Stainless steel wire for metal rubber, preparation method of stainless steel wire and metal rubber molded part

Abstract

The invention belongs to the technical field of metal rubber, and relates to a stainless steel wire for metal rubber, a preparation method of the stainless steel wire and a metal rubber molded part, the preparation method comprises the following steps: S1, smelting by adopting an electric arc furnace, an argon-oxygen decarburization furnace and a ladle refining furnace, carrying out manganese-nitrogen alloying in the smelting process, and then carrying out continuous casting to obtain a casting blank; s2, the casting blank is heated and then subjected to hot rolling, and a wire rod is obtained and then cooled; s3, the wire rod is drawn, and then hydrogen bright annealing is conducted; the drawing and annealing processes are repeated until the steel wire with the target size is obtained; and S4, the surface of the drawn steel wire is ground and polished, and the stainless steel wire is obtained. Through combination of manganese-nitrogen alloying, repeated drawing and intermediate heat treatment processes and surface finishing, it is ensured that the steel wire has high strength and high surface quality, the plasticity of the steel wire is improved, and the steel wire can be finally made into a metal rubber formed part with excellent fatigue performance.

Description

Technical Field

[0001] This invention belongs to the field of metal rubber technology, and relates to a stainless steel wire for metal rubber, its preparation method, and metal rubber molded parts. Background Technology

[0002] Metal rubber is a homogeneous, porous, elastic network material made from metal wires through processes such as winding, weaving, and compression molding. The helical network structure distributed within metal rubber is similar to the spatial network structure of rubber polymers. When subjected to loads, this structure dissipates energy through heat generated by dry friction between the metal wires, thus acting as a damping agent. Therefore, metal rubber combines the elastic characteristics of rubber with the excellent properties of metals, such as resistance to high and low temperatures, corrosion resistance, and fatigue resistance. It overcomes the shortcomings of traditional polymer rubbers, such as easy aging and intolerance to extreme environments, and has wide applications in aerospace, military equipment, marine engineering, and many other fields.

[0003] The performance and fatigue life of metal rubber largely depend on the comprehensive properties of its raw material, the metal wire. Currently, austenitic stainless steel wires such as 304 and 321 are commonly used as raw materials in the preparation of metal rubber in China. During the drawing and deformation process, the austenitic lattice inside these metastable austenitic stainless steel wires slips, twists, and transforms into hard and brittle deformed martensite. Relying on this leap in strength and hardness brought about by the martensitic phase transformation, these steel wires can meet the performance requirements of metal rubber for high strength and efficient energy dissipation.

[0004] However, after undergoing significant drawing deformation, most of the steel wire's microstructure transforms into martensite, leading to a marked decrease in the wire's plasticity and severely impacting the fatigue properties of both the steel wire and the metal rubber. Stainless steel wires produced using conventional drawing methods have poor surface quality, making them more prone to wear marks due to friction during use with the metal rubber, easily triggering fatigue cracks and ultimately causing wire breakage, thus reducing the fatigue performance of the metal rubber.

[0005] Therefore, there is an urgent need to develop a systematic and mature technology to prepare stainless steel wires with high strength, high plasticity, and high surface quality for use in metal rubber, thereby improving the fatigue resistance of metal rubber molded parts. Summary of the Invention

[0006] In view of the above-mentioned shortcomings in the prior art, the purpose of this invention is to provide a stainless steel wire for metal rubber, a method for preparing the same, and a metal rubber molded part. By combining manganese-nitrogen alloying with repeated drawing and intermediate heat treatment processes and surface finishing, the steel wire is ensured to have high strength and high surface quality, while retaining a certain proportion of austenitic structure after drawing, thereby improving the plasticity of the steel wire and enabling it to be finally made into a metal rubber molded part with excellent fatigue performance.

[0007] To achieve the above objectives, the present invention adopts the following technical solution: In a first aspect, the present invention provides a method for preparing stainless steel wire for use in metal rubber, comprising the following steps: S1. Smelting and continuous casting: Smelting is carried out using an electric arc furnace, an argon-oxygen decarburization furnace and a ladle refining furnace. During the smelting process, manganese and nitrogen alloying is carried out, followed by continuous casting to obtain a billet with a manganese mass percentage of 15.00%-17.00% and a nitrogen mass percentage of 0.65%-0.70%. S2. Hot rolling and cooling of wire rod: The billet is first heated and then hot rolled to obtain wire rod, which is then cooled. S3. Drawing and intermediate heat treatment: The wire rod is drawn and then subjected to hydrogen bright annealing; the drawing and annealing process is repeated until the steel wire of the target size is obtained; S4. Surface finishing: The drawn steel wire is ground and polished to obtain the stainless steel wire; The chemical composition of the billet by weight percentage is as follows: C: 0.08%-0.12%, N: 0.65%-0.70%, Si: 0.10%-0.30%, Mn: 15.00%-17.00%, P: ≤0.03%, S: ≤0.008%, Cr: 21.00%-23.00%, Ni: 1.00%-1.30%, Cu: ≤0.30%, with the balance being Fe and unavoidable impurities.

[0008] This invention utilizes manganese and nitrogen to alloy the steel during the smelting stage, resulting in a manganese (Mn) content of 15.00%-17.00% by mass in the billet. This increases the solubility of nitrogen in austenitic steel and achieves a final nitrogen (N) content of 0.65%-0.70% by mass in the billet. Nitrogen has a stabilizing effect on austenite. This high-nitrogen composition, dissolved in the austenitic matrix through alloying, ensures that some austenite is retained in the microstructure after drawing deformation, improving the plasticity of the steel wire. Simultaneously, the solid solution strengthening effect of nitrogen directly enhances the strength of the austenitic matrix. Even with a reduced martensite conversion rate, the strength and surface hardness of the steel wire are maintained, meeting the requirements for wire strength and toughness in metal rubber. In this invention, the nickel (Ni) content is significantly reduced to 1.00%-1.30%. Reducing the nickel content serves two purposes: firstly, it significantly reduces the cost of expensive alloys; secondly, it avoids excessively high nickel content from lowering the material's stacking fault energy, thus allowing the material to maintain a high work hardening rate during cold drawing, which is beneficial for ultimately obtaining ultra-high strength wire. Approximately 1% nickel content primarily plays a supporting role in stabilizing austenite.

[0009] The process flow defined in this invention, namely "smelting and continuous casting → hot rolling and cooling → drawing and intermediate heat treatment → surface finishing," constitutes a complete technical solution designed to meet the performance requirements of metal rubber. Starting with component smelting, this solution systematically controls the entire production process of the wire through continuous forming, deformation, and finishing steps, laying a technological foundation for the stable production of high-performance metal rubber wire. Through the repeated cycle of "drawing and intermediate heat treatment," precise control over the wire's microstructure and properties is achieved. The repeated setting of the "drawing and annealing process" allows for the gradual accumulation of deformation, grain refinement, and adjustment of dislocation structure through the combination of drawing deformation and intermediate recrystallization annealing, thereby increasing the wire strength to the target level without excessively sacrificing plasticity. This cyclical process provides an effective means to obtain a good balance between high strength and good toughness.

[0010] Furthermore, in step S1, the manganese-nitrogen alloying during the smelting process includes: bottom blowing nitrogen gas throughout the argon-oxygen decarburization furnace smelting process, and adding electrolytic manganese during the reduction stage to make the manganese content in the molten steel reach 12.00%-14.00% and the nitrogen content reach 0.40%-0.50%, and then adding manganese nitride during the ladle refining furnace smelting process to carry out the manganese-nitrogen alloying.

[0011] Furthermore, in step S1, the continuous casting process employs superheated casting to maintain the temperature of the molten steel in the continuous casting tundish at 1400℃-1430℃, and electromagnetic stirring is used.

[0012] Furthermore, in step S2, the heating temperature is 1200℃-1300℃, and the heating time is 2-4 hours.

[0013] Furthermore, in step S2, the inlet temperature of the hot-rolled finishing mill is 1040℃-1090℃.

[0014] Furthermore, in step S2, the hot rolling temperature is 1000℃-1040℃.

[0015] Furthermore, in step S2, the cooling is water cooling to room temperature.

[0016] Furthermore, in step S2, the diameter (φ) of the wire rod is 6.4mm-6.6mm.

[0017] Furthermore, after step S2 and before step S3, a surface pretreatment step is included for the wire rod. The surface pretreatment includes peeling and a first hydrogen bright annealing. The first hydrogen bright annealing uses hydrogen with a purity of 99.99%-99.999% and a dew point of <-60℃, an annealing temperature of 1050℃-1080℃, a holding time of 10-20 minutes, and water quenching after holding.

[0018] Furthermore, in step S3, the drawing process is performed using a polycrystalline diamond drawing die.

[0019] Furthermore, in step S3, the number of pulls is 4-6, the deformation rate of each pull does not exceed 30%, and the total deformation rate of each pull is 70%-80%.

[0020] Furthermore, in step S3, the hydrogen bright annealing is a second hydrogen bright annealing. The hydrogen used in the second hydrogen bright annealing has a purity of 99.99%-99.999% and a dew point of <-60℃. The annealing temperature is 1050℃-1080℃, and the holding time t (min) satisfies the formula: t=2+2R / 3, where R is the diameter of the wire before annealing, and the unit of the diameter is mm.

[0021] Furthermore, step S4 also includes cleaning the polished steel wire.

[0022] Furthermore, the target diameter (φ) of the steel wire obtained in step S3 is 0.27mm-0.33mm.

[0023] Furthermore, after step S3 is completed, the tensile strength of the steel wire is 2050MPa-2250MPa, and the elongation after fracture is 1.7%-2.5%.

[0024] Furthermore, after step S4 is completed, the surface roughness Ra value of the stainless steel wire is 0.1μm-0.3μm.

[0025] In a second aspect, the present invention provides a stainless steel wire for use in metal rubber, which is made by the preparation method described in the first aspect.

[0026] Thirdly, the present invention provides a metal-rubber molded part, which is made of stainless steel wire for metal-rubber as described in the second aspect.

[0027] Furthermore, the metal-rubber molded part is made by winding the stainless steel wire used for metal-rubber into a spiral coil, winding a blank, and stamping. During the spiral coil winding process, the spiral diameter and pitch are equal, both being 3.0mm-3.5mm. During the blank winding process, the amount of stainless steel wire used for metal-rubber is 40g-55g. During the stamping process, the stamping pressure is 8.0±0.5kN. The density of the metal-rubber molded part is 2.5g / cm³. 3 -3.5g / cm 3 .

[0028] Compared with the prior art, the beneficial effects of the present invention include at least one of the following: 1) This invention provides a complete and systematic process for preparing stainless steel wire for use in metal rubber. The process flow defined by this invention, namely "smelting and continuous casting → hot rolling and cooling → drawing and intermediate heat treatment → surface finishing," constitutes a complete technical solution designed to meet the performance requirements of metal rubber. Starting from component smelting, this solution systematically controls the entire wire production process through continuous forming, deformation, and finishing steps, laying a technological foundation for the stable acquisition of high-performance metal rubber wire. 2) This invention achieves high-nitrogen manganese-nitrogen alloying during the smelting stage, providing a core component guarantee for achieving high strength and good toughness matching in the wire. Adding manganese and nitrogen elements, and performing manganese-nitrogen alloying during the smelting stage, results in a manganese (Mn) mass percentage of 15.00%-17.00% in the billet, increasing the solubility of nitrogen in austenitic steel and achieving a final nitrogen (N) mass percentage of 0.65%-0.70%. Nitrogen has a stabilizing effect on austenite. This high-nitrogen composition design, through alloying, dissolves in the austenitic matrix, ensuring that a portion of austenite is retained in the microstructure after drawing deformation, thus improving the plasticity of the steel wire. Simultaneously, the solid solution strengthening effect of nitrogen directly enhances the strength of the austenitic matrix, maintaining the strength and surface hardness of the steel wire even with a reduced martensite conversion rate, meeting the requirements of metal rubber for wire strength and toughness. In this invention, the nickel (Ni) content is significantly reduced to 1.00%-1.30%. Reducing the nickel content serves two purposes: firstly, it significantly reduces the cost of expensive alloys; secondly, it avoids excessively high nickel content from lowering the material's stacking fault energy, thus allowing the material to maintain a high work hardening rate during cold drawing, which is beneficial for ultimately obtaining ultra-high strength wire. Approximately 1% nickel content primarily serves to help stabilize austenite. 3) This invention achieves precise control over the microstructure and properties of wire through repeated cycles of drawing and intermediate heat treatment. The repeated drawing and annealing processes allow for the gradual accumulation of deformation, grain refinement, and adjustment of dislocation structure through the combination of drawing deformation and intermediate recrystallization annealing. This, in turn, increases the wire strength to the target level without excessively sacrificing plasticity. This cyclical process provides an effective means of achieving a good balance between high strength and good toughness. 4) This invention achieves refined optimization of wire surface quality by using hydrogen bright annealing throughout the steel wire drawing process, simplifying the drawing process. By using high-purity hydrogen (with a purity of 99.99%-99.999% and a dew point <-60℃ for both the first and second bright annealing processes), bright annealing eliminates work hardening of the steel wire, obtains an austenitic structure, and yields a smooth, clean wire surface with a metallic luster without further surface treatment. Hydrogen bright annealing eliminates the need for pickling or other surface treatments, leaving no residue on the wire surface, thus reducing the wear rate of the drawing die and significantly extending its lifespan. This method simplifies the process, reduces equipment wear, and effectively improves the surface quality of the steel wire, achieving a balance between economic benefits and finished product quality. 5) This invention uses a polycrystalline diamond drawing die for drawing and then grinds and polishes the stainless steel wire after drawing, which improves the surface quality of the finished steel wire, giving it higher surface smoothness and fewer surface scratches, laying a good foundation for the subsequent preparation of metal rubber molded parts. 6) The metal-rubber molded parts provided by the present invention are obtained by further processing the stainless steel wire used for metal-rubber as described above. Since the high-nitrogen stainless steel wire described in 1)-5) has excellent strength and elongation, as well as high surface quality, the metal-rubber molded parts made from it have excellent stiffness and damping performance, and at the same time have significant advantages in fatigue performance compared with metal-rubber made from traditional steel. Attached Figure Description

[0029] To more clearly illustrate the technical solutions in this invention or the prior art, the drawings used in the description of the embodiments or the prior art will be briefly introduced below. Obviously, the drawings described below are some embodiments of this invention. For those skilled in the art, other drawings can be obtained from these drawings without creative effort.

[0030] Figure 1 The images show actual pictures of the hydrogen annealing furnaces used in Embodiments 1-5 and Comparative Examples 1-4 of the present invention. Figure 2 These are physical images of the polycrystalline diamond drawing dies used in Examples 1-4 and Comparative Examples 1-4 of the present invention; Figure 3 This is a photograph of the finished steel wire obtained in Example 1 of the present invention; Figure 4 The image shows a scanning electron microscope image of the surface morphology of the finished steel wire obtained in Example 1 of this invention. Figure 5 This is a physical image of the metal-rubber molded part obtained in Embodiment 1 of the present invention; Figure 6 This is a laser confocal microscope image showing the test results of the finished steel wire obtained in Example 1 of the present invention; Figure 7 This is a laser confocal microscope image showing the test results of the finished steel wire obtained in Example 5 of the present invention; Figure 8 This is a laser confocal microscope image showing the results of laser confocal microscopy testing on the finished steel wire prepared in Comparative Example 4 of this invention. Figure 9 This is a photograph of the metal-rubber molded part obtained in Embodiment 1 of the present invention after fatigue testing. Figure 10 This is a photograph of the metal-rubber molded part obtained in Comparative Example 1 of the present invention after fatigue testing. Figure 11 This is a photograph of the metal-rubber molded part obtained in Comparative Example 4 of the present invention after fatigue testing. Detailed Implementation

[0031] To make the objectives, technical solutions, and advantages of this invention clearer, the technical solutions in the embodiments of this invention will be clearly and completely described below in conjunction with the embodiments of this invention. Those skilled in the art should understand that the embodiments described are merely illustrative of the invention and should not be considered as specific limitations thereof. All other embodiments obtained by those skilled in the art based on the embodiments of this invention without creative effort are within the scope of protection of this invention. Process parameters not specifically specified in the following embodiments are generally performed under conventional conditions.

[0032] The endpoints and any values ​​of the ranges disclosed in this invention are not limited to the precise ranges or values, and these ranges or values ​​should be understood to include values ​​close to these ranges or values. For numerical ranges, the endpoint values ​​of the various ranges, the endpoint values ​​of the various ranges and individual point values, and individual point values ​​can be combined with each other to obtain one or more new numerical ranges, which should be considered as specifically disclosed in this invention.

[0033] In a first aspect, the present invention provides a method for preparing stainless steel wire for use in metal rubber, comprising the following steps: S1. Smelting and continuous casting: Smelting is carried out using an electric arc furnace, an argon-oxygen decarburization furnace and a ladle refining furnace. During the smelting process, manganese and nitrogen alloying is carried out, followed by continuous casting to obtain a billet with a manganese mass percentage of 15.00%-17.00% and a nitrogen mass percentage of 0.65%-0.70%. S2. Hot rolling and cooling of wire rod: The billet is first heated and then hot rolled to obtain wire rod, which is then cooled. S3. Drawing and intermediate heat treatment: The wire rod is drawn and then subjected to hydrogen bright annealing; the drawing and annealing process is repeated until the steel wire of the target size is obtained; S4. Surface finishing: The drawn steel wire is ground and polished to obtain the stainless steel wire; The chemical composition of the billet by weight percentage is as follows: C: 0.08%-0.12%, N: 0.65%-0.70%, Si: 0.10%-0.30%, Mn: 15.00%-17.00%, P: ≤0.03%, S: ≤0.008%, Cr: 21.00%-23.00%, Ni: 1.00%-1.30%, Cu: ≤0.30%, with the balance being Fe and unavoidable impurities.

[0034] This invention utilizes manganese and nitrogen to alloy the steel during the smelting stage, resulting in a manganese (Mn) content of 15.00%-17.00% by mass in the billet. This increases the solubility of nitrogen in austenitic steel and achieves a final nitrogen (N) content of 0.65%-0.70% by mass in the billet. Nitrogen has a stabilizing effect on austenite. This high-nitrogen composition, dissolved in the austenitic matrix through alloying, ensures that some austenite is retained in the microstructure after drawing deformation, improving the plasticity of the steel wire. Simultaneously, the solid solution strengthening effect of nitrogen directly enhances the strength of the austenitic matrix. Even with a reduced martensite conversion rate, the strength and surface hardness of the steel wire are maintained, meeting the requirements for wire strength and toughness in metal rubber. In this invention, the nickel (Ni) content is significantly reduced to 1.00%-1.30%. Reducing the nickel content serves two purposes: firstly, it significantly reduces the cost of expensive alloys; secondly, it avoids excessively high nickel content from lowering the material's stacking fault energy, thus allowing the material to maintain a high work hardening rate during cold drawing, which is beneficial for ultimately obtaining ultra-high strength wire. Approximately 1% nickel content primarily plays a supporting role in stabilizing austenite.

[0035] The process flow defined in this invention, namely "smelting and continuous casting → hot rolling and cooling → drawing and intermediate heat treatment → surface finishing," constitutes a complete technical solution designed to meet the performance requirements of metal rubber. Starting from component smelting, this solution systematically controls the entire production process of the wire through continuous forming, deformation, and finishing steps, laying a technological foundation for the stable production of high-performance metal rubber wire. Through repeated cycles of "drawing and intermediate heat treatment," precise control over the wire's microstructure and properties is achieved. The repeated setting of the "drawing and annealing process" allows for the gradual accumulation of deformation, grain refinement, and adjustment of dislocation structure through the combination of drawing deformation and intermediate recrystallization annealing, thereby increasing the wire strength to the target level without excessively sacrificing plasticity. This cyclical process provides an effective means to obtain a good balance between high strength and good toughness.

[0036] As an optional implementation, step S1, the manganese-nitrogen alloying during the smelting process, includes: bottom blowing nitrogen gas throughout the argon-oxygen decarburization furnace smelting process, and adding electrolytic manganese during the reduction stage to make the manganese content in the molten steel reach 12.00%-14.00%, for example, 12.00%, 12.50%, 12.80%, 13.00%, 13.20%, 13.50%, or 14.00%, and the nitrogen content reach 0.40%-0.50%, for example, 0.40%, 0.42%, 0.45%, 0.47%, 0.48%, or 0.50%, and then adding manganese nitride during the ladle refining furnace smelting process to perform the manganese-nitrogen alloying.

[0037] In this invention, nitrogen is bottom-blown throughout the argon-oxygen decarburization furnace (AOD), and electrolytic manganese is added during the reduction stage. This first establishes a molten pool environment with high manganese (12.00%-14.00%) and medium nitrogen (0.40%-0.50%), allowing the molten steel to form a high-manganese austenitic matrix after solidification. This matrix, due to its expanded lattice and stable structure, significantly improves the solubility limit of nitrogen in solid austenite, providing a crucial microstructure for increasing and stabilizing nitrogen content. The bottom-blown nitrogen achieves preliminary decarburization, chromium preservation, and manganese-nitrogen alloying. In the ladle refining furnace (LF), nitrogen composition is "fine-tuned" and final manganese-nitrogen alloying is achieved by adding manganese nitride, which has stable composition and good solubility. This step effectively compensates for nitrogen loss in previous processes and precisely adjusts the nitrogen content of the molten steel to the level required to obtain the final high-nitrogen content (0.65%-0.70%) in the billet, solving the problem of nitrogen recovery and compositional precision control in high-nitrogen steel smelting.

[0038] As an optional implementation, in step S1, the chemical composition of the cast billet, by weight percentage, is as follows: C: 0.08%, 0.09%, 0.10%, 0.11% or 0.12%; N: 0.65%, 0.66%, 0.67%, 0.68%, 0.69% or 0.70%; Si: 0.10%, 0.13%, 0.15%, 0.20%, 0.22%, 0.25%, 0.27% or 0.30%; Mn: 15.00%, 15.07%, 15.60%, 15.71%, 15.85%, 16.00%, 16.35% or 17.00%; P : 0.020%, 0.024%, 0.028% or 0.030%; S: 0.002%, 0.003%, 0.005% or 0.008%; Cr: 21.00%, 21.03%, 21.05%, 21.50%, 21.75%, 22.25%, 22.50% or 23.00%; Ni: 1.00%, 1.05%, 1.10%, 1.15%, 1.18%, 1.20%, 1.24% or 1.30%; Cu: 0.10%, 0.15%, 0.20%, 0.25% or 0.30%, with the balance being Fe and unavoidable impurities.

[0039] This invention designs the composition of the billet, and the roles of each element are as follows: 1) Carbon: Carbon is an effective interstitial solid solution strengthening element. This invention controls its content at 0.08%-0.12%, aiming to utilize its significant solid solution strengthening effect to provide a foundation for achieving high strength in steel wire. Simultaneously, carbon is also an austenite forming element, playing an auxiliary role in stabilizing the austenite phase during cold working. The upper limit of the content is set at 0.12% to avoid excessive carbon causing carbide precipitation along grain boundaries, thereby impairing the material's plasticity; 2) Nitrogen: Nitrogen is the core element of this invention, with a content of 0.65%-0.70%, reaching the level of high-nitrogen stainless steel. Its role is multifaceted and crucial: Nitrogen is an extremely strong austenite stabilizing element. Its high content, synergistically with carbon and manganese, can ensure that the material maintains austenite stability during large deformation cold drawing even with extremely low nickel content (approximately 1%), thus achieving the dual goals of "austenite stabilization" and "nickel saving." As an interstitial atom, high nitrogen content can produce a strong solid solution strengthening effect, making it one of the main contributors to improving wire strength. Nitrogen significantly improves the stability and repassivation ability of the stainless steel passivation film, greatly enhancing the corrosion resistance of the wire; 3) Si element: Silicon, as a deoxidizing element, is controlled at a low content of 0.10%-0.30%. Its main function is to improve the purity of the molten steel during the smelting process. Controlling it at a low level is to avoid promoting the formation of intermetallic compounds or harmful precipitates, and to maintain the purity and stability of the wire structure while ensuring the necessary deoxidation effect; 4) Cr element: Chromium is the cornerstone element for ensuring the corrosion resistance of stainless steel, resisting corrosion by forming a dense Cr2O3 passivation film. This invention increases the chromium content to 21.00%-23.00%, significantly higher than conventional 316 stainless steel (~18%). The high chromium content ensures the passivation film formation capability, and in combination with nitrogen, further enhances the regeneration capability and pitting corrosion resistance of the passivation film, thus achieving excellent corrosion resistance. 5) Mn element: The manganese content is set at a relatively high 15.00%-17.00%, and its role is crucial and multifaceted: As a strong austenite forming element, high manganese content is the core guarantee for stabilizing the austenite structure, especially for suppressing martensitic transformation during drawing deformation. Manganese can significantly increase the solubility of nitrogen in austenite, which is a prerequisite for this invention to achieve and stably obtain a high nitrogen content of 0.65%-0.70% under conventional smelting conditions. High manganese helps maintain a single austenite structure during casting and hot working, thereby improving the hot working performance of the material and reducing defects. 6) Ni element: Nickel, as a traditional austenite stabilizing element, has its content significantly reduced to 1.00%-1.30% in this invention. Reducing the nickel content serves two purposes: firstly, it significantly reduces the cost of expensive alloys; secondly, it avoids excessively high nickel content from lowering the material's stacking fault energy, thus allowing the material to maintain a high work hardening rate during cold drawing, which is beneficial for ultimately obtaining ultra-high strength wire. Approximately 1% nickel content primarily plays a supporting role in stabilizing austenite.

[0040] As an optional implementation, in step S1, the continuous casting process adopts superheated casting to maintain the temperature of the molten steel in the continuous casting tundish at 1400℃-1430℃, for example, 1400℃, 1405℃, 1410℃, 1415℃, 1420℃, 1425℃ or 1430℃, and electromagnetic stirring is used.

[0041] The present invention employs "overheating casting" (1400-1430℃) which is beneficial to the fluidity of molten steel and reduces nozzle blockage; and employs "electromagnetic stirring" which can effectively break dendrites, homogenize the composition, significantly reduce macroscopic segregation of high nitrogen steel, obtain a more uniform and dense billet, and improve the consistency and reliability of the material.

[0042] As an optional implementation, in step S2, the heating temperature is 1200℃-1300℃, for example, it can be 1200℃, 1210℃, 1240℃, 1250℃, 1280℃ or 1300℃, and the heating time is 2-4h, for example, it can be 2h, 2.5h, 3h, 3.5h or 4h.

[0043] As an optional implementation, in step S2, the inlet temperature of the hot rolling finishing mill is 1040℃-1090℃, for example, it can be 1040℃, 1050℃, 1060℃, 1070℃, 1080℃ or 1090℃.

[0044] As an optional implementation, in step S2, the hot rolling temperature is 1000℃-1040℃, for example, it can be 1000℃, 1010℃, 1020℃, 1030℃ or 1040℃.

[0045] As an optional implementation, in step S2, the cooling is water cooling to room temperature.

[0046] As an optional implementation, in step S2, the diameter (φ) of the wire rod is 6.4mm-6.6mm, for example, it can be 6.4mm, 6.5mm or 6.6mm.

[0047] This invention provides a specific hot rolling temperature control process (heating temperature 1200-1300℃, finishing mill inlet temperature 1040-1090℃, wire drawing temperature 1000-1040℃). This process ensures that the steel undergoes plastic deformation in the austenitic single-phase region, achieving good hot working properties and avoiding excessive deformation resistance or cracking caused by rolling in the low-temperature region, resulting in a uniform and fine austenitic structure in the hot-rolled wire rod. Subsequent water cooling to room temperature aims to rapidly pass through Cr2N and Cr... 23The process targets the sensitive temperature range for harmful precipitates such as C6, inhibiting their precipitation and preserving the fine-grained austenite structure after hot rolling to room temperature to prevent grain growth. Further reducing the heating temperature during hot rolling may result in excessively low temperatures, causing Cr to reach its maximum density during rolling. 23 The sensitive temperatures of precipitates such as C6 and Cr2N (usually between 600-1000℃) make hot-rolled products prone to surface defects or cracks, or cause a significant decrease in the performance of finished steel wire.

[0048] As an optional implementation, after step S2 and before step S3, a surface pretreatment step is further included for the wire rod. The surface pretreatment includes peeling and a first hydrogen bright annealing. The hydrogen used in the first hydrogen bright annealing has a purity of 99.99%-99.999%, for example, 99.99%, 99.993%, 99.995%, or 99.999%, a dew point <-60℃, for example, -63℃, -65℃, or -70℃, an annealing temperature of 1050℃-1080℃, for example, 1050℃, 1060℃, 1070℃, or 1080℃, a holding time of 10-20 minutes, for example, 10 minutes, 15 minutes, or 20 minutes, followed by water quenching.

[0049] This invention adds a "surface pretreatment" step to remove surface oxide scale and defects, and softens the structure through bright annealing, providing a clean, soft, and uniform raw material surface for subsequent cold drawing processes. This reduces die wear during drawing and prevents surface defects from being introduced into the wire, making it a key process to ensure the final wire surface quality and smooth drawing.

[0050] As an optional implementation, in step S3, the drawing process is performed using a polycrystalline diamond drawing die.

[0051] This invention uses polycrystalline diamond molds, which have a dense structure and high surface finish. They are less prone to sticking during the drawing process, solving the problems of rapid mold wear and scratches on the wire surface during the drawing process. This can effectively improve the surface quality of the drawn steel wire, reduce surface undulations and surface defects, and effectively improve the service life of the subsequently produced metal-rubber molded parts.

[0052] As an optional implementation, the number of pull-out passes is 4-6, for example, 4, 5 or 6 passes, and the deformation rate of each pass does not exceed 30%, for example, 20%, 25% or 30%, and the total deformation rate of each pull-out is 70%-80%, for example, 70%, 75% or 80%.

[0053] This invention achieves stable and controllable work hardening by controlling the drawing process parameters, ensuring processing efficiency while avoiding the risk of internal damage or wire breakage caused by excessive deformation in a single pass.

[0054] As an optional implementation, the hydrogen bright annealing is a second hydrogen bright annealing. The hydrogen used in the second hydrogen bright annealing has a purity of 99.99%-99.999%, such as 99.99%, 99.993%, 99.995%, or 99.999%, a dew point of <-60℃, such as -63℃, -65℃, or -70℃, an annealing temperature of 1050℃-1080℃, such as 1050℃, 1060℃, 1070℃, or 1080℃, and a holding time t (min) that satisfies the formula: t=2+2R / 3, where R is the diameter of the wire before annealing, and the unit of the diameter is mm.

[0055] This invention employs a second hydrogen bright annealing as an intermediate annealing process. Through short-time, high-temperature annealing, the stress generated during drawing is released, and the deformed structure recrystallizes to obtain an austenitic structure, regaining high plasticity. Hydrogen bright annealing is used throughout the entire wire drawing process, achieving refined optimization of the wire surface quality while simplifying the drawing process. By using high-purity hydrogen (99.99%-99.999%, dew point <-60℃) for bright annealing, work hardening of the wire is eliminated, and an austenitic structure is obtained without further surface treatment, resulting in a smooth, clean wire surface with a metallic luster. Hydrogen bright annealing eliminates the need for pickling or other surface treatments, leaving no residue on the wire surface, thus reducing the wear rate of the drawing die and significantly extending its lifespan. Further defining the second hydrogen bright annealing formula allows for precise calculation of the annealing time based on the instantaneous diameter of the wire, ensuring that work hardening is fully eliminated and plasticity is restored, while avoiding excessive recrystallization that leads to strength loss. This is the key to achieving a balance between high strength and plasticity.

[0056] As an optional implementation, step S4 also includes cleaning the polished steel wire.

[0057] As an optional implementation, the target diameter (φ) of the steel wire obtained in step S3 is 0.27mm-0.33mm, for example, it can be 0.27mm, 0.28mm, 0.29mm, 0.30mm, 0.31mm, 0.32mm or 0.33mm.

[0058] As an optional implementation, after step S3 is completed, the tensile strength of the steel wire is 2050MPa-2250MPa, and the elongation after fracture is 1.7%-2.5%.

[0059] As an optional implementation, after step S4 is completed, the surface roughness Ra value of the stainless steel wire is 0.1μm-0.3μm.

[0060] In a second aspect, the present invention provides a stainless steel wire for use in metal rubber, which is made by the preparation method described in the first aspect.

[0061] Thirdly, the present invention provides a metal-rubber molded part made of stainless steel wire for metal-rubber as described in the second aspect.

[0062] In one optional embodiment, the metal-rubber molded part is made by winding the stainless steel wire used for metal-rubber into a spiral coil, winding a blank, and stamping. During the spiral coil winding process, the spiral diameter and pitch are equal, both being 3.0mm-3.5mm, for example, 3.0mm, 3.1mm, 3.2mm, 3.3mm, 3.4mm, or 3.5mm. During the blank winding process, the amount of stainless steel wire used for metal-rubber is 40g-55g, for example, 40g, 41g, 42g, 45g, 48g, 50g, 54g, or 55g. During the stamping process, the stamping pressure is 8.0±0.5kN, for example, 7.5kN, 8.0kN, or 8.5kN. The density of the metal-rubber molded part is 2.5g / cm³. 3 -3.5g / cm 3 For example, it can be 2.5g / cm³. 3 2.6g / cm 3 2.8g / cm 3 3.0g / cm 3 3.2g / cm 3 3.4g / cm 3 Or 3.5g / cm 3 .

[0063] The present invention will now be described in further detail with reference to specific embodiments.

[0064] Example 1 This embodiment provides a method for preparing stainless steel wire for use in metal rubber, including the following steps: S1. Smelting and Continuous Casting: A three-step smelting process was adopted, consisting of primary smelting in an electric arc furnace (EAF), refining in an argon-oxygen decarburization furnace (AOD), and final smelting in a ladle refining furnace (LF). During the AOD smelting process, nitrogen was blown through the bottom throughout, and electrolytic manganese was added during the reduction stage to achieve a manganese content of approximately 13.50% and a nitrogen content of approximately 0.45% in the molten steel. Subsequently, during the LF refining process, manganese-nitrogen alloying was further carried out by adding manganese nitride, ultimately precisely adjusting the manganese content in the molten steel to 15.71% and the nitrogen content to 0.69%. After smelting, continuous casting was performed using a superheated casting method, controlling the temperature of the molten steel in the tundish at 1425℃, and applying electromagnetic stirring (300A current, 4Hz frequency) to obtain 180mm×180mm square billets with uniform composition and dense microstructure.

[0065] The chemical composition of the billet by weight percentage is: C 0.10%, N 0.69%, Si 0.27%, Mn 15.71%, P 0.024%, S 0.003%, Cr 21.05%, Ni 1.18%, Cu 0.25%, with the balance being Fe and unavoidable impurities.

[0066] S2. Hot rolling and cooling of wire rod: The billet was heated to 1250℃ and held for 3 hours before hot rolling. The inlet temperature of the finishing mill was controlled at 1060℃, and the wire drawing temperature was 1020℃, yielding wire rod with a diameter of φ6.5mm. After hot rolling, the wire rod was cooled to room temperature by water cooling.

[0067] S3. Surface pretreatment: The surface of the hot-rolled wire rod is peeled to remove oxide scale and surface defects. Then, as... Figure 1 The first hydrogen bright annealing was carried out in the hydrogen annealing furnace shown. The hydrogen used had a purity of 99.993% and a dew point of -63℃. The annealing temperature was 1080℃, and the holding time was 10 minutes. After the holding time was completed, the furnace was immediately water quenched.

[0068] S4. First drawing and intermediate heat treatment: Use such as Figure 2 The polycrystalline diamond drawing die shown is used for the first drawing of the pretreated wire rod. The drawing is performed in 6 passes, with a deformation rate of no more than 30% in each pass, and a total deformation rate of about 75%, to obtain a semi-finished steel wire with a diameter of φ3.5mm.

[0069] The semi-finished steel wire was then subjected to a second hydrogen bright annealing. The hydrogen used had a purity of 99.993% and a dew point of -63℃. The annealing temperature was 1080℃, and the holding time was calculated using the formula t=2+2R / 3 (where R is the wire diameter in mm). With R=3.5mm, the holding time was calculated to be 4.3min. After annealing, the wire was water quenched.

[0070] S5. Multiple drawing and heat treatment cycles: The process of drawing and intermediate annealing was repeated to gradually draw the steel wire to diameters of φ1.8mm, φ0.9mm, φ0.6mm, and φ0.3mm. After each drawing, hydrogen bright annealing was performed at a temperature of 1080℃. The holding time was calculated based on the wire diameter before annealing using the formula t=2+2R / 3, corresponding to 3.2min, 2.6min, and 2.4min respectively. Finally, a stainless steel wire with a target diameter of φ0.30mm was obtained.

[0071] S6. Surface finishing: The steel wire obtained after final drawing is surface-ground and polished, then cleaned to obtain the finished stainless steel wire. The macroscopic morphology of the finished stainless steel wire is as follows: Figure 3 As shown in the image, a scanning electron microscope (SEM) image of the surface microstructure of the finished stainless steel wire is as follows: Figure 4 As shown, scanning electron microscopy (SEM) revealed that the surface of the finished stainless steel wire was smooth and free of obvious scratches. The surface roughness Ra value of the finished wire was 0.156 μm, the tensile strength was 2198 MPa, and the elongation after fracture was 2.22%.

[0072] This embodiment also provides a method for preparing a metal-rubber molded part, including the following steps: 1) The above-mentioned finished stainless steel wire (diameter φ0.30mm, tensile strength 2198MPa, elongation after fracture 2.22%, surface roughness Ra=0.156μm) is wound into a spiral coil. The spiral coil has the same diameter and pitch, both set to 3.0 mm.

[0073] 2) Weigh the spiral coil to obtain its mass m0 based on the pre-designed density ρ and dimension V of the metal-rubber molded part; set the design density of the target metal-rubber molded part to ρ = 2.6 g / cm³. 3 The designed volume V = 30mm × 30mm × 17.6mm = 15840mm 3 =15.84cm 3 .

[0074] Calculate the total mass m0 of the required spiral coil: m0 = ρ × V = 2.6 g / cm³ 3 ×15.84cm 3 ≈41.2g.

[0075] 3) Set n (n=8) winding nodes on the mandrel. The height of any two adjacent winding nodes is h1=D×tanθ. In this embodiment, the winding angle θ is 45° and the diameter D of the mandrel is 13mm. Therefore, the height of any two adjacent winding nodes is h1=D=13mm. The total winding height of the spiral on the mandrel is h0=(n-1)×h1=91mm.

[0076] 4) The spiral coil is crisscrossed along the winding nodes on the mandrel at a winding angle of 45°. The specific winding steps are as follows: First, the spiral coil is wound clockwise from bottom to top along the winding node trajectory until the entire winding height is filled. Then, the spiral coil is wound counterclockwise from top to bottom along the winding node trajectory until the entire winding height is filled again. The crisscrossing is repeated in the above winding method to obtain the metal rubber blank.

[0077] 5) Remove the prepared metal-rubber blank from the mandrel and place it in a stamping die with dimensions of 30mm × 30mm × 45mm. Perform cold stamping and shaping under a pressure of 8.0 kN to obtain the metal-rubber molded part. The density of the metal-rubber molded part was measured to be approximately 2.6 g / cm³. 3 Its macroscopic morphology is as follows Figure 5 As shown.

[0078] Example 2 This embodiment provides a method for preparing stainless steel wire for use in metal rubber, the steps of which are basically the same as in Embodiment 1, the main difference being the reduction of the content of elements in the casting billet, especially the further reduction of the nickel content. Details are as follows: S1. Smelting and Continuous Casting: The chemical composition of the billet by weight percentage is: C 0.08%, N 0.65%, Si 0.10%, Mn 15.00%, P 0.028%, S 0.005%, Cr 21.00%, Ni 1.00%, Cu 0.10%, with the balance being Fe and unavoidable impurities. The temperature of the molten steel in the continuous casting tundish is 1400℃, and the electromagnetic stirring parameters are: current 300A, frequency 4Hz.

[0079] The process parameters for the remaining steps S2-S6 are consistent with those in Example 1. The preparation method of the metal-rubber molded part is the same as in Example 1.

[0080] Example 3 This embodiment provides a method for preparing stainless steel wire for use in metal rubber, the steps of which are basically the same as those in Embodiment 1, the main difference being: adjusting the hot rolling process parameters, while maintaining the same composition as in Embodiment 1. Details are as follows: S2. Hot rolling and cooling of wire rod: The billet is heated to 1300℃, and the holding time is shortened to 2 hours. The inlet temperature of the finishing mill is controlled at 1090℃, and the wire drawing temperature is controlled at 1040℃. The process parameters for the remaining steps S1, S3-S6 are exactly the same as in Example 1. The preparation method of the metal rubber molded parts is the same as in Example 1.

[0081] Example 4 This embodiment provides a method for preparing stainless steel wire for use in metal rubber, the steps of which are basically the same as those in Example 1, the main difference being: the annealing process is adjusted, and the composition is the same as in Example 1. Details are as follows: S4. First drawing and intermediate heat treatment: After obtaining semi-finished steel wire with a diameter of approximately φ3.5mm, hydrogen bright annealing is performed at a temperature of 1080℃ and a holding time of 5min. After annealing, the wire is water quenched.

[0082] S5. Multiple drawing and heat treatment cycles: The subsequent annealing procedure is adjusted to: annealing temperature of 1080℃, followed by 3 annealing cycles, with each annealing time fixed at 5 minutes.

[0083] The remaining steps S1-S3 and S6 are the same as in Example 1. The preparation method of the metal-rubber molded part is the same as in Example 1.

[0084] Example 5 This embodiment provides a method for preparing stainless steel wire for use with metal rubber. The only difference between this method and Example 1 is that a cemented carbide drawing die is used instead of a polycrystalline diamond drawing die during the drawing process. All other process steps and parameters are exactly the same as in Example 1. Specifically: In all drawing processes in steps S4 (first drawing and intermediate heat treatment) and S5 (multiple drawing and heat treatment), carbide drawing dies are used for drawing.

[0085] The process parameters for steps S1 (smelting and casting, using the high-nitrogen composition of this invention), S2 (hot rolling), S3 (surface pretreatment), and S6 (surface finishing, including grinding and polishing) are consistent with those of Example 1. The preparation method of the metal-rubber molded parts is the same as that of Example 1.

[0086] Comparative Example 1 This comparative example provides a method for preparing stainless steel wire, the steps of which are basically the same as those in Example 1, the main difference being that the billet composition uses conventional 316 stainless steel, rather than the composition of Example 1 of this invention. Details are as follows: S1. Smelting and Continuous Casting: Smelting and continuous casting are carried out using conventional 316 stainless steel to obtain a billet. The chemical composition of the billet by weight percentage is: C 0.04%, N 0.03%, Si 0.29%, Mn 0.92%, P 0.038%, S 0.003%, Cr 16.57%, Ni 10.06%, Mo 2.35%, with the balance being Fe and unavoidable impurities.

[0087] The process parameters for the remaining steps S2-S6 (including the use of polycrystalline diamond drawing dies and surface polishing) are exactly the same as in Example 1. The preparation method of the metal-rubber molded parts is the same as in Example 1.

[0088] Comparative Example 2 This comparative example provides a method for preparing stainless steel wire, the only difference between which is the procedure and that of Example 1: the nitrogen (N) content in the cast billet is adjusted to be lower than that of this invention, while maintaining the content of all other alloying elements similar to that of Example 1 and all process parameters exactly the same as those of Example 1. Specifically, as follows: S1. Smelting and continuous casting: The chemical composition of the billet by weight percentage is: C 0.09%, N 0.35%, Si 0.28%, Mn 15.68%, P 0.021%, S 0.002%, Cr 21.09%, Ni 1.13%, Cu 0.24%, with the balance being Fe and unavoidable impurities.

[0089] The process parameters for the remaining steps S2-S6 are exactly the same as in Example 1. The preparation method of the metal-rubber molded part is the same as in Example 1.

[0090] Comparative Example 3 This comparative example provides a method for preparing stainless steel wire, the only difference between this method and Example 1 being: adjusting the nitrogen (N) content in the cast billet to be higher than that of this invention, while maintaining the content of all other alloying elements similar to that of Example 1 and ensuring all process parameters are exactly the same as in Example 1. Specifically, as follows: S1. Smelting and continuous casting: The chemical composition of the billet by weight percentage is: C 0.10%, N 0.80%, Si 0.25%, Mn 15.75%, P 0.027%, S 0.003%, Cr 21.11%, Ni 1.16%, Cu 0.22%, with the balance being Fe and unavoidable impurities.

[0091] The process parameters for the remaining steps S2-S6 are exactly the same as in Example 1. Due to the excessively high nitrogen content in the billet in Comparative Example 3, there are many pores in the billet, which often crack during subsequent hot rolling, making it impossible to obtain finished steel wire.

[0092] Comparative Example 4 This comparative example provides a method for preparing stainless steel wire, the difference between which is that the surface grinding and polishing in step S6 is omitted, and only cleaning is performed. Specifically: In step S6, the steel wire obtained by the final drawing is only cleaned, without surface grinding or polishing.

[0093] All other process steps and parameters are exactly the same as in Example 1. The preparation method of the metal-rubber molded parts is the same as in Example 1.

[0094] Performance testing: To comprehensively evaluate the overall performance of the high-performance stainless steel wire and its metal-rubber molded parts provided by this invention, systematic performance tests and comparative analyses were conducted on the finished steel wires and molded parts provided in each embodiment and comparative example. The test items included: surface quality of the steel wire (roughness Ra value), basic mechanical properties (tensile strength and elongation after fracture), microstructure observation, and accelerated fatigue performance of the metal-rubber molded parts made from it. Specific test methods, results, and analyses are as follows: 1. Testing of steel wire surface quality and basic mechanical properties Surface roughness test: The arithmetic mean (Ra value) of the surface profile deviation of the finished steel wire was measured using an OLYMPUS LEXT OLS3000 laser confocal microscope. The measurement results are as follows: Figure 6-8 As shown in Table 1.

[0095] Room temperature tensile properties test: According to HB 5177-1996 "Metallic wires - Tensile testing method", samples of finished steel wires were taken for room temperature tensile tests to determine their tensile strength and elongation after fracture. The test results are shown in Table 1.

[0096] Table 1 Data Analysis: Figure 6 , 7 Figures 8 and 9 respectively show the surface 3D morphology and laser confocal microscopy test results of Example 1 (Ra=0.156μm), Example 5 (Ra=0.572μm), and Comparative Example 4 (Ra=1.291μm). It can be observed that the surface of Sample 1 is smooth with virtually no unevenness, while the surface of Sample 5 exhibits some fluctuations and a stepped morphology, indicating the presence of some shallow drawing marks. The surface of Sample 4 shows obvious undulations and unevenness, exhibiting more drawing defects and deeper drawing marks. Based on the images, it can be determined that the calculated Ra value corresponds well with the actual surface roughness of the samples, and has high reference value.

[0097] As shown in Table 1, Example 1, the metal-rubber stainless steel wire prepared using the method of this invention has an austenitic + martensite microstructure, a smooth surface, and an Ra value of 0.156 μm, exhibiting high tensile strength (2198 MPa) and good elongation after fracture (2.22%). Combined with the data from Example 3, it can be seen that adjusting the hot rolling temperature within a certain range can yield stainless steel wires with excellent surface quality, tensile strength, and elongation after fracture. Example 2 shows that reducing the content of various alloying elements within a certain range will cause a slight decrease in tensile strength and elongation after fracture. The data from Example 4 shows that using a fixed-duration annealing during the drawing process also causes a decrease in tensile strength and elongation after fracture, presumably due to excessively long annealing time leading to grain coarsening. In Example 5, changing the drawing die to a cemented carbide die resulted in a significant increase in the Ra value, reaching 0.572 μm, indicating a substantial increase in the surface roughness of the stainless steel wire. Comparative Example 1 changed the steel material to 316 stainless steel, and it can be seen that under the same process, its strength and plasticity are lower than the high-performance stainless steel wire designed in this invention. Comparative Example 2 significantly reduced the nitrogen content (0.35%) in the steel wire, which is the main strengthening element, resulting in a complete martensitic microstructure and a significant decrease in tensile strength and elongation after fracture. Comparative Example 3 increased the target nitrogen content (0.80%) in the steel wire. During the production process, due to the excessively high nitrogen content in Comparative Example 3, the supersaturated nitrogen was released as gas during the cooling process of the molten steel to form a billet. It did not have time to float to the surface and solidified before remaining in the billet, forming a large number of pores. The billet cracked frequently during subsequent hot rolling, and finished steel wire could not be obtained. Comparative Example 4 did not undergo surface grinding and polishing, and the Ra value increased significantly, reaching 1.291 μm.

[0098] 2. Accelerated fatigue performance testing of metal-rubber molded parts Test method: Standard metal-rubber molded parts were made from the finished steel wires prepared in the various embodiments and comparative examples (preparation method is the same as in Example 1). Accelerated fatigue tests were conducted on an HDT105B electro-hydraulic servo fatigue testing machine. The test conditions were: cyclic compression, cosine wave displacement waveform, maximum displacement 1.5 mm, frequency 4 Hz, and cumulative loading time 30 minutes.

[0099] Evaluation indicators: The mass of the molded parts is accurately weighed before and after the test, and the weight loss rate is calculated as a quantitative indicator to evaluate its wear resistance and fatigue spalling resistance. The lower the weight loss rate, the better the fatigue performance. Simultaneously, the macroscopic morphology of the sample after the fatigue test is observed. Figure 9-11 ).

[0100] Table 2 Data Analysis: Figure 9 , 10Images 1 and 11 respectively show physical photographs of the metal-rubber components after fatigue in Examples 1, 1, and 4. Figure 9 As can be seen, in Example 1, the metal rubber prepared using the method of the present invention maintained its structural integrity after fatigue testing, with no obvious broken filament areas. Figure 10 The metal rubber made from 316 stainless steel wires on display shows some fatigue damage areas, such as some loose and broken wire areas on the edge, and side burrs in the upper left corner. Figure 11 The image shows the morphology of metal rubber made from stainless steel wire that has not been polished and has poor surface quality after fatigue testing. There are obvious broken wire areas in the upper left and lower right parts, indicating poor fatigue performance.

[0101] As shown in Table 2, the metal rubber prepared using the method of this invention exhibits excellent fatigue performance, with a weight loss rate of only 0.371% after accelerated fatigue testing. Combined with the data in Table 1, it can be found that the surface roughness, tensile strength, and elongation of the stainless steel wire all have a certain impact on the fatigue performance of the metal rubber component. As shown in Example 5 and Comparative Example 4, changing the drawing die or omitting the grinding and polishing steps significantly increases the surface roughness of the stainless steel wire, and its fatigue performance also decreases substantially. In Example 4, the longer annealing time leads to a decrease in the strength and elongation of the steel wire, which also has a certain impact on fatigue performance. The metal rubber made from the 316 stainless steel wire used in Comparative Example 1 has lower strength and elongation, and its fatigue performance is significantly lower than that of the metal rubber made from the high-performance stainless steel wire prepared in this invention. Comparative Example 2, which reduces the nitrogen content in the stainless steel wire, has a lower elongation (1.28%) and lower tensile strength (1854 MPa), and its fatigue performance is also significantly lower than that of the metal rubber made from the high-performance stainless steel wire prepared in Example 1 of this invention.

[0102] Finally, it should be noted that the above embodiments are only used to illustrate the technical solutions of the present invention, and not to limit them; although the present invention has been described in detail with reference to the foregoing embodiments, those skilled in the art should understand that modifications can still be made to the technical solutions described in the foregoing embodiments, or equivalent substitutions can be made to some or all of the technical features; and these modifications or substitutions do not cause the essence of the corresponding technical solutions to deviate from the scope of the technical solutions of the embodiments of the present invention.

Claims

1. A method for preparing stainless steel wire for use in metal rubber, characterized in that, Includes the following steps: S1. Smelting and continuous casting: Smelting is carried out using an electric arc furnace, an argon-oxygen decarburization furnace and a ladle refining furnace, and manganese-nitrogen alloying is carried out during the smelting process, followed by continuous casting to obtain a billet; S2. Hot rolling and cooling of wire rod: The billet is first heated and then hot rolled to obtain wire rod, which is then cooled. S3. Drawing and intermediate heat treatment: The wire rod is drawn and then subjected to hydrogen bright annealing; the drawing and annealing process is repeated until the steel wire of the target size is obtained; S4. Surface finishing: The drawn steel wire is ground and polished to obtain the stainless steel wire; The chemical composition of the billet by weight percentage is as follows: C: 0.08%-0.12%, N: 0.65%-0.70%, Si: 0.10%-0.30%, Mn: 15.00%-17.00%, P: ≤0.03%, S: ≤0.008%, Cr: 21.00%-23.00%, Ni: 1.00%-1.30%, Cu: ≤0.30%, with the balance being Fe and unavoidable impurities.

2. The preparation method according to claim 1, characterized in that, In step S1, the manganese-nitrogen alloying during the smelting process includes: bottom blowing nitrogen gas throughout the argon-oxygen decarburization furnace smelting process, and adding electrolytic manganese during the reduction stage to make the manganese content in the molten steel reach 12.00%-14.00% and the nitrogen content reach 0.40%-0.50%, and then adding manganese nitride during the ladle refining furnace smelting process to carry out the manganese-nitrogen alloying.

3. The preparation method according to claim 1 or 2, characterized in that, In step S1, the continuous casting process adopts superheated casting to maintain the temperature of molten steel in the continuous casting tundish at 1400℃-1430℃, and electromagnetic stirring is used.

4. The preparation method according to claim 1, characterized in that, In step S2, the heating temperature is 1200℃-1300℃, and the heating time is 2-4 hours; And / or, the inlet temperature of the hot-rolled finishing mill is 1040℃-1090℃; And / or, the hot-rolled wire drawing temperature is 1000℃-1040℃; And / or, the cooling is water cooling to room temperature; and / or, The diameter (φ) of the wire rod is 6.4mm-6.6mm.

5. The preparation method according to claim 1, characterized in that, After step S2 and before step S3, the process also includes a surface pretreatment step for the wire rod, which includes peeling and a first hydrogen bright annealing. The first hydrogen bright annealing uses hydrogen with a purity of 99.99%-99.999% and a dew point of <-60℃, an annealing temperature of 1050℃-1080℃, a holding time of 10-20 min, and water quenching after holding.

6. The preparation method according to claim 1, characterized in that, In step S3, the drawing process is performed using a polycrystalline diamond drawing die; And / or, the number of passes for each drawing operation is 4-6, the deformation rate of each pass does not exceed 30%, and the total deformation rate of each drawing operation is 70%-80%; And / or, the hydrogen bright annealing is a second hydrogen bright annealing, wherein the hydrogen used in the second hydrogen bright annealing has a purity of 99.99%-99.999%, a dew point of <-60℃, an annealing temperature of 1050℃-1080℃, and a holding time t (min) that satisfies the formula: t=2+2R / 3, where R is the diameter of the wire before annealing, and the unit of the diameter is mm; And / or, step S4 may also include cleaning the polished steel wire.

7. The preparation method according to claim 1, characterized in that, The target diameter (φ) of the steel wire obtained in step S3 is 0.27mm-0.33mm; And / or, after step S3 is completed, the tensile strength of the steel wire is 2050MPa-2250MPa, and the elongation after fracture is 1.7%-2.5%; And / or, after step S4 is completed, the surface roughness Ra value of the stainless steel wire is 0.1μm-0.3μm.

8. A stainless steel wire for use in metal rubber, characterized in that, It is prepared by any one of claims 1-7.

9. A metal-rubber molded part, characterized in that, It is made using the stainless steel wire for metal rubber as described in claim 8.

10. The metal-rubber molded part according to claim 9, characterized in that, The metal rubber molded part is made by the stainless steel wire used for metal rubber through the steps of winding into a spiral coil, winding into a blank, and stamping. During the process of winding the spiral coil, the diameter and pitch of the spiral coil are equal, both being 3.0mm-3.5mm; During the winding process of the blank, the amount of stainless steel wire used for the metal rubber is 40g-55g. During the stamping process, the stamping pressure is 8.0 ± 0.5 kN; The density of the metal-rubber molded part is 2.5 g / cm³. 3 -3.5g / cm 3 .

Images