℃ / min, 3.5℃ / min, 4℃ / min, 4.5℃ / min, 5℃ / min, 5.5℃ / min, 6℃ / min, etc. If the preset cooling rate VT2 is too slow, it increases the time and energy consumption of hot isostatic pressing, reduces the efficiency of fabricating structural component 100, and increases the fabrication cost of structural component 100; if the preset cooling rate VT2 is too fast, the cooling rate becomes too rapid, increasing the brittleness of the fabricated structural component 100 and easily causing inhomogeneity in the performance of different parts of structural component 100.

[0192] Specifically, the preset pressure reduction rate VP2 can be, but is not limited to, 0.5 MPa / min, 0.6 MPa / min, 0.7 MPa / min, 0.8 MPa / min, 0.9 MPa / min, 1.0 MPa / min, etc. If the preset pressure reduction rate VP2 is too slow, it increases the time and energy consumption of hot isostatic pressing, reduces the efficiency of fabricating the structural component 100, and increases the fabrication cost of the structural component 100; if the preset pressure reduction rate VP2 is too fast, the fabricated structural component 100 is prone to deformation, affecting the accuracy of the fabricated structural component 100.

[0193] Optionally, after hot isostatic pressing, the preparation method further includes: removing the sheath 20a and separating the mold 10a to obtain a semi-finished product.

[0194] Optionally, the sleeve 20a is removed using a water jet cutter, avoiding the mold 10a during the removal process to prevent damage to the mold 10a; the mold 10a is then mechanically separated from the semi-finished product. The surface of the semi-finished product is then deburred by machining to remove residual mold release agents and other substances from the product surface.

[0195] Please see Figure 10 In some embodiments, after hot isostatic pressing, the preparation method further includes:

[0196] S205, undergoes heat treatment;

[0197] Understandably, after heat treatment of the semi-finished product, structural component 100 is obtained.

[0198] Please see Figure 11 Optionally, the heat treatment includes:

[0199] S2051, undergo solution treatment;

[0200] Optionally, the semi-finished product is subjected to solution treatment under negative pressure, with the gas pressure of the solution treatment ≤0.1 kPa. In this embodiment, solution treatment is performed after hot isostatic pressing, which allows the impurity elements and impurity phases corresponding to the ultra-high strength part 10 of the semi-finished product to be dissolved in the iron matrix, so that the material is completely transformed into austenite in the high-temperature heat preservation section of the solution treatment, thereby improving the toughness of the ultra-high strength part 10.

[0201] Please see Figure 12 Optionally, the solution treatment includes:

[0202] S2051a undergoes a first-stage solution treatment at a temperature of 180℃ to 220℃;

[0203] Optionally, the temperature is increased at a rate of 5°C / min to 8°C / min, and held at 180°C to 220°C for 25 min to 35 min to perform the first stage of solution treatment.

[0204] Specifically, the temperature of the first stage of solution treatment can be, but is not limited to, 180℃, 185℃, 190℃, 195℃, 200℃, 205℃, 210℃, 215℃, 220℃, etc.

[0205] Specifically, the heating rate of the first stage of solution treatment can be, but is not limited to, 5℃ / min, 5.5℃ / min, 6℃ / min, 6.5℃ / min, 7℃ / min, 7.5℃ / min, 8℃ / min, etc.

[0206] In one specific embodiment, the temperature is raised to 200°C in 30 minutes and held for 30 minutes to perform the first stage of solution treatment.

[0207] In this embodiment, the first stage of solution treatment is carried out at 180°C to 220°C. This avoids the temperature from rising rapidly to the target value and prevents uneven temperature in the furnace cavity, resulting in better overall temperature consistency in the furnace cavity. Consequently, the ultra-high strength part 10 obtained in the end has better comprehensive performance.

[0208] S2051b, subjected to a second-stage solution treatment at a temperature of 580°C to 620°C; and

[0209] Optionally, the temperature is increased at a rate of 11°C / min to 16°C / min, and held at 580°C to 620°C for 15 min to 25 min to perform the second stage of solution treatment.

[0210] Specifically, the temperature of the second stage solution treatment can be, but is not limited to, 580℃, 585℃, 590℃, 595℃, 600℃, 605℃, 610℃, 615℃, 620℃, etc.

[0211] Specifically, the heating rate of the second stage solution treatment can be, but is not limited to, 11℃ / min, 12℃ / min, 13℃ / min, 14℃ / min, 15℃ / min, 16℃ / min, etc.

[0212] In one specific embodiment, the temperature is increased from 200°C to 600°C in 30 minutes and held for 20 minutes to perform the second stage of solution treatment.

[0213] Because the austenite transformation onset temperature of the material is 600°C and the austenite transformation end temperature is approximately 750°C, in this embodiment, a second-stage solution treatment is performed at 580°C to 620°C to ensure a more complete austenite transformation. Furthermore, by controlling the heating rate of the second-stage solution treatment to 11°C / min to 16°C / min, the transformation speed can be better promoted by controlling the material's internal driving force, while preventing grain growth that could affect the tensile strength, yield strength, and toughness of the final ultra-high strength portion 10. A heating rate that is too slow or a holding time that is too long can easily lead to increased grain size.

[0214] S2051c undergoes a third-stage solution treatment at temperatures ranging from 920°C to 1040°C.

[0215] Optionally, the temperature is increased at a rate of 10°C / min to 15°C / min, and then held at 920°C to 1040°C for 50 min to 70 min.

[0216] Specifically, the temperature of the third stage solution treatment can be, but is not limited to, 920℃, 930℃, 940℃, 950℃, 960℃, 970℃, 980℃, 990℃, 1000℃, 1010℃, 1020℃, 1030℃, 1040℃, etc.

[0217] Specifically, the heating rate of the third stage solution treatment can be, but is not limited to, 10℃ / min, 10.6℃ / min, 11℃ / min, 12℃ / min, 13℃ / min, 14℃ / min, 14.67℃ / min, 15℃ / min, etc.

[0218] In one specific embodiment, the temperature is increased from 600°C to 960°C in 30 minutes and held for 60 minutes to perform the third stage of solution treatment.

[0219] In this embodiment, a third-stage solution treatment at 920°C to 1040°C allows the material to be completely transformed into austenite, and enables impurity elements and phases to dissolve better in the iron matrix after sintering. This results in the final ultra-high strength portion 10 exhibiting better tensile strength, yield strength, and plasticity. Furthermore, by controlling the heating rate of the third-stage solution treatment to 10°C / min to 15°C / min, the internal driving force of the material can be better controlled to promote the transformation speed while preventing grain growth that could affect the tensile strength, yield strength, and toughness of the final ultra-high strength portion 10. A heating rate that is too slow or a holding time that is too long can easily lead to increased grain size.

[0220] Optionally, after the third solution treatment, the solution treatment further includes:

[0221] S2051d, rapidly cooled to room temperature.

[0222] Optionally, liquid nitrogen is used for rapid cooling to bring the semi-finished product to room temperature. In this embodiment, rapid cooling allows most of the austenite in the material to transform into lath martensite, resulting in the final ultra-high strength part 10 having better tensile strength, yield strength, and toughness.

[0223] S2052, undergoes cryogenic treatment; and

[0224] Optionally, liquid nitrogen is used to perform cryogenic treatment on the semi-finished product after solution treatment, so that the temperature of the semi-finished product is reduced to -196°C to -180°C.

[0225] Specifically, the temperature for cryogenic treatment can be, but is not limited to, -180℃, -183℃, -185℃, -188℃, -190℃, -193℃, and -196℃.

[0226] Optionally, the holding time for cryogenic treatment can be from 20 min to 90 min. Specifically, the holding time for cryogenic treatment can be, but is not limited to, 20 min, 30 min, 40 min, 50 min, 60 min, 70 min, 80 min, 90 min, etc.

[0227] Since the martensitic transformation endpoint temperature of the material system in this embodiment is below zero degrees Celsius, it cannot be completely transformed into full martensite at room temperature. Therefore, deep cryogenic treatment of the semi-finished product after solution treatment can increase the content of lath martensite in the product, so that the content of lath martensite in the product can be increased to more than 99.5 wt%, thereby making the final ultra-high strength part 10 have better tensile strength, yield strength and toughness.

[0228] S2053, timeliness processing.

[0229] In this embodiment, after cryogenic treatment, aging treatment is performed, which allows precipitates to form between the grain boundaries of the material. By forming dislocations at the grain boundaries, the resistance to slippage between the grain boundaries is increased, and the strength of the material is also increased. In addition, during the aging strengthening process, some lath martensite will undergo reverse transformation into austenite. By adjusting the reverse transformation into austenite, the tensile strength, yield strength and plasticity of the ultra-high strength part 10 are adjusted.

[0230] Please see Figure 13 Optionally, timeliness processing may be performed, including:

[0231] S2053a, subjected to a first stage of aging treatment at a temperature of 180°C to 220°C; and

[0232] Optionally, the temperature is increased at a rate of 5°C / min to 8°C / min, and then held at 180°C to 220°C for 25 min to 35 min to perform the first stage of aging treatment.

[0233] Specifically, the temperature for the first stage of aging treatment can be, but is not limited to, 180℃, 185℃, 190℃, 195℃, 200℃, 205℃, 210℃, 215℃, 220℃, etc.

[0234] Specifically, the heating rate of the first stage of aging treatment can be, but is not limited to, 5℃ / min, 5.5℃ / min, 6℃ / min, 6.5℃ / min, 7℃ / min, 7.5℃ / min, 8℃ / min, etc.

[0235] In one specific embodiment, the temperature is raised to 200°C in 30 minutes and held for 30 minutes to perform the first stage of aging treatment.

[0236] S2053b undergoes a second stage of aging treatment at temperatures ranging from 460°C to 540°C.

[0237] Optionally, the temperature is increased at a rate of 8°C / min to 12°C / min, and then held at 460°C to 540°C for 3 to 5 hours for the second stage of aging treatment.

[0238] Specifically, the temperature for the second stage of aging treatment can be, but is not limited to, 460℃, 470℃, 480℃, 490℃, 500℃, 510℃, 520℃, 530℃, 540℃, etc.

[0239] Specifically, the heating rate of the second aging treatment can be, but is not limited to, 8℃ / min, 8.5℃ / min, 9℃ / min, 9.5℃ / min, 10℃ / min, 10.5℃ / min, 11℃ / min, 11.5℃ / min, 12℃ / min, etc.

[0240] In one specific embodiment, the temperature is increased from 200°C to 500°C in 30 minutes and held for 4 hours to perform the second stage of aging treatment.

[0241] It should be noted that both the first and second stages of aging treatment were carried out under an environment with a pressure ≤0.1 kPa.

[0242] Optionally, after performing the second stage of timeliness processing, the timeliness processing further includes:

[0243] S2053c, rapidly cooled to room temperature.

[0244] Optionally, liquid nitrogen is used for rapid cooling to room temperature to obtain structural component 100.

[0245] In this embodiment, the temperature is first raised to 180°C to 220°C for the first stage of aging treatment, and then raised to 460°C to 540°C for the second stage of aging treatment. This makes the temperature inside the furnace cavity more uniform, which is beneficial to improving the tensile strength, yield strength and toughness of the ultra-high strength part 10.

[0246] In some embodiments, the preparation method further includes: performing computer numerical control (CNC) machining, polishing, and other processing on the structural component 100 to remove surface burrs and control the roughness of the structural component 100. A coating treatment may also be performed to improve the wear resistance of the material.

[0247] The structural component 100 of this application embodiment will be further described below through specific embodiments.

[0248] Example 1

[0249] Foldable devices, such as the hinge of a foldable phone, require high reliability, miniaturization, strength, and wear resistance due to space constraints. If the hinge wears easily, it will cause significant torque loss, affecting the user experience. Therefore, this embodiment uses the hinge of a foldable device as an example. The slide rail area of ​​the hinge needs high wear resistance, and this area is designated as the wear-resistant part 20; other areas need high strength, and this area is designated as the ultra-high strength part 10.

[0250] The structural component 100 of this embodiment is prepared through the following steps:

[0251] (1) Provide a first alloy steel powder, the main components of which include: 18.2% Ni, 14.8% Co, 6.5% Mo, 0.61% V, 0.21% C, 0.03% S, 0.25% Si, 0.08% Mn, 0.32% Cr, and the balance Fe; the first alloy steel powder has a D10 of 8.14 μm, a D50 of 39.3 μm, and a D90 of 61.2 μm;

[0252] (2) Provide wear-resistant powder, wherein the wear-resistant powder is silicon carbide, the D10' of silicon carbide is 3.11 μm, the D50' of silicon carbide is 10.3 μm, and the D90' of silicon carbide is 21.25 μm;

[0253] (3) Provide mold 10a and sleeve 20a according to the shape of structural component 100. Sleeve 20a is 316L stainless steel with a thickness of 1mm.

[0254] (4) Assemble the mold 10a and the sleeve 20a, add the first alloy steel powder into the mold 10a, and use ultrasonic vibration to fill the first alloy steel powder. Then, add wear-resistant powder and weld the mold 10a and the sleeve 20a together.

[0255] (5) Evacuate the air to ensure that the pressure inside the 20a casing is less than 0.005pa, and seal the evacuation port to check the airtightness.

[0256] (6) Heat to 1100℃ at 5℃ / min, pressurize to 75MPa at 0.5MPa / min, and hold for 3 hours; then cool down at 4℃ / min and depressurize at 0.6MPa / min.

[0257] (7) Remove the packaging 20a and the mold 10a to obtain the semi-finished product;

[0258] (8) At a pressure 0.1 kPa lower than the pressure, the temperature is raised to 200°C in 30 min and held for 30 min to carry out the first stage of solid solution treatment; the temperature is raised from 200°C to 600°C in 30 min and held for 20 min to carry out the second stage of solid solution treatment; the temperature is raised from 600°C to 960°C in 30 min and held for 60 min to carry out the third stage of solid solution treatment; then the liquid nitrogen is used to rapidly cool to room temperature;

[0259] (9) Use liquid nitrogen to rapidly cool to -196℃ for cryogenic treatment;

[0260] (10) Heat to 200℃ in 30 min and hold for 30 min for the first stage of aging treatment; heat from 200℃ to 500℃ in 30 min and hold for 4 h for the second stage of aging treatment; cool rapidly to room temperature with liquid nitrogen to obtain structural component 100.

[0261] The structural component 100 prepared in this embodiment was subjected to hardness and tensile bond strength tests. The microhardness of the ultra-high strength part 10 of the structural component 100 in this embodiment is 581 HV (averaged by three measurements, the three measurements are 583 HV, 592 HV, and 568 HV respectively), and the Mohs hardness of the wear-resistant part 20 is 9.26 (averaged by three measurements, the three measurements are 9.12, 9.34, and 9.33 respectively).

[0262] The structural component 100 prepared in this embodiment was subjected to tensile strength test using a standard component in the furnace. The fracture occurred in the wear-resistant part 20 area, exhibiting brittle fracture.

[0263] The material and method used in this embodiment are used to prepare the following: Figure 14 The tensile bar (half of which is an ultra-high strength part 10 and the other half is a wear-resistant part 20) was subjected to a tensile test, and the tensile strength was found to be 380 MPa. The fracture location of the structural component 100 was in the wear-resistant part 20 area.

[0264] Example 2

[0265] The structural component 100 of this embodiment is prepared through the following steps:

[0266] (1) Provide a first alloy steel powder, the main components of which include: 18.2% Ni, 14.8% Co, 6.5% Mo, 0.61% V, 0.21% C, 0.03% S, 0.25% Si, 0.08% Mn, 0.32% Cr, and the balance Fe; the first alloy steel powder has a D10 of 8.14 μm, a D50 of 39.3 μm, and a D90 of 61.2 μm;

[0267] (2) Provide wear-resistant powder, wherein the wear-resistant powder is silicon carbide and second alloy steel powder, wherein the mass fraction of silicon carbide in the wear-resistant powder is 16%, the D10' of silicon carbide is 8.12μm, the D50' of silicon carbide is 23.2μm, the D90' of silicon carbide is 32.25μm, and the second alloy steel powder is the same as the first alloy steel powder;

[0268] (3) Provide mold 10a and sleeve 20a according to the shape of structural component 100. Sleeve 20a is 316L stainless steel with a thickness of 1mm.

[0269] (4) Assemble the mold 10a and the sleeve 20a, add the first alloy steel powder into the mold 10a, and use ultrasonic vibration to fill the first alloy steel powder. Then, add wear-resistant powder and weld the mold 10a and the sleeve 20a together.

[0270] (5) Evacuate the air to ensure that the pressure inside the 20a casing is less than 0.005pa, and seal the evacuation port to check the airtightness.

[0271] (6) Heat to 1100℃ at 5℃ / min, pressurize to 75MPa at 0.5MPa / min, and hold for 3 hours; then cool down at 4℃ / min and depressurize at 0.6MPa / min.

[0272] (7) Remove the packaging 20a and the mold 10a to obtain the semi-finished product;

[0273] (8) At a pressure 0.1 kPa lower than the pressure, the temperature is raised to 200°C in 30 min and held for 30 min to carry out the first stage of solid solution treatment; the temperature is raised from 200°C to 600°C in 30 min and held for 20 min to carry out the second stage of solid solution treatment; the temperature is raised from 600°C to 960°C in 30 min and held for 60 min to carry out the third stage of solid solution treatment; then the liquid nitrogen is used to rapidly cool to room temperature;

[0274] (9) Use liquid nitrogen to rapidly cool to -196℃ for cryogenic treatment;

[0275] (10) Heat to 200℃ in 30 min and hold for 30 min for the first stage of aging treatment; heat from 200℃ to 500℃ in 30 min and hold for 4 h for the second stage of aging treatment; cool rapidly to room temperature with liquid nitrogen to obtain structural component 100.

[0276] The structural component 100 prepared in this embodiment was subjected to hardness and tensile bond strength tests. The microhardness of the ultra-high strength part 10 of the structural component 100 in this embodiment is 596.7 HV (averaged by three measurements, the three measurement results are 579 HV, 612 HV, and 599 HV respectively), and the Mohs hardness of the wear-resistant part 20 is 576.3 HV (averaged by three measurements, the three measurement results are 581 HV, 56 HV, and 562 HV respectively).

[0277] The structural component 100 prepared in this embodiment was subjected to tensile strength test using a standard component in the furnace. The fracture occurred in the wear-resistant part 20 area, exhibiting brittle fracture.

[0278] The material and method used in this embodiment are used to prepare the following: Figure 14 The tensile bar was subjected to a tensile test, and the tensile strength was found to be 1120 MPa. The fracture location of structural component 100 was in the wear-resistant part 20 area.

[0279] As can be seen from the test results of Examples 1 and 2, the structural component 100 of this application has high tensile strength and high hardness, and high wear resistance. Compared with the structural component 100 of Example 1, the structural component 100 of Example 2 has higher tensile strength, but the wear resistance of Example 2 is weaker than that of Example 1.

[0280] Example 3

[0281] The structural component 100 of this embodiment is prepared through the following steps:

[0282] (1) Provide a first alloy steel powder, the main components of which include: 18.5% Ni, 14.4% Co, 7.1% Mo, 0.75% V, 0.18% C, 0.03% S, 0.25% Si, 0.08% Mn, 0.32% Cr, and the balance Fe; the first alloy steel powder has a D10 of 7.82 μm, a D50 of 34 μm, and a D90 of 53.51 μm;

[0283] (2) A wear-resistant part 20 is provided, the material of the wear-resistant part 20 is silicon carbide;

[0284] (3) Provide mold 10a and sleeve 20a according to the shape of structural component 100. Sleeve 20a is 316L stainless steel with a thickness of 1mm.

[0285] (4) Assemble the mold 10a and the sleeve 20a, add the first alloy steel powder into the mold 10a, and use ultrasonic vibration to fill the first alloy steel powder. Then put in the wear-resistant part 20 and weld the mold 10a and the sleeve 20a together.

[0286] (5) Evacuate the air to ensure that the pressure inside the 20a casing is less than 0.005pa, and seal the evacuation port to check the airtightness.

[0287] (6) Heat to 1100℃ at 5℃ / min, pressurize to 75MPa at 0.5MPa / min, and hold for 3 hours; then cool down at 4℃ / min and depressurize at 0.6MPa / min.

[0288] (7) Remove the packaging 20a and the mold 10a to obtain the semi-finished product;

[0289] (8) At a pressure 0.1 kPa lower than the pressure, the temperature is raised to 200°C in 30 min and held for 30 min to carry out the first stage of solid solution treatment; the temperature is raised from 200°C to 600°C in 30 min and held for 20 min to carry out the second stage of solid solution treatment; the temperature is raised from 600°C to 960°C in 30 min and held for 60 min to carry out the third stage of solid solution treatment; then the liquid nitrogen is used to rapidly cool to room temperature;

[0290] (9) Use liquid nitrogen to rapidly cool to -196℃ for cryogenic treatment;

[0291] (10) Heat to 200℃ in 30 min and hold for 30 min for the first stage of aging treatment; heat from 200℃ to 500℃ in 30 min and hold for 4 h for the second stage of aging treatment; cool rapidly to room temperature with liquid nitrogen to obtain structural component 100.

[0292] The structural component 100 prepared in this embodiment was subjected to hardness and tensile bond strength tests. The microhardness of the ultra-high strength part 10 of the structural component 100 in this embodiment is 582.3 HV (averaged by three measurements, the three measurements are 575 HV, 583 HV, and 589 HV respectively), and the Mohs hardness of the wear-resistant part 20 is 9.39 (averaged by three measurements, the three measurements are 9.21, 9.45, and 9.51 respectively).

[0293] The structural component 100 prepared in this embodiment was subjected to tensile strength test using a standard component in the furnace. The fracture occurred in the wear-resistant part 20 area, exhibiting brittle fracture.

[0294] The material and method used in this embodiment are used to prepare the following: Figure 14 The tensile bar was subjected to a tensile test, and the tensile strength was found to be 450 MPa. The fracture location of the structural component 100 was in the wear-resistant part 20 area.

[0295] Example 4

[0296] The structural component 100 of this embodiment is prepared through the following steps:

[0297] (1) Provide a first alloy steel powder, the main components of which include: 18.5% Ni, 14.4% Co, 7.1% Mo, 0.75% V, 0.18% C, 0.03% S, 0.25% Si, 0.08% Mn, 0.32% Cr, and the balance Fe; the first alloy steel powder has a D10 of 7.82 μm, a D50 of 34 μm, and a D90 of 53.51 μm;

[0298] (2) A wear-resistant part 20 is provided, the material of the wear-resistant part 20 being tungsten carbide;

[0299] (3) Provide mold 10a and sleeve 20a according to the shape of structural component 100. Sleeve 20a is 316L stainless steel with a thickness of 1mm.

[0300] (4) Assemble the mold 10a and the sleeve 20a, add the first alloy steel powder into the mold 10a, and use ultrasonic vibration to fill the first alloy steel powder. Then put in the wear-resistant part 20 and weld the mold 10a and the sleeve 20a together.

[0301] (5) Evacuate the air to ensure that the pressure inside the 20a casing is less than 0.005pa, and seal the evacuation port to check the airtightness.

[0302] (6) Heat to 1100℃ at 5℃ / min, pressurize to 75MPa at 0.5MPa / min, and hold for 3 hours; then cool down at 4℃ / min and depressurize at 0.6MPa / min.

[0303] (7) Remove the packaging 20a and the mold 10a to obtain the semi-finished product;

[0304] (8) At a pressure 0.1 kPa lower than the pressure, the temperature is raised to 200°C in 30 min and held for 30 min to carry out the first stage of solid solution treatment; the temperature is raised from 200°C to 600°C in 30 min and held for 20 min to carry out the second stage of solid solution treatment; the temperature is raised from 600°C to 960°C in 30 min and held for 60 min to carry out the third stage of solid solution treatment; then the liquid nitrogen is used to rapidly cool to room temperature;

[0305] (9) Use liquid nitrogen to rapidly cool to -196℃ for cryogenic treatment;

[0306] (10) Heat to 200℃ in 30 min and hold for 30 min for the first stage of aging treatment; heat from 200℃ to 500℃ in 30 min and hold for 4 h for the second stage of aging treatment; cool rapidly to room temperature with liquid nitrogen to obtain structural component 100.

[0307] The structural component 100 prepared in this embodiment was subjected to hardness and tensile bond strength tests. The microhardness of the ultra-high strength part 10 of the structural component 100 in this embodiment is 582.3 HV (averaged by three measurements, the three measurements are 575 HV, 583 HV, and 589 HV respectively), and the Mohs hardness of the wear-resistant part 20 is 8.56 (averaged by three measurements, the three measurements are 8.78, 8.45, and 8.46 respectively).

[0308] The structural component 100 prepared in this embodiment was subjected to tensile strength test using a standard component in the furnace. The fracture occurred in the wear-resistant part 20 area, exhibiting brittle fracture.

[0309] The material and method used in this embodiment are used to prepare the following: Figure 14 The tensile bar was subjected to a tensile test, and the tensile strength was found to be 380 MPa. The fracture location of the structural component 100 was in the wear-resistant part 20 area.

[0310] Please see Figure 15 and Figure 16 This application also provides an electronic device 300, which includes a display screen 310, a processor 330, and the structural component 100 described in this application. The processor 330 is electrically connected to the display screen 310 and is used to control the display screen 310 to display.

[0311] For a detailed description of other aspects of structural component 100, please refer to the description of the corresponding part of the above embodiment, which will not be repeated here.

[0312] Optionally, the structural member 100 serves as a force-bearing member of the electronic device 300.

[0313] The electronic device 300 in this application embodiment can be, but is not limited to, a mobile phone, a foldable mobile phone, a tablet computer, a foldable tablet computer, a laptop computer, a desktop computer, a smart bracelet, a smartwatch, smart glasses, an e-reader, a game console, and other portable electronic devices 300. The electronic device 300 described in this embodiment is merely one form of the electronic device 300 used in the structural component 100. In the figures, the electronic device 300 is illustrated using a foldable electronic device 300 as an example, and the structural component 100 is illustrated using the hinge of the foldable electronic device 300 as an example. This should not be construed as a limitation on the electronic device 300 provided in this application, nor should it be construed as a limitation on the structural component 100 provided in the various embodiments of this application.

[0314] Optionally, the display screen 310 can be a flat display screen or a flexible display screen. Optionally, the display screen 310 can be, but is not limited to, one or more of the following: liquid crystal display screen, light-emitting diode display screen (LED display screen), micro light-emitting diode display screen (Micro LED display screen), mini LED display screen, organic light-emitting diode display screen (OLED display screen).

[0315] Optionally, processor 330 includes one or more general-purpose processors, wherein the general-purpose processor can be any type of device capable of processing electronic instructions, including a central processing unit (CPU), microprocessor, microcontroller, main processor, controller, and ASIC, etc. Processor 330 is used to execute various types of digital storage instructions, such as software or firmware programs stored in memory, which enables the computing device to provide a wide range of services.

[0316] Optionally, the electronic device 300 of this application further includes a foldable mechanism 320, which includes a pivot 321, and the pivot 321 is the structural component 100 of the embodiment of this application.

[0317] Optionally, the electronic device 300 of this application further includes a memory 350 and a camera module 370. The memory 350 is electrically connected to the processor 330 and is used to store the program code required for the processor 330 to run, the program code required to control the display screen 310, the display content of the display screen 310, etc. The camera module 370 is electrically connected to the processor 330 and is used to take pictures under the control of the processor 330.

[0318] Optionally, memory 350 may include volatile memory, such as random access memory (RAM); memory 350 may also include non-volatile memory (NVM), such as read-only memory (ROM), flash memory (FM), hard disk drive (HDD), or solid-state drive (SSD). Memory 350 may also include combinations of the above types of memory.

[0319] In this application, the terms "embodiment" and "implementation" mean that a specific feature, structure, or characteristic described in connection with an embodiment can be included in at least one embodiment of this application. The appearance of these phrases in various locations throughout the specification does not necessarily refer to the same embodiment, nor are they independent or alternative embodiments mutually exclusive with other embodiments. Those skilled in the art will understand, explicitly and implicitly, that the embodiments described in this application can be combined with other embodiments. Furthermore, it should be understood that the features, structures, or characteristics described in the various embodiments of this application can be arbitrarily combined to form yet another embodiment that does not depart from the spirit and scope of the technical solution of this application, provided there is no contradiction between them.

[0320] Finally, it should be noted that the above embodiments are only used to illustrate the technical solutions of this application and are not intended to limit it. Although this application has been described in detail with reference to the above preferred embodiments, those skilled in the art should understand that modifications or equivalent substitutions to the technical solutions of this application should not depart from the spirit and scope of the technical solutions of this application.

Claims

1. A structural member, characterized by, The structural component includes: The ultra-high strength section, wherein the material of the ultra-high strength section is a first ultra-high strength steel; and The wear-resistant part is connected to the ultra-high strength part. The tensile strength of the ultra-high strength part is greater than that of the wear-resistant part. The wear resistance of the wear-resistant part is greater than that of the ultra-high strength part. The tensile bond strength between the ultra-high strength part and the wear-resistant part is greater than that of the wear-resistant part.

2. The structural member of claim 1, wherein The tensile strength of the wear-resistant part ranges from 300 MPa to 1500 MPa.

3. The structural member of claim 1, wherein The first ultra-high strength steel comprises, by mass fraction: 16% to 19% nickel; 14% to 17% cobalt; 5% to 8% molybdenum; 0.2% to 0.4% chromium; Less than or equal to 1% vanadium; and The remaining amount of iron.

4. The structural member of claim 1, wherein The tensile strength of the ultra-high strength part ranges from 1900 MPa to 2200 MPa; the yield strength of the ultra-high strength part ranges from 1600 MPa to 1800 MPa; the elongation of the ultra-high strength part ranges from 4% to 10%; the modulus of the ultra-high strength part ranges from 170 GPa to 200 GPa; and the microhardness of the ultra-high strength part ranges from 560 HV to 650 HV.

5. The structural member of claim 1, wherein The wear-resistant part is made of ceramic material; or, The wear-resistant part is made of a second ultra-high strength steel and ceramic material. In the wear-resistant part, the mass fraction of the ceramic material ranges from 5% to 18%, and the mass fraction of the second ultra-high strength steel ranges from 82% to 95%.

6. The structural member of claim 1, wherein The wear-resistant part is made of ceramic material, and the Mohs hardness of the wear-resistant part ranges from 7.5 to 9.

8. or, The wear-resistant part is made of a second ultra-high strength steel and ceramic materials, and the microhardness of the wear-resistant part ranges from 560HV to 650HV.

7. The structural member of claim 1, wherein The raw material components of the ultra-high strength section include a first alloy steel powder, and the raw material components of the wear-resistant section include ceramic powder, or ceramic powder and a second alloy steel powder, wherein the average particle size of the first alloy steel powder is greater than the average particle size of the ceramic powder.

8. The structural member of claim 7, wherein The first alloy steel powder has a D10 range of 3μm≤D10≤10μm, a median particle size D50 range of 15μm≤D50≤75μm, and a D90 range of 50μm≤D90≤90μm; the ceramic powder has a D10' range of 3μm≤D10'≤5μm, a median particle size D50' range of 8μm≤D50'≤15μm, and a D90' range of 18μm≤D90'≤25μm.

9. The structural member of claim 5, wherein The ceramic material includes at least one of silicon carbide, tungsten carbide, alumina, and zirconium oxide.

10. A method of producing a structural member, characterized by, include: Provide first alloy steel powder; Provide wear-resistant powder or wear-resistant components; The first alloy steel powder is brought into contact with the wear-resistant powder or the first alloy steel powder is brought into contact with the wear-resistant part. as well as Hot isostatic pressing is performed to form an ultra-high strength section from the first alloy steel powder and a wear-resistant section from the wear-resistant powder, resulting in a structural component. The structural component includes a connected ultra-high strength section and a wear-resistant section. The ultra-high strength section is made of first ultra-high strength steel. The tensile strength of the ultra-high strength section is greater than the tensile strength of the wear-resistant section. The wear resistance of the wear-resistant section is greater than that of the ultra-high strength section. The tensile bond strength between the ultra-high strength section and the wear-resistant section is greater than the tensile strength of the wear-resistant section.

11. The method of producing a structural member according to claim 10, wherein The hot isostatic pressing process includes: The temperature is increased to the preset temperature T1 at a preset heating rate of 1000℃≤T1≤1200℃, and the pressure is increased to the preset pressure P at a preset pressure rate of 65Mpa≤P≤125Mpa, and then the temperature and pressure are maintained.

12. The method for manufacturing a structural component according to claim 11, characterized in that, The preset heating rate VT1 is in the range of 2℃ / min ≤ VT1 ≤ 8℃ / min; the preset pressure rate VP1 is in the range of 0.5Mpa / min ≤ VP1 ≤ 2Mpa / min.

13. The method for preparing the structural component according to claim 10, characterized in that, After heat preservation and pressure holding, the hot isostatic pressing further includes: cooling at a preset cooling rate and depressurizing at a preset depressurization rate, wherein the preset cooling rate VT2 is in the range of 2.5℃ / min≤VT2≤6℃ / min; and the preset depressurization rate VP2 is in the range of 0.5Mpa / min≤VP2≤1Mpa / min.

14. The method for manufacturing a structural component according to claim 10, characterized in that, The step of bringing the first alloy steel powder into contact with the wear-resistant powder or the first alloy steel powder into contact with the wear-resistant part includes: A mold and a housing are provided, the mold having a cavity, the mold being disposed within the housing, and a first release agent, wherein the first release agent is boron nitride, being disposed between the mold and the housing; and The first alloy steel powder and the wear-resistant powder or the first alloy steel powder and the wear-resistant part are disposed in the mold cavity, and a second release agent is disposed on the inner side wall of the mold, wherein the second release agent is boron nitride.

15. The method for manufacturing a structural component according to claim 14, characterized in that, The mold includes a base plate, side plates, and a top plate. The side plates are arranged around the outer periphery of the base plate and are connected to the base plate in a limiting manner. The top plate is spaced apart from the base plate and is movably connected to the side plates. The top plate can move toward the base plate. The base plate, side plates, and top plate form the mold cavity.

16. The method for manufacturing a structural component according to any one of claims 10-15, characterized in that, After hot isostatic pressing, the preparation method further includes: heat treatment; The heat treatment includes: solution treatment, cryogenic treatment and aging treatment in sequence.

17. The method for manufacturing a structural component according to any one of claims 10-15, characterized in that, The wear-resistant powder includes ceramic powder, wherein the average particle size of the first alloy steel powder is larger than the average particle size of the ceramic powder; the D10 range of the first alloy steel powder is: 3μm≤D10≤10μm, the median particle size D50 range of the first alloy steel powder is: 15μm≤D50≤75μm, and the D90 range of the first alloy steel powder is: 50μm≤D90≤90μm; the D10' range of the ceramic powder is: 3μm≤D10'≤5μm, the median particle size D50' range of the ceramic powder is: 8μm≤D50'≤15μm, and the D90' range of the ceramic powder is: 18μm≤D90'≤25μm.

18. An electronic device, characterized in that, include: Display screen; A processor, electrically connected to the display screen, is used to control the display screen to perform a display. as well as The structural component as described in any one of claims 1-9 or the structural component as described in any one of claims 10-17 is prepared by the same method.

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