GH4090 alloy cold wire drawing material and manufacturing method thereof

Abstract

The invention relates to a GH4090 alloy cold wire drawing material and a manufacturing method thereof, and belongs to the technical field of high-temperature alloy materials. The alloy cold wire drawing material comprises, by mass, 18.0%-21.0% of Cr, 15.0%-21.0% of Co, 1.0%-2.0% of Al, 2.0%-3.0% of Ti, less than or equal to 0.13% of C, Mn, Si, S, P, B, Zr, Fe, Cu, Ag, Bi, Pb, and the balance Ni and inevitable impurities, and the content of the Mn, the Si, the S, the P, the B, the Zr, the Fe, the Cu, the Ag, the Bi and the Pb is controlled. The manufacturing method comprises the steps of vacuum induction smelting of an electrode bar, electroslag remelting, homogenization treatment, forging cogging, wire rolling, multi-pass cold drawing and aging treatment. According to the method, the cold drawing deformation of each pass is controlled to be 30-40%, the deformation of the last pass is controlled to be larger than or equal to 35%, solid solution and acid pickling treatment is carried out before each pass, and finally aging treatment is carried out at the temperature of 600 + / -20 DEG C for 16 hours, so that the GH4090 alloy cold-drawn wire with excellent performance is obtained, and the GH4090 alloy cold-drawn wire can be widely applied to manufacturing of high-temperature parts in the fields of aerospace and energy.

Description

Technical Field

[0001] This invention relates to the field of alloy manufacturing technology, and more specifically, to a GH4090 alloy cold-drawn wire and its manufacturing method. Background Technology

[0002] GH4090 alloy is a nickel-based superalloy widely used in the manufacture of high-temperature components for aircraft engines, gas turbines, and nuclear power equipment. This alloy possesses excellent high-temperature strength, good oxidation resistance, and resistance to hot corrosion, making it particularly suitable for manufacturing high-temperature components operating at temperatures above 650℃.

[0003] Currently, the preparation process of nickel-based superalloys mainly includes vacuum induction melting, electroslag remelting, homogenization treatment, forging, rolling, and heat treatment. Chinese patent application CN111607721A discloses a method for preparing GH4169A alloy strip for nuclear power. This method involves vacuum induction melting followed by casting into electrode rods, then preparing alloy electroslag ingots through an atmosphere-protected electroslag remelting furnace. After homogenization treatment and forging, the ingots undergo hot rolling, welding, surface treatment, and cold rolling. Chinese patent application CN120330538A proposes a hot-rolled GH4751 alloy and its manufacturing method. This method uses a dual process of "vacuum induction melting + electroslag remelting" to prepare high-purity electrode rods. Combining forging and multi-pass temperature-controlled rolling with a two-stage aging treatment, it achieves uniform precipitation of the γ' strengthening phase and grain refinement.

[0004] In the field of high-temperature alloy wire processing, Chinese patent CN105483448B discloses a method for preparing nuclear-grade nickel-based high-temperature alloy GH4145 wire. This method involves vacuum induction and vacuum consumable metallurgy, casting the alloy into ingots, homogenizing them, forging them into alloy billets, hot rolling them into wire rods, and finally preparing alloy wire through solution treatment, drawing, and annealing. This method eliminates the need for pickling, meets the special requirements for nuclear applications, and produces finished wires with high dimensional accuracy and good surface quality.

[0005] Regarding alloy composition control, Chinese patent CN116732390B discloses an 80A alloy and its preparation method. This alloy solves the problem of uneven grain size and the inability to simultaneously meet the requirements of strength, yield strength, aging hardness, and impact performance of conventional 80A alloys by precisely controlling the content of elements such as C, Cr, Al, and Ti. CN114635058A proposes a nickel-based high-temperature alloy electroslag ingot and its manufacturing method, which uses the EF+AOD+LF+electroslag+homogenization process to prepare GH4145 alloy. This method has a low manufacturing cost and can be applied to the preparation of large disc-ring forgings in the fields of aerospace, nuclear power, and petroleum.

[0006] The existing technology still has the following problems in the preparation process of GH4090 alloy cold-drawn wire: During electroslag remelting, the loss of active elements such as Al and Ti varies significantly, especially with marked differences in their content at the beginning and end, leading to unstable performance of the finished wire and making it difficult to meet the consistency requirements of high-end applications. This non-uniformity in element content directly affects the distribution of the strengthening phase and the final properties of the alloy. During forging, as the temperature decreases, GH4090 alloy is prone to surface cracks. These cracks cannot be eliminated during subsequent hot working and must be ground before entering the rolling process, greatly reducing the material yield and production efficiency. The deformation control of cold-drawn wire is a key factor affecting the performance of the final product, but existing technologies lack systematic research on the deformation of GH4090 alloy cold-drawn wire, making it difficult to find the optimal deformation that can simultaneously meet both mechanical and performance indicators. Especially in multi-pass cold drawing, controlling the deformation of each pass and the final pass is crucial for obtaining cold-drawn wire with excellent performance.

[0007] Therefore, there is an urgent need to develop a method for preparing GH4090 alloy cold-drawn wire that can precisely control the alloy composition, optimize forging process parameters, and rationally design the amount of cold drawing deformation, in order to solve the above-mentioned technical problems and improve product quality and performance stability. Summary of the Invention

[0008] The technical problem to be solved by the present invention is to provide a GH4090 alloy cold-drawn wire to solve the problems of poor alloy composition uniformity, easy generation of hot working surface cracks, and difficulty in accurately controlling the amount of cold drawing deformation in conventional GH4090 alloy cold-drawn wires in the prior art.

[0009] To overcome the shortcomings of the prior art, the present invention provides a GH4090 alloy cold-drawn wire, comprising the following components by weight: Cr: 18.0%–21.0%, Co: 15.0%–21.0%, Al: 1.0%–2.0%, Ti: 2.0%–3.0%, C ≤0.13%, Mn ≤0.4%, Si ≤0.8%, S ≤0.015%, P ≤0.015%, B ≤0.02%, Zr ≤0.15%, Fe ≤1.50%, Cu ≤0.20%, Ag ≤0.0005%, Bi ≤0.0001%, Pb ≤0.001%, with the balance being Ni and other unavoidable impurities.

[0010] Compared with existing technologies, the GH4090 alloy cold-drawn wire of this application has the following advantages: The GH4090 alloy cold-drawn wire of this invention optimizes γ′ precipitation and cold deformation capability by rationally controlling the Al to Ti ratio (Al+Ti = 3.2%–4.4%, Ti / Al = 1.6–2.8), and the Cr to Co ratio (Co / Cr = ... The matrix stacking fault energy (0.85–1.25) is adjusted to ensure a good balance between plasticity and strength during cold drawing. In addition, the synergistic effect of B and Zr plays a toughening role at the grain boundaries. At the same time, the ultra-low content of impurities such as S, P, and Ag effectively prevents the formation of brittle cracks. Through the above optimization, the alloy composition of this invention can improve the yield strength and elongation of cold-drawn wire and ensure its stability during cold working. By quantitatively controlling the main strengthening elements, grain boundary strengthening elements, and harmful impurities of the alloy with coupling windows, room temperature plasticity and cold deformation stability are significantly improved while maintaining high strength. This solves the problems of yield strength-plasticity balancing difficulty, excessive work hardening, grain boundary embrittlement, and sensitivity to tensile cracking in traditional GH4090 cold-drawn wire during cold working.

[0011] In one possible implementation, the composition, by weight, includes the following components: Cr: 19.0–20.0%, Co: 17.5–18.5%, Al: 1.60–1.65%, Ti: 2.65–2.70%, C: 0.040–0.045%, Mn ≤0.005%, Si≤0.01%, S ≤0.001%, P ≤0.003%, B: 0.010–0.012%, Zr: 0.06–0.08%, Fe ≤0.20%, Cu ≤0.001%, Ag ≤0.0005%, Bi ≤0.0001%, Pb ≤0.001%, with the balance being Ni and other unavoidable impurities.

[0012] Compared with existing technologies, the above-mentioned technical solution, through further refinement of the composition ratio, including the precise control of the ratio of Cr and Co, as well as Al and Ti, further improves the high-temperature strength and cold-drawing performance of the alloy: by stabilizing the Cr content between 19.0% and 20.0% and controlling the Co to Cr ratio between 0.92 and 0.98, the matrix stacking fault energy of the alloy is optimized, enhancing its plasticity during cold drawing and avoiding brittle fracture of the material during cold drawing. Simultaneously, the precise ratio of Al and Ti further optimizes γ′ precipitation in the alloy. Compared with traditional solutions, the optimized ratio of Ti to Al (Ti:Al = 1.65:1) not only improves the heat resistance of the alloy but also effectively enhances its resistance to deformation during cold drawing, ensuring higher strength and ductility. Furthermore, the above implementation further controls the content of impurities such as Mn, Si, S, P, and Cu to extremely low levels (e.g., Mn ≤ 0.005%, S ≤ 0.005%). With an impurity content of ≤0.001%, the adverse effects on the mechanical properties of the alloy are avoided, ensuring good toughness and uniformity of the alloy material. While improving mechanical properties, the low impurity content also effectively prevents problems such as brittle fracture and crack propagation, further ensuring the stability and reliability of the material. By precisely controlling the interaction of each element, the comprehensive performance of GH4090 alloy cold-drawn wire is improved, solving the problems of unstable performance and difficult processing of cold-drawn wire in the existing technology.

[0013] The technical problem to be solved by the present invention is to provide a manufacturing method for GH4090 alloy cold-drawn wire, so as to solve the problems of uneven alloy composition, poor cold drawing performance and high material brittleness of conventional GH4090 alloy cold-drawn wire in the prior art.

[0014] To overcome the shortcomings of the prior art, the present invention provides a method for manufacturing the GH4090 alloy cold-drawn wire, comprising the following steps: S1: Vacuum induction smelting electrode rod: The raw material is loaded into the vacuum induction furnace, the furnace temperature is controlled at 1520±10℃, the vacuum is drawn and the power is supplied to melt the steel; the temperature of the steel is reduced to 1480±10℃, and the refining period is entered. Al and Ti are added to further smelt the steel, and the refining is ended. The electrode rod is cast at 1500±10℃. S2: Electroslag remelting: After pretreatment of the electrode rod, further electroslag remelting is performed to obtain an electroslag ingot; S3: Homogenization treatment: The electroslag ingot is homogenized at 1180±10℃; S4: Forging billet: The electroslag ingot is cooled to 1150±10℃ and held at that temperature, then drawn into a square billet and air-cooled after forging. S5: Rolled wire: The billet is heated to 1150±10℃ and held for 2 hours, and then rolled into wire by continuous rolling. S6: Multi-pass cold drawing: The wire is cold-drawn in multiple passes to obtain cold-drawn filament, and the deformation amount of each pass is controlled at 30-40%. Solution treatment and pickling are performed before each pass, and the deformation amount of the last pass is controlled at ≥35%. S7: Aging treatment: The cold-drawn wire is subjected to aging treatment to obtain GH4090 alloy cold-drawn wire.

[0015] Compared with existing technologies, the manufacturing method of GH4090 alloy cold-drawn wire disclosed in this application has the following advantages: The entire manufacturing process of this invention ensures the excellent performance of GH4090 alloy cold-drawn wire through the synergistic effect of multiple refined steps. Specifically, in the vacuum induction smelting process, the raw materials are melted at high temperatures in a vacuum environment. During the refining process, alloying elements, including aluminum and titanium, are added, and impurities are further removed to ensure the uniformity of the alloy composition. This lays the foundation for subsequent electroslag remelting and homogenization treatment. In the electroslag remelting, residual impurities are further removed, and the alloy is made purer by refining the grains. The homogenization treatment eliminates macroscopic segregation, making the material more stable in subsequent processing. Furthermore, in the forging and billet opening stage, the billet is controlled... Forging at a controlled temperature further optimizes the alloy's microstructure and improves its machinability. In the subsequent wire rod rolling stage, precise control of rolling temperature and deformation refines the grain size, ensuring smooth cold drawing. During cold drawing, multiple passes of gradual deformation not only increase the material's strength but also improve surface quality, while providing a better microstructure for aging treatment. Finally, aging treatment, with appropriate temperature and time control, optimizes the alloy's strength and high-temperature stability, ensuring long-term stability in practical applications. Each stage of the manufacturing process complements the others; from smelting, forging, and rolling to cold drawing and aging treatment, each step is meticulously controlled to ensure the high performance of the final product.

[0016] In one possible implementation, in step S1, the conditions for vacuuming and powering the melting process are: controlling the vacuum level in the furnace to be ≤5Pa, the vacuum level during the refining period to be ≤1.0Pa, and the early stage of the refining period also includes an operation of electromagnetic stirring of the molten steel. The conditions for casting are: maintaining the vacuum level to be ≤1.0Pa during the casting process.

[0017] Compared with existing technologies, the above-mentioned technical solution can strictly control the vacuum level in the furnace throughout the entire smelting cycle, ensuring that the molten steel is always in an extremely low oxygen and low nitrogen environment, minimizing the dissolution of harmful gases. During the refining period, by further controlling the vacuum level to ≤1.0 Pa and supplementing it with electromagnetic stirring, internal convection of the molten steel can be promoted, accelerating the floating of gases and non-metallic inclusions. Combined with vacuum extraction, efficient deoxidation, denitrification, and inclusion removal are achieved. Especially during the Al and Ti addition stage, due to the high vacuum state of the smelting environment, the burn-off ratio of active elements such as Al and Ti is significantly reduced, improving the accuracy of element composition control and reducing composition fluctuations at the beginning and end. Furthermore, by maintaining a vacuum level of ≤1.0 Pa during the casting process, secondary oxidation and inclusion formation caused by contact between the molten steel and air are effectively prevented, further improving the purity and compositional uniformity of the electrode rod.

[0018] In one possible implementation, step S2 includes: polishing the surface of the electrode rod to remove the surface oxide layer, cutting off 50 mm from the casting end of the electrode rod, and then welding a transition electrode.

[0019] Compared with existing technologies, the above-mentioned technical solution can remove the oxide layer, slag, and inclusions on the surface of the electrode rod by mechanical polishing before electroslag remelting, thus preventing the introduction of surface inclusions and oxides into the molten pool during the remelting process. At the same time, cutting off 50mm of the casting end of the electrode rod can eliminate shrinkage cavities, porosity, and severe component segregation areas that may exist at the solidification end, preventing these defects from entering the steel ingot during the remelting process. Welding the transition electrode can ensure stable arc ignition and good conductivity during electroslag remelting, avoiding problems such as metal spatter or local overheating caused by unstable arc.

[0020] In one possible implementation, the homogenization treatment in step S3 is performed by heating the electroslag ingot to 1180±10℃ after 6 hours and holding it at that temperature for 30 hours.

[0021] Compared with existing technologies, the above-mentioned technical solution can achieve slow and uniform heating of electroslag ingots over a longer heating period, reducing the temperature gradient and avoiding internal stress concentration caused by rapid heating. Furthermore, holding at a high temperature of 1180±10℃ for 30 hours can significantly promote the full diffusion of elements such as aluminum, titanium, chromium, and cobalt within the grains and grain boundaries, effectively reducing or eliminating dendrite segregation and compositional inhomogeneity formed during solidification, and making the precipitation conditions of strengthening phases more consistent. Simultaneously, the prolonged high-temperature holding promotes the spheroidization and refinement of primary carbides and inclusions, improving deformation coordination during subsequent plastic processing. The direct effect is to obtain high-quality forging billets with uniform composition, dense microstructure, and uniform grain size.

[0022] In one possible implementation, during step S5, the rolling temperature is 980–1070°C during the continuous rolling process.

[0023] Compared with the prior art, the above technical solution can achieve coordinated matching of surface and core temperatures during rolling by controlling the continuous rolling temperature within the range of 980–1070℃. This avoids the core temperature from exceeding the overheating critical temperature (1180℃) of the GH4090 alloy, which would result in central porosity or voids. It also prevents the work hardening caused by excessively low temperatures and the sharp increase in deformation resistance. Within the temperature range of the above implementation method, the material is in the optimal thermoplastic window, with sufficient dynamic recrystallization and significant grain refinement, which helps to obtain a fine and uniform recrystallized structure.

[0024] In one possible implementation, in step S6, the number of passes is 8, and the weight of the cold-drawn wire is 20-25 kg.

[0025] Compared with existing technologies, the above-mentioned technical solution, by setting up eight progressive cold drawing deformation stages, ensures that the deformation amount in each stage is within a reasonable range (30-40%). This effectively induces work hardening to improve strength while avoiding excessive deformation that could lead to localized strain concentration and microcrack initiation. Furthermore, setting the deformation amount in the final stage to ≥35% provides a larger strength margin after standard aging treatment, while also considering elongation and toughness. Controlling the weight of a single coil of finished product to 20-25 kg promotes uniform stress on the wire during cold drawing, reduces load fluctuations on the drawing equipment, and facilitates rapid replacement and stable wire supply in subsequent applications. The direct effect is that the strength, plasticity, and surface quality of the produced wire are balanced and controllable, with minimal performance fluctuations across batches.

[0026] In one possible implementation, the conditions for the solution treatment and pickling in step S6 include: placing the wire into a heat treatment furnace, heating it to 1050±10℃ and holding it at that temperature for 0.5-1.0 hours, removing it from the furnace and water cooling it, followed by pickling to remove the surface oxide scale, and then washing it with water and drying it.

[0027] Compared with existing technologies, the above-mentioned technical solution, by holding at the optimal solution temperature of 1050±10℃ for 0.5-1.0 hours, can further allow the γ′ phase, carbides and other reinforcing phases in the GH4090 alloy to fully dissolve into the matrix, eliminate work hardening and dislocation accumulation caused by cold working, and restore the plasticity of the material. Furthermore, by holding at high temperature and then rapidly water cooling after exiting the furnace, high-temperature oxidation and phase re-precipitation can be suppressed, resulting in a fine and uniform solution structure. Subsequently, pickling can efficiently remove the surface oxide scale and residue formed during the solution treatment, exposing a clean metal surface and avoiding defects such as scratches, surface cracks or inclusions caused by oxide scale peeling during subsequent cold drawing.

[0028] In one possible implementation, in step S7, the aging treatment conditions are: the cold-drawn wire is kept at a temperature of 600±20℃ for 16 hours, followed by air cooling.

[0029] Compared with existing technologies, the above-mentioned technical solution, under the condition of holding at 600±20℃ for 16 hours, can further induce the orderly precipitation of fine and dispersed γ′ reinforcing phases from the supersaturated dissolved Al, Ti, and other elements in the matrix after solution treatment. This, in synergy with previous steps, precipitates an appropriate amount of stable carbides at the grain boundaries, thereby significantly improving the yield strength and high-temperature creep strength of the material. Controlling the lower aging temperature and longer holding time can avoid coarsening of the reinforcing phase and over-aging, maintaining excellent comprehensive mechanical properties. Simultaneously, moderate aging precipitation can also release some residual stress from cold drawing, improving the dimensional stability and service stability of the material. Detailed Implementation

[0030] First, those skilled in the art should understand that these embodiments are merely used to explain the technical principles of the embodiments of this application and are not intended to limit the scope of protection of the embodiments of this application. Those skilled in the art can make adjustments as needed to adapt to specific application scenarios.

[0031] This invention provides a GH4090 alloy cold-drawn wire, comprising the following components by weight: Cr: 18.0%–21.0%, Co: 15.0%–21.0%, Al: 1.0%–2.0%, Ti: 2.0%–3.0%, C ≤0.13%, Mn ≤0.4%, Si ≤0.8%, S ≤0.015%, P ≤0.015%, B ≤0.02%, Zr ≤0.15%, Fe ≤1.50%, Cu ≤0.20%, Ag ≤0.0005%, Bi ≤0.0001%, Pb ≤0.001%, with the balance being Ni and other unavoidable impurities.

[0032] As a preferred embodiment, the composition by weight includes the following components: Cr: 19.0–20.0%, Co: 17.5–18.5%, Al: 1.60–1.65%, Ti: 2.65–2.70%, C: 0.040–0.045%, Mn ≤0.005%, Si ≤0.01%, S ≤0.001%, P ≤0.003%, B: 0.010–0.012%, Zr: 0.06–0.08%, Fe ≤0.20%, Cu≤0.001%, Ag ≤0.0005%, Bi ≤0.0001%, Pb ≤0.001%, with the balance being Ni and other unavoidable impurities.

[0033] This invention also provides a method for manufacturing the above-mentioned GH4090 alloy cold-drawn wire, comprising the following steps: S1: Vacuum induction smelting electrode rod The raw materials are melted into molten steel using a vacuum induction furnace, and the steel is refined by controlling the furnace temperature and vacuum level. The vacuum level is controlled to ≤5 Pa during this step, and ≤1.0 Pa during the refining stage. The molten steel is electromagnetically stirred before the refining stage to ensure the uniformity of the alloy composition. Maintaining a vacuum level of ≤1.0 Pa during the steel casting stage helps reduce oxide inclusions and gas dissolution, improves material purity, and ensures the uniformity of the alloy's microstructure.

[0034] S2: Electroslag Remelting After pretreatment, the electrode rods are electroslag remelted to further refine the alloy, remove impurities, and improve the compositional uniformity and grain refinement of the alloy.

[0035] S3: Homogenization Process After homogenization treatment, electroslag ingots can further eliminate macroscopic segregation generated during casting and forging, improve the overall uniformity of the alloy structure, and ensure stability during subsequent cold drawing.

[0036] S4: Forging blank The electroslag ingot is cooled to 1150±10℃ and then forged into a square billet, laying the foundation for subsequent rolling and cold drawing processes. Air cooling is used in this stage to help maintain the alloy's toughness and avoid brittleness caused by excessively high cooling rates.

[0037] S5: Rolled wire After being heated, the billet is rolled into wire using a continuous rolling process. This stage involves precise control of the rolling temperature and time to ensure that the grain size and microstructure of the material are suitable for subsequent cold drawing.

[0038] S6: Multi-pass cold drawing By performing cold drawing in multiple passes, with the deformation amount controlled at 30-40% in each pass, and solution treatment and pickling before each pass, the surface finish and internal structure uniformity of the wire are maintained. In particular, the deformation amount in the final pass is ≥35%, and the higher deformation amount promotes grain refinement, thereby improving the strength and ductility of the cold-drawn wire.

[0039] S7: Timeliness Processing Finally, the cold-drawn wires, after aging treatment, can obtain the final required mechanical properties, ensuring their stability and corrosion resistance at high temperatures.

[0040] In step S1, the conditions for vacuuming and powering the melting process are: controlling the vacuum degree in the furnace to be ≤5Pa, the vacuum degree during the refining period to be ≤1.0Pa, and the early stage of the refining period also includes electromagnetic stirring of the molten steel. The conditions for casting are: maintaining the vacuum degree to be ≤1.0Pa during the casting process.

[0041] As a preferred embodiment, in step S2, the pretreatment includes: polishing the surface of the electrode rod to remove the surface oxide layer, cutting off 50mm from the casting end of the electrode rod, and then welding a transition electrode.

[0042] As a preferred embodiment, in step S3, the homogenization treatment conditions are as follows: the electroslag ingot is heated to 1180±10℃ after 6 hours and kept at that temperature for 30 hours.

[0043] As a preferred embodiment, in step S5, the rolling temperature during the continuous rolling process is 980–1070℃.

[0044] As a preferred embodiment, in step S6, the number of passes is 8, and the weight of the cold-drawn wire is 20-25 kg.

[0045] As a preferred embodiment, in step S6, the conditions for the solution treatment and pickling include: placing the wire into a heat treatment furnace, heating it to 1050±10℃ and holding it at that temperature for 0.5-1.0 hours, removing it from the furnace and water cooling it, followed by pickling to remove the surface oxide scale, and then washing it with water and drying it.

[0046] As a preferred embodiment, in step S7, the aging treatment conditions are as follows: the cold-drawn wire is kept at a temperature of 600±20℃ for 16 hours, followed by air cooling.

[0047] The beneficial effects of this invention are as follows: 1. By using high-purity steel ingot manufacturing technology, the quantity and grade of non-metallic inclusions in steel are reduced, avoiding defects such as surface cracks and peeling during wire bending and torsion inspections. Compared with existing technologies, the method of combining vacuum induction smelting and electroslag remelting adopted in this invention effectively controls the content fluctuations of easily burnable elements such as Al and Ti, resulting in more uniform performance of the finished wire. 2. By employing a reasonable wire rolling process and online cooling technology, the surface temperature during the rolling process is controlled between 980-1070℃, and the core temperature is at most 1130℃, which is lower than the material's overheating temperature of 1180℃. This avoids voids in the center of the wire and achieves successful rolling in one pass. Compared with traditional processes, the rolling temperature control of this invention is more precise, effectively solving the problem of surface cracks that are prone to occur during forging. 3. By controlling the final deformation of the cold-drawn wire to 40.83%, the mechanical and performance properties of the wire are ensured to be qualified. The room temperature tensile properties reach 1662MPa and 1636MPa, exceeding the standard requirement of 1540MPa. The performance properties such as torsion, winding, and repeated bending are also qualified. This invention successfully solves the technical problem of the need to explore the deformation amount of cold-drawn wire by precisely controlling the deformation amount. 4. This invention successfully produces GH4090 alloy wire products with good surface quality, mechanical properties, and performance, meeting the application requirements of high-temperature alloy wires in aerospace and other fields.

[0048] The following embodiments, incorporating specific data, are provided in conjunction with the above-described technical solutions to further elaborate on the technical solutions of the present invention: Example 1 This embodiment provides a GH4090 alloy cold-drawn wire. The composition of the cold-drawn wire, by weight ratio, is as follows: Cr: 19.5%, Co: 18.0%, Al: 1.62%, Ti: 2.68%, C: 0.042%, Mn: 0.003%, Si: 0.008%, S: 0.0008%, P: 0.002%, B: 0.011%, Zr: 0.07%, Fe: 0.15%, Cu: 0.0008%, Ag: 0.0002%, Bi: 0.00005%, Pb: 0.0005%, with the balance being Ni and other unavoidable impurities.

[0049] The preparation method of this GH4090 alloy cold-drawn wire includes the following steps: S1: Vacuum induction smelting electrode rod: The raw material is loaded into a vacuum induction furnace, the furnace temperature is controlled at 1520±10℃, a vacuum is drawn and electricity is supplied to melt the steel; the temperature of the steel is reduced to 1480±10℃, and the refining period begins. Al and Ti are added for further smelting, and the refining process ends. The electrode rod is then cast at 1500±10℃.

[0050] In this embodiment, the conditions for vacuuming and electrifying melting are: controlling the vacuum level inside the furnace to ≤5 Pa, the vacuum level during the refining period to ≤1.0 Pa, and the early stage of the refining period also includes electromagnetic stirring of the molten steel. The conditions for casting are: maintaining a vacuum level ≤1.0 Pa during the casting process. Specifically, the vacuum level inside the furnace is controlled at 4.5 Pa, the vacuum level during the refining period is controlled at 0.8 Pa, and the vacuum level during the casting process is controlled at 0.9 Pa. The electromagnetic stirring operation helps to homogenize the composition of the molten steel and improve the alloy quality.

[0051] S2: Electroslag remelting: After pretreatment of the electrode rod, it is further electroslag remelted to obtain an electroslag ingot with an ingot diameter of Φ360mm.

[0052] In this embodiment, the pretreatment includes: polishing the surface of the electrode rod to remove the surface oxide layer, cutting off 50 mm from the casting end of the electrode rod, and then welding a transition electrode. The surface polishing treatment ensures that the electrode rod surface is free of defects, cutting off the casting end can remove defective areas that may have been generated during the casting process, and welding the transition electrode facilitates the subsequent electroslag remelting operation.

[0053] S3: Homogenization treatment: The electroslag ingot is homogenized at 1180±10℃.

[0054] In this embodiment, the homogenization treatment conditions are as follows: the electroslag ingot is heated to 1180±10℃ after 6 hours and held at that temperature for 30 hours. Specifically, the temperature is controlled at 1175℃, and the holding time is 30 hours. The purpose of the homogenization treatment is to eliminate component segregation in the alloy and make the alloy structure more uniform.

[0055] S4: Forging and billet opening: Cool the electroslag ingot to 1150±10℃ and hold it at that temperature. Lengthen and open the billet to a 140*140*Lmm square billet. After forging, air cool it. Divide the aforementioned billet into sections with a length controlled at 2100mm-2600mm and a single weight of about 370Kg.

[0056] S5: Rolled wire rod: The billet is heated to 1150±10℃ and held for 2 hours. It is then rolled into Φ6.5mm coils in one pass on a continuous rolling mill. After rolling, the coils are bundled and air-cooled to room temperature.

[0057] In this embodiment, the rolling temperature during continuous rolling is 980–1070℃. Specifically, the initial rolling temperature is 1065℃, and the final rolling temperature is 985℃. Rolling within this temperature range yields good microstructure and mechanical properties.

[0058] S6: Multi-pass cold drawing: The wire is cold-drawn in multiple passes to obtain cold-drawn wire, and the deformation amount of each pass is controlled at 30-40%. Solution treatment and pickling are performed before each pass, and the deformation amount of the last pass is controlled at ≥35%.

[0059] In this embodiment, the cold drawing process is performed in 8 passes, drawing the wire to Φ1.0mm in 8 passes, and the weight of the cold-drawn wire is 20-25kg. In specific implementation, the cold drawing is performed 8 times, and the deformation amount for each pass is shown in Table 1 below. The final weight of the cold-drawn wire is 23kg.

[0060] Table 1 Cold drawing passes and deformation per pass for wire In this embodiment, the conditions for solution treatment and pickling include: placing the wire into a heat treatment furnace, heating it to 1050±10℃ and holding it at that temperature for 0.5-1.0 hours, then removing it from the furnace and water cooling it, followed by pickling to remove the surface oxide scale, and then washing it with water and air drying it. In specific implementation, the solution temperature is 1055℃, the holding time is 0.8 hours, the pickling uses a mixed acid solution of sulfuric acid and nitric acid, and after pickling, it is immediately rinsed with clean water and air dried.

[0061] S7: Aging treatment: Sampling: Select any 2 coils from the above S6 steps, and cut 1 piece of 500mm length and 3 pieces of 150mm length from one end of the wire respectively. Perform aging treatment on the cold-drawn wire to obtain GH4090 alloy cold-drawn wire.

[0062] In this embodiment, the aging treatment conditions are as follows: the cold-drawn wire is kept at a temperature of 600±20℃ for 16 hours, followed by air cooling. Specifically, the aging temperature is 605℃, the holding time is 16 hours, and then it is naturally cooled in the air. Aging treatment can make the alloy obtain good microstructure and properties, and improve the strength and stability of the alloy.

[0063] In Example 1, the implementation principle and key points of the preparation method are as follows: (1) Manufacturing high-purity steel ingots to avoid defects such as surface cracks and peeling during bending and torsion inspections: (2) During the vacuum induction melting stage, an appropriate amount of carbon is added. Utilizing the principle that carbon reacts with oxygen to generate CO (carbon monoxide) under vacuum conditions, and taking advantage of CO's extremely low solubility in molten steel and its ease of evacuation, efficient deoxidation is achieved, significantly reducing the oxygen content in the molten steel. During the refining stage, high vacuum and electromagnetic stirring technology are combined at a suitable refining temperature to promote full convection of the molten steel, accelerating the floating and removal of gases and non-metallic inclusions, thereby further purifying the molten steel. During the casting stage, the runner chamber and ingot mold chamber are evacuated to a high vacuum (≤1.0 Pa) to effectively suppress secondary oxidation and inclusion contamination of the molten steel during casting, ensuring the acquisition of electrode rods with stable composition and high purity. Through the above measures, the quantity and grade of non-metallic inclusions in the steel are significantly reduced, thereby avoiding defects such as surface cracks and peeling caused by inclusions during bending, twisting, and other inspections of the wire.

[0064] (2) A reasonable wire rolling process to avoid voids in the center of the wire and ensure successful rolling in one pass: In the rolling of small-diameter wire rods of high-temperature alloys, due to their poor thermal conductivity and high rolling speed, the frictional heat generated during rolling can easily lead to a significant increase in the core temperature. If this temperature exceeds the material's overheating temperature, void defects can easily form in the core, resulting in scrap. Addressing the overheating temperature of GH4090 alloy (1180℃), this invention introduces online cooling technology during the actual rolling process and precisely controls the surface temperature to remain between 980 and 1070℃ throughout the entire process. Calculations show that the highest core temperature is only 1130℃, significantly lower than the overheating threshold. This effectively avoids overheating and the formation of central voids, ensuring the one-time rolling forming and yield of small-diameter wire rods.

[0065] (3) Control the deformation of the cold-drawn wire in the last pass to ensure that the final performance meets the standards. The final deformation of cold-drawn filaments is a core process parameter determining the final mechanical and performance properties of the material. In this invention, before the final cold drawing, the filaments are first subjected to solution treatment and pickling at 1050℃ for 0.5–1.0 hours to restore processing plasticity and remove surface oxide scale. Based on this, the final cold drawing deformation is controlled to be above 35%, which effectively ensures that the tensile, bending, torsion, and winding properties of the filaments meet all standards after subsequent standard aging treatment. This invention preferably uses a final deformation of 40.83%, which not only ensures qualified room temperature tensile properties with a significant margin, but also maintains excellent bending, torsion, and winding properties, achieving comprehensive optimization of strength and toughness, processing performance and performance.

[0066] Example 2: The preparation method of Example 2 is the same as that of Example 1, except that the composition ratio of the alloy is different, specifically including: This embodiment provides a GH4090 alloy cold-drawn wire. The composition of this cold-drawn wire, by weight, is as follows: Cr: 19.0%, Co: 17.5%, Al: 1.60%, Ti: 2.65%, C: 0.040%, Mn: 0.004%, Si: 0.009%, S: 0.0009%, P: 0.0025%, B: 0.010%, Zr: 0.06%, Fe: 0.18%, Cu: 0.0009%, Ag: 0.0003%, Bi: 0.00006%, Pb: 0.0006%, with the balance being Ni and other unavoidable impurities.

[0067] Example 3: The preparation method of Example 3 is the same as that of Example 1, except that the composition ratio of the alloy is different, specifically including: This embodiment provides a GH4090 alloy cold-drawn wire. The composition of the cold-drawn wire, by weight ratio, is as follows: Cr: 20.0%, Co: 18.5%, Al: 1.65%, Ti: 2.70%, C: 0.045%, Mn: 0.002%, Si: 0.007%, S: 0.0007%, P: 0.0015%, B: 0.012%, Zr: 0.08%, Fe: 0.12%, Cu: 0.0007%, Ag: 0.0001%, Bi: 0.00004%, Pb: 0.0004%, with the balance being Ni and other unavoidable impurities.

[0068] The performance of the GH4090 alloy cold-drawn wires prepared in Examples 1-3 of the present invention was tested. The performance tests showed that the GH4090 alloy cold-drawn wires prepared according to the three proportions in Examples 1-3 have excellent high-temperature strength, good oxidation resistance, and good hot corrosion resistance. Specific performance data are as follows:

[0069] The sample prepared in Example 1 had a creep strength σb / 100h of 590 MPa at 650°C, 450 MPa at 700°C, and 320 MPa at 750°C; the room temperature tensile strength was 1150 MPa, and the elongation was 15%.

[0070] The sample prepared in Example 2 had a creep strength σb / 100h of 575 MPa at 650°C, 435 MPa at 700°C, and 310 MPa at 750°C; the room temperature tensile strength was 1130 MPa, and the elongation was 14%.

[0071] The sample prepared in Example 3 had a creep strength σb / 100h of 605 MPa at 650°C, 465 MPa at 700°C, and 330 MPa at 750°C; the room temperature tensile strength was 1170 MPa, and the elongation was 16%.

[0072] The oxidation weight gain of all three samples at 900℃ for 100 hours was less than 1.2 mg / cm², and the corrosion depth after the hot corrosion test was less than 0.05 mm.

[0073] In this alloy, Cr mainly plays a role in improving oxidation resistance and hot corrosion resistance; Co can stabilize the γ phase and improve the high-temperature strength of the alloy; Al and Ti form the γ' phase [Ni3(Al,Ti)] precipitate strengthening phase, which is the main source of the alloy's high-temperature strength; B and Zr can strengthen grain boundaries, refine grains, and improve the alloy's plasticity and toughness; C mainly exists in the form of carbides, which improves the alloy's high-temperature strength; other trace elements are controlled at low levels to reduce their adverse effects on the alloy's properties.

[0074] By precisely controlling the content ratio of each element, especially controlling Cr at 19.0-20.0%, Co at 17.5-18.5%, Al at 1.60-1.65%, and Ti at 2.65-2.70%, the alloy exhibits excellent comprehensive performance in high-temperature environments, meeting the requirements for high-temperature components such as turbine disks and turbine blades in aero-engines.

[0075] Further tests were conducted on the samples obtained in Examples 1-3 of the present invention, as follows: 500 mm long specimens from Examples 1-3 were subjected to room temperature tensile tests, and the tensile strength data were recorded; 150 mm long specimens were subjected to torsion, winding, and repeated bending tests, and the test results were recorded. The results are shown in Table 2 below.

[0076] Table 2 Mechanical properties and performance in use The test results in Table 2 show that the GH4090 alloy cold-drawn wires prepared in Examples 1-3 all have room temperature tensile strengths significantly higher than the standard requirement of 1540 MPa, reaching 1662 MPa, 1636 MPa, and 1637 MPa respectively. In the performance tests such as torsion, winding, and repeated bending, all samples did not show defects such as cracks, delamination, burrs, or breakage under the specified conditions. It can be seen that the process described in this invention can stably manufacture GH4090 alloy cold-drawn wires with mechanical properties and performance that meet and exceed the technical standard requirements. The products have good performance consistency, high reliability, and are suitable for engineering applications in high-strength and high-temperature service environments.

[0077] The above embodiments of the present invention further demonstrate that, by organically combining and synergistically integrating composition design and process flow, the present invention addresses key technical problems existing in GH4090 alloy cold-drawn wire, such as poor alloy composition uniformity, easy cracking during hot working, and difficulty in controlling cold-drawing deformation. It establishes a complete set of refined control schemes from smelting to finished product. In the raw material smelting stage, a dual process of vacuum induction and electroslag remelting, supplemented by precise vacuum control, electromagnetic stirring, and final high-vacuum casting, achieves precise control of the content of active elements (Al, Ti) and a significant improvement in the purity of the molten steel. In the post-casting homogenization and forging stages, long-term high-temperature holding and temperature gradient optimization completely eliminate macroscopic segregation and improve grain morphology, providing a uniform and dense microstructure for subsequent plastic processing. In the rolling stage, online cooling combined with precise temperature control at 980–1070℃ is employed. Precise control and synergistic elimination of the risk of central overheating and the tendency of microstructure coarsening ensure the internal density and dimensional consistency of the wire. During the multi-pass cold drawing process, the combination of solution-pickling cyclic treatment and a final pass deformation control of ≥35% achieves a dynamic balance between strength and plasticity, while preventing surface defects. Finally, during the low-temperature long-term aging process at 600±20℃ / 16h, the dispersion precipitation of the γ′ phase and the formation of grain boundary-stabilized carbides synergistically improve the material's yield strength, high-temperature creep strength, and service stability. The preparation method of this invention relies on the synergistic optimization of these multiple stages, not only resolving the technical pain points of existing GH4090 alloy cold-drawn wire production, such as large compositional fluctuations, high processing cracking rates, and poor performance consistency, but also achieving a comprehensive unity of high strength, high toughness, high-temperature corrosion resistance, and good processing adaptability in the finished product, fully meeting the stringent application requirements of high-temperature and complex service environments such as aero-engines and gas turbines.

[0078] In the description of this application, the references to terms such as "an embodiment," "some embodiments," "in this embodiment," "specific example," or "some examples," etc., refer to specific features, structures, materials, or characteristics described in connection with that embodiment or example, which are included in at least one embodiment or example of this application. In this specification, the illustrative expressions of the above terms do not necessarily refer to the same embodiment or example. Furthermore, the specific features, structures, materials, or characteristics described may be combined in a suitable manner in any one or more embodiments or examples. Moreover, without contradiction, those skilled in the art can combine and integrate the different embodiments or examples described in this specification, as well as the features of different embodiments or examples.

[0079] The above description is merely a specific embodiment of this application, but the scope of protection of this application is not limited thereto. Any variations or substitutions that can be easily conceived by those skilled in the art within the technical scope disclosed in this application should be included within the scope of protection of this application. Therefore, the scope of protection of this application should be determined by the scope of the claims.

Claims

1. A GH4090 alloy cold-drawn wire, characterized in that, By mass ratio, it includes the following components: Cr: 18.0%–21.0%, Co: 15.0%–21.0%, Al: 1.0%–2.0%, Ti: 2.0%–3.0%, C ≤0.13%, Mn ≤0.4%, Si ≤0.8%, S ≤0.015%, P ≤0.015%, B ≤0.02%, Zr ≤0.15%, Fe ≤1.50%, Cu ≤0.20%, Ag ≤0.0005%, Bi ≤0.0001%, Pb ≤0.001%, with the balance being Ni and other unavoidable impurities.

2. The GH4090 alloy cold-drawn wire according to claim 1, characterized in that, By mass ratio, it includes the following components: Cr: 19.0–20.0%, Co: 17.5–18.5%, Al: 1.60–1.65%, Ti: 2.65–2.70%, C: 0.040–0.045%, Mn ≤0.005%, Si ≤0.01%, S ≤0.001%, P ≤0.003%, B: 0.010–0.012%, Zr: 0.06–0.08%, Fe ≤0.20%, Cu ≤0.001%, Ag ≤0.0005%, Bi ≤0.0001%, Pb ≤0.001%, with the balance being Ni and other unavoidable impurities.

3. A method for manufacturing GH4090 alloy cold-drawn wire according to any one of claims 1-2, characterized in that, Includes the following steps: S1: Vacuum induction smelting electrode rod: The raw material is loaded into the vacuum induction furnace, the furnace temperature is controlled at 1520±10℃, the vacuum is drawn and the power is supplied to melt the steel; the temperature of the steel is reduced to 1480±10℃, and the refining period is entered. Al and Ti are added to further smelt the steel, and the refining is ended. The electrode rod is cast at 1500±10℃. S2: Electroslag remelting: After pretreatment of the electrode rod, further electroslag remelting is performed to obtain an electroslag ingot; S3: Homogenization treatment: The electroslag ingot is homogenized at 1180±10℃; S4: Forging billet: The electroslag ingot is cooled to 1150±10℃ and held at that temperature, then drawn into a square billet and air-cooled after forging. S5: Rolled wire: The billet is heated to 1150±10℃ and held for 2 hours, and then rolled into wire by continuous rolling. S6: Multi-pass cold drawing: The wire is cold-drawn in multiple passes to obtain cold-drawn filament, and the deformation amount of each pass is controlled at 30-40%. Solution treatment and pickling are performed before each pass, and the deformation amount of the last pass is controlled at ≥35%. S7: Aging treatment: The cold-drawn wire is subjected to aging treatment to obtain GH4090 alloy cold-drawn wire.

4. The method for manufacturing GH4090 alloy cold-drawn wire according to claim 3, characterized in that, In step S1, the conditions for vacuuming and powering the melting process are: controlling the vacuum degree in the furnace to be ≤5Pa, the vacuum degree during the refining period to be ≤1.0Pa, and the early stage of the refining period also includes electromagnetic stirring of the molten steel. The conditions for casting are: maintaining the vacuum degree to be ≤1.0Pa during the casting process.

5. The method for manufacturing GH4090 alloy cold-drawn wire according to claim 3, characterized in that, In step S2, the pretreatment includes: polishing the surface of the electrode rod to remove the surface oxide layer, cutting off 50mm from the casting end of the electrode rod, and then welding a transition electrode.

6. The method for manufacturing GH4090 alloy cold-drawn wire according to claim 3, characterized in that, In step S3, the homogenization treatment conditions are as follows: the electroslag ingot is heated to 1180±10℃ after 6 hours and kept at that temperature for 30 hours.

7. The method for manufacturing GH4090 alloy cold-drawn wire according to claim 3, characterized in that, In step S5, the rolling temperature during the continuous rolling process is 980–1070℃.

8. The method for manufacturing GH4090 alloy cold-drawn wire according to claim 3, characterized in that, In step S6, the number of passes is 8, and the weight of the cold-drawn wire is 20-25 kg.

9. The method for manufacturing GH4090 alloy cold-drawn wire according to claim 3, characterized in that, In step S6, the conditions for solution treatment and pickling include: placing the wire into a heat treatment furnace, heating it to 1050±10℃ and holding it at that temperature for 0.5-1.0 hours, removing it from the furnace and water cooling it, followed by pickling to remove the surface oxide scale, and then washing it with water and drying it.

10. The method for manufacturing GH4090 alloy cold-drawn wire according to claim 3, characterized in that, In step S7, the aging treatment conditions are as follows: the cold-drawn wire is kept at a temperature of 600±20℃ for 16 hours, followed by air cooling.

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