A large-weight, wide-width high-temperature alloy coil and its manufacturing method

Abstract

This invention relates to a large-weight, wide-width high-temperature alloy coil and its manufacturing method, belonging to the field of high-temperature alloy materials. It solves at least one of the following problems existing in the production of wide-width high-temperature alloy sheets: difficulty in controlling dimensional accuracy, poor surface quality, large quality fluctuations, high production difficulty, and high cost. A method for preparing a large-weight, wide-width high-temperature alloy coil includes: slab pretreatment; hot rolling of the coil; solution treatment and surface treatment of the coil; cold rolling and intermediate annealing of the semi-finished coil; and cold rolling and processing of the finished coil. This invention achieves the production of high-quality, high-performance, and high-dimensional-accuracy high-temperature alloy sheets with wider widths and thinner thicknesses.

Description

Technical Field

[0001] This invention relates to the field of high-temperature alloy materials technology, and in particular to a large-weight, wide-width high-temperature alloy coil and its manufacturing method. Background Technology

[0002] High-temperature alloys, due to their high strength, oxidation and corrosion resistance, fatigue resistance, and structural stability exhibited at high temperatures, play an indispensable role in demanding fields such as aerospace and nuclear power. However, behind these excellent properties lie characteristics such as severe work hardening, high deformation resistance, and low thermal conductivity. These characteristics pose significant challenges to the processing of high-temperature alloys, making them far more difficult to manufacture than other metals (such as ordinary steel, stainless steel, aluminum-magnesium alloys, and titanium alloys).

[0003] Previously, high-temperature alloys were typically manufactured using tensionless single-sheet rolling technology. This method is relatively simple in terms of equipment requirements and process control, and can accommodate the high deformation resistance of high-temperature alloys. However, it has many drawbacks, such as insufficient dimensional accuracy, poor surface quality, poor quality stability, low production efficiency, and large scrap metal loss. These shortcomings make tensionless single-sheet rolling difficult to meet the stringent requirements of aerospace and other fields for high-performance, high-precision, and wide-width high-temperature alloy sheets.

[0004] With the increasing demands for the size and performance of high-temperature alloy sheets in key fields such as aerospace and nuclear power, the limitations of single-sheet rolling are becoming more and more apparent. There is an urgent need to develop new production processes to improve production efficiency and product quality, and to meet the requirements of certain application fields for high-performance, high-precision, and wide-width high-temperature alloy sheets. Summary of the Invention

[0005] Based on the above analysis, the present invention aims to provide a large-weight, wide-width high-temperature alloy coil and its manufacturing method, in order to solve at least one of the following problems in the existing production of wide-width high-temperature alloy sheets: difficulty in controlling dimensional accuracy, poor surface quality, large quality fluctuations, high production difficulty, and high cost.

[0006] The objective of this invention is achieved through the following technical solution:

[0007] This invention provides a method for preparing large-weight, wide-width high-temperature alloy coils, comprising the following steps:

[0008] S1. Slab pretreatment:

[0009] The forged slab is subjected to homogenization heat treatment. The forged slab is then loaded into a heating furnace, ensuring that the furnace temperature is ≤700℃. The furnace temperature is increased at a rate of 30-50℃ / h until the homogenization heat treatment temperature T is reached. 均匀化 =0.88T 初熔 ~0.92T终熔 Heat preservation is carried out, and the heat preservation time t1≥7δ1, where t1 is in min and δ1 is the thickness of the forging slab in mm;

[0010] S2, Hot-rolled coil:

[0011] The pretreated slab is hot-rolled into a thin slab in the first hot rolling process; the thin slab is then hot-rolled into a coil in the second hot rolling process.

[0012] S3. Solution treatment and surface treatment of rolled blanks:

[0013] The hot-rolled coil is first subjected to solution treatment, and then surface treatment to obtain intermediate coil products.

[0014] S4. Cold rolling and intermediate annealing of semi-finished coils:

[0015] The intermediate coil is subjected to a single-pass cold rolling process, wherein the cumulative reduction rate of the single-pass cold rolling process reaches 25% to 50%; the coil after the single-pass cold rolling process is subjected to intermediate annealing; the single-pass cold rolling process and intermediate annealing process are repeated until the coil reaches the target thickness; the coil that has reached the target thickness is subjected to surface treatment to obtain a semi-finished coil.

[0016] S5. Cold rolling and processing of finished coils:

[0017] The semi-finished coil is cold-rolled to obtain the finished coil; the finished coil is then subjected to solution treatment and surface treatment in sequence to obtain the large-weight, wide-width high-temperature alloy coil.

[0018] Furthermore, in the first hot rolling step S2, the pretreated slab is loaded into the heating furnace, ensuring the furnace loading temperature is ≤700℃, and the temperature is increased with the furnace at a rate of 50-60℃ / h until the first hot rolling heating temperature = (0.9-0.95)T is reached. 初熔 Insulate for heat preservation, heat preservation time t 21 ≥7δ1,t 21 The unit is min, and δ1 is the thickness of the forged slab in mm; after the heat preservation is completed, the first hot rolling is carried out, and the cumulative reduction rate of the first hot rolling is 80-95%.

[0019] Furthermore, in the second hot rolling process of step S2, the thin slab is loaded into a heating furnace for online heating compensation, wherein the online heating compensation temperature is (0.9~0.95)T. 初熔 Insulation time t 22 ≥5δ 21 , t 22 The unit is min, δ 21The thickness of the slab obtained from the first hot rolling is in mm; after the online reheating is completed, a second hot rolling is carried out, and the cumulative reduction rate of the second hot rolling is 65-80%.

[0020] Furthermore, in the first hot rolling step S2, the final rolling temperature is (0.65~0.70)T. 初熔 ; and / or,

[0021] In the second hot rolling process of step S2, the final rolling temperature is (0.65~0.70)T. 初熔 .

[0022] Furthermore, in the solution treatment of the rolled blank in step S3, the solution treatment temperature is (0.80~0.95)T. 初熔 Insulation time t3≥5δ 22 t3 is in min, δ 22 The thickness of the coil obtained from the second hot rolling is in mm.

[0023] Furthermore, in the intermediate annealing process of step S4, the intermediate annealing temperature is (0.80~0.95)T. 初熔 The heat preservation time t4 ≥ 4δ4, where t4 is in min and δ4 is the thickness of the coil after one cold rolling process before the intermediate annealing treatment, in mm.

[0024] Furthermore, in step S5, during the cold rolling of the coil semi-finished product, the total cold rolling reduction rate is 30-60%, the reduction rate decreases with each pass, and the reduction rate of each pass is controlled between 5-15%.

[0025] Furthermore, in the solution treatment of step S5, the solution treatment temperature is (0.8~0.95)T. 初熔 The heat preservation time t5≥4δ5, where t5 is in min and δ5 is the thickness of the finished coil in mm.

[0026] Furthermore, the width of the large-weight, wide-width high-temperature alloy coil is 1000-1100mm, the thickness is 0.5-2.0mm, the single coil weight is ≥3t, the thickness accuracy of the coil is within ±3%δ of the thickness, and the surface roughness Ra value of the coil is ≤0.1μm, where δ is the thickness of the large-weight, wide-width high-temperature alloy coil.

[0027] This invention provides a large-weight, wide-width high-temperature alloy coil obtained according to the preparation method described above.

[0028] Compared with the prior art, the present invention can achieve at least one of the following beneficial effects:

[0029] (1) By optimizing the process flow and key process parameters, this invention overcomes the technical difficulties such as severe work hardening, large deformation resistance and low thermal conductivity of high-temperature alloys, and realizes the production of high-quality, high-dimensional precision high-temperature alloy plates with wider width and thinner thickness.

[0030] Specifically, unlike the conventional process of directly hot-rolling forged slabs, this invention adds a crucial slab pretreatment step before hot rolling. Through homogenization heat treatment, the slab is heated to a specific temperature range at a controlled heating rate and held at that temperature for a sufficient time, effectively eliminating residual stress generated during forging and resulting in a more uniform internal structure. This pretreatment step provides a good microstructure foundation for subsequent rolling processes, helping to improve the dimensional accuracy and performance stability of the final product and enhancing the overall quality of the high-temperature alloy sheet.

[0031] By using step-by-step hot rolling, the pre-treated slab is first rolled into a thin slab, and then rolled into a coil. This gradual thinning method can effectively control the amount of deformation, reduce defects such as cracks, and ensure the quality of the coil while taking into account rolling efficiency.

[0032] After hot rolling, solution treatment is performed to fully dissolve the alloying elements, resulting in a uniform solid solution structure that improves the material's high-temperature strength and oxidation resistance. Subsequent surface treatment removes impurities such as oxide scale, improving surface quality and creating favorable conditions for subsequent cold rolling.

[0033] Cold rolling further reduces the thickness of the sheet metal, and intermediate annealing eliminates work hardening, restores plasticity, avoids cracks, ensures the operability of subsequent processing, and improves dimensional accuracy and surface quality.

[0034] The final cold-rolled sheet thickness meets the requirements for thin sheet dimensions; solution treatment and surface treatment ensure the performance and surface quality of the final product, achieving high performance, high quality, and high dimensional accuracy standards.

[0035] Compared with traditional single-sheet slab rolling, this invention directly rolls the slab into coils after each rolling process, which significantly improves the dimensional accuracy, surface quality and shape control of the final product, reduces the generation of defects such as cracks, and improves production efficiency and material utilization.

[0036] (2) In some preferred embodiments, the process parameters in each process step (hot rolling of coil, solution treatment of coil, cold rolling and intermediate annealing of coil semi-finished product, cold rolling of coil finished product, etc.) are controlled to more effectively address the problems caused by the characteristics of high temperature alloys such as severe work hardening, large deformation resistance and low thermal conductivity. While ensuring wide width and thin specifications, uniform microstructure and stress concentration are obtained, thereby providing a strong guarantee for subsequent processes and the final product to obtain high dimensional accuracy, better plate shape and surface quality.

[0037] (3) In some specific embodiments, the preparation method of the present invention achieves a wider width (1000-1100 mm) while significantly reducing the thickness of the high-temperature alloy sheet to 0.5-2.0 mm. Under such conditions of wider width and thinner dimensions, the thickness accuracy achieved by the embodiments of the present invention can be controlled within ±3%δ, and the surface flatness and roughness can be controlled with Ra values ​​≤0.1 μm. These indicators are not only significantly better than those of the prior art, but also better meet the stringent requirements of high-performance, lightweight, and integrated high-temperature alloy sheets in aerospace, nuclear power, and other application fields.

[0038] In this invention, the above-described technical solutions can be combined with each other to achieve more preferred combinations. Other features and advantages of this invention will be set forth in the following description, and some advantages may become apparent from the description or be learned by practicing the invention. The objects and other advantages of this invention can be realized and obtained from what is particularly pointed out in the description and drawings. Attached Figure Description

[0039] The accompanying drawings are for illustrative purposes only and are not intended to limit the invention. Throughout the drawings, the same reference numerals denote the same parts.

[0040] Figure 1 A photograph of the large-weight, wide-width high-temperature alloy coil provided in Embodiment 2 of the present invention;

[0041] Figure 2 This is a grain structure diagram of the large-weight, wide-width high-temperature alloy coil provided in Embodiment 2 of the present invention. Detailed Implementation

[0042] Preferred embodiments of the present invention will now be described in detail with reference to the accompanying drawings, which form part of this application and are used together with the embodiments of the present invention to illustrate the principles of the present invention, but are not intended to limit the scope of the present invention.

[0043] The production of high-temperature alloys (such as common nickel-based high-temperature alloys) faces numerous challenges in wide-width sheet production, especially for sheets thinner than 5 mm. These challenges are mainly reflected in the following aspects: high-temperature alloys are highly sensitive to temperature, and improper temperature control can easily lead to uneven microstructure of the sheet, thus affecting the quality of the sheet; during hot working, high-temperature alloys (such as nickel-based and cobalt-based alloys) are prone to cracking, especially under conditions of high strength and poor plasticity at high temperatures; due to the narrow processing window and high cracking tendency, sheet shape control is difficult in wide-width production; high content of elements such as Nb and Ti in the alloy is detrimental to the uniform growth of recrystallized grains, easily causing microstructure inhomogeneity in the thickness direction; when producing thinner sheets, dimensional accuracy control becomes more difficult, and thickness inhomogeneity is likely to occur.

[0044] This invention addresses the technical challenges faced by existing technologies in producing wide-width, thin-plate (thickness < 5 mm) high-temperature alloy sheets, including severe work hardening, high deformation resistance, and low thermal conductivity. It proposes a production method based on sheet roll rolling. This method overcomes the limitation of traditional sheet roll rolling, which is only applicable to materials with relatively low processing difficulty, such as ordinary steel, stainless steel, titanium alloys, and aluminum-magnesium alloys. By optimizing the overall process flow and key process parameters of each step, and adapting to the narrow processing window of high-temperature alloys, this method aims to achieve the production of high-quality, high-dimensional-precision high-temperature alloy sheets with wider widths and thinner thicknesses. This fills a gap in existing technologies and provides solid technical support for the integrated, lightweight, and structurally integrated needs of key fields such as aerospace and nuclear power.

[0045] In a first aspect, the present invention provides a method for preparing large-weight, wide-width high-temperature alloy coils, comprising the following steps:

[0046] S1. Slab pretreatment:

[0047] The forged slab is subjected to homogenization heat treatment. The forged slab is then loaded into a heating furnace, ensuring that the furnace temperature is ≤700℃. The furnace temperature is increased at a rate of 30-50℃ / h until the homogenization heat treatment temperature T is reached. 均匀化 =0.88T 初熔 ~0.92T 终熔 Heat preservation is carried out, and the heat preservation time t1≥7δ1, where t1 is in min and δ1 is the thickness of the forging slab in mm;

[0048] S2, Hot-rolled coil:

[0049] The pretreated slab is hot-rolled into a thin slab in the first hot rolling process; the thin slab is then hot-rolled into a coil in the second hot rolling process.

[0050] S3. Solution treatment and surface treatment of rolled blanks:

[0051] The hot-rolled coil is first subjected to solution treatment, and then surface treatment to obtain intermediate coil products.

[0052] S4. Cold rolling and intermediate annealing of semi-finished coils:

[0053] The intermediate coil is subjected to a single-pass cold rolling process, wherein the cumulative reduction rate of the single-pass cold rolling process reaches 25% to 50%; the coil after the single-pass cold rolling process is subjected to intermediate annealing; the single-pass cold rolling process and intermediate annealing process are repeated until the coil reaches the target thickness; the coil that has reached the target thickness is subjected to surface treatment to obtain a semi-finished coil.

[0054] S5. Cold rolling and processing of finished coils:

[0055] The semi-finished coil is cold-rolled to obtain the finished coil; the finished coil is then subjected to solution treatment and surface treatment in sequence to obtain the large-weight, wide-width high-temperature alloy coil.

[0056] It is understood that the T described in this invention 初熔 The definition of T is the temperature at which an alloy begins to melt, corresponding to the solidus temperature. 终熔 The Tc is defined as the temperature at which an alloy completely melts, corresponding to the liquidus temperature. For example, the Tc of an alloy is determined by differential scanning calorimetry. 初熔 and T 终熔 .

[0057] Compared with existing technologies, this invention overcomes technical challenges such as severe work hardening, high deformation resistance, and low thermal conductivity of high-temperature alloys by optimizing the process flow and key process parameters, and realizes the production of high-quality, high-dimensional precision high-temperature alloy plates with wider widths and thinner thicknesses.

[0058] Specifically, unlike the conventional process of directly hot-rolling forged slabs, this invention adds a crucial slab pretreatment step before hot rolling. Through homogenization heat treatment, the slab is heated to a specific temperature range at a controlled heating rate and held at that temperature for a sufficient time, effectively eliminating residual stress generated during forging and resulting in a more uniform internal structure. This pretreatment step provides a good microstructure foundation for subsequent rolling processes, helping to improve the dimensional accuracy and performance stability of the final product and enhancing the overall quality of the high-temperature alloy sheet.

[0059] Furthermore, through step-by-step hot rolling, the pretreated slab is first rolled into a thin slab, and then rolled into a coil. This gradual thinning method can effectively control the amount of deformation and reduce defects such as cracks, ensuring the quality of the coil while taking into account rolling efficiency.

[0060] Furthermore, solution treatment following hot rolling allows the alloying elements to fully dissolve, resulting in a uniform solid solution structure that improves the material's high-temperature strength and oxidation resistance. Subsequent surface treatment removes impurities such as oxide scale, improving surface quality and creating favorable conditions for subsequent cold rolling.

[0061] Furthermore, cold rolling further reduces the thickness of the sheet metal, and intermediate annealing eliminates work hardening, restores plasticity, avoids cracks, ensures the operability of subsequent processing, and improves dimensional accuracy and surface quality.

[0062] Furthermore, the final cold-rolled sheet thickness is reduced to meet the dimensional requirements of thin sheets; solution treatment and surface treatment ensure the performance and surface quality of the final product, achieving high performance, high quality, and high dimensional accuracy standards.

[0063] Compared with traditional single-sheet slab rolling, this invention directly rolls the slab into coils after each rolling process, which significantly improves the dimensional accuracy, surface quality and shape control of the final product, reduces the generation of defects such as cracks, and improves production efficiency and material utilization.

[0064] While traditional processes have achieved certain results in the production of high-temperature alloy sheets, numerous challenges remain when producing wide and thin high-temperature alloy sheets. To overcome these difficulties, this invention, based on increasing slab pretreatment and optimizing the overall process flow, further controls the process parameters in each process step (hot rolling of coils, solution treatment of coils, cold rolling and intermediate annealing of semi-finished coils, cold rolling of finished coils, etc.). This more effectively addresses the problems caused by the severe work hardening, high deformation resistance, and low thermal conductivity of high-temperature alloys, further improving production efficiency, dimensional accuracy, surface quality, and product performance, while reducing production costs.

[0065] It should be noted that in the production of high-temperature alloys, heat treatment process parameters, especially temperature, are crucial to product quality. Traditionally, the temperature range and holding time for heat treatment have relied mainly on experience, standards, and experimental data. While these methods offer some guidance, they suffer from insufficient precision and difficulty in adapting to differences in alloy properties, resulting in poor dimensional accuracy, microstructure uniformity, and surface quality. This invention addresses this issue by precisely measuring the T of the alloy. 初熔 and T 终熔 By combining the actual thickness before each heat treatment and using quantitative relationships to set an appropriate process window range, the characteristics of high-temperature alloys, such as temperature sensitivity and narrow process windows, are adapted. This not only ensures uniform microstructure and reduces stress concentration under wide-width and thin-gauge conditions, but also provides strong support for the dimensional accuracy, shape control, and surface quality of subsequent processes and the final product.

[0066] For example, in the homogenization heat treatment of step S1, the furnace loading temperature is 400℃, 500℃, 550℃, 600℃, 620℃, 640℃, 660℃, 680℃, or 700℃; the furnace heating rate is 30℃ / h, 35℃ / h, 40℃ / h, 42℃ / h, 44℃ / h, 46℃ / h, 48℃ / h, or 50℃ / h; T 均匀化 =K1×T 初熔 ~K2×T 终熔 Where K1 takes values ​​of 0.88, 0.89, and 0.90; K2 takes values ​​of 0.90, 0.91, and 0.92; and the heat preservation time t1 is 7δ1, 7.2δ1, 7.4δ1, 7.6δ1, 7.8δ1, 8δ1, 9δ1, and 10δ1.

[0067] Preferably, in the homogenization heat treatment of step S1, the furnace loading temperature is 600–700°C; the furnace temperature is increased at a rate of 40–50°C / h; and the homogenization heat treatment temperature T 均匀化 =0.90T 初熔 ~0.90T 终熔 The heat preservation time t1 is 7δ1~8δ1.

[0068] Furthermore, after homogenization heat treatment, the surface of the slab is ground to achieve a state free of defects such as cracks, corner cracks, and scabs. For example, after grinding in step S1, the surface roughness Ra value of the slab is 0.8 to 1.6 μm.

[0069] It should be noted that by optimizing the process parameters of slab pretreatment (the homogenization heat treatment) and treating the slab surface, this invention can obtain hot-rolled coil blanks with high homogeneity and high surface quality, laying a good foundation for the smooth hot rolling of coil blanks and the surface quality control of finished coil products.

[0070] In some embodiments, during the first hot rolling in step S2, the pretreated slab is loaded into the heating furnace, ensuring the furnace loading temperature is ≤700℃, and the temperature is increased with the furnace at a rate of 50-60℃ / h until the first hot rolling heating temperature = (0.9-0.95)T is reached. 初熔 Insulate for heat preservation, heat preservation time t 21 ≥7δ1,t 21 The unit is min, and δ1 is the thickness of the forged slab in mm; after the heat preservation is completed, the first hot rolling is carried out, and the cumulative reduction rate of the first hot rolling is 80-95%.

[0071] For example, in the first hot rolling of step S2, the furnace charging temperature is 400℃, 500℃, 550℃, 600℃, 620℃, 640℃, 660℃, 680℃, or 700℃; the furnace heating rate is 50℃ / h, 51℃ / h, 52℃ / h, 53℃ / h, 54℃ / h, 55℃ / h, 56℃ / h, 58℃ / h, or 60℃ / h; T 均匀化 = (K3~K4)×T 初熔 Where K3 and K4 independently take values ​​such as 0.90, 0.91, 0.92, 0.93, 0.94, and 0.95, and K3 ≤ K4; the heat preservation time t 21 They are 7δ1, 7.2δ1, 7.4δ1, 7.6δ1, 7.8δ1, 8δ1, 9δ1, and 10δ1.

[0072] Preferably, in the first hot rolling, the furnace charging temperature is 600–700°C; the furnace temperature is increased at a rate of 50–55°C / h; the heating temperature of the first hot rolling is (0.91–0.93)T. 初熔 Insulation time t21 It is 7δ1~8δ1.

[0073] Preferably, in the first hot rolling, the final rolling temperature is (0.65~0.70)T. 初熔 For example, in the first hot rolling, the final rolling temperature is 0.65T. 初熔 0.66T 初熔 0.67T 初熔 0.68T 初熔 0.69T 初熔 0.70T 初熔 .

[0074] Preferably, in the first hot rolling, the rolling speed is 1–10 m / s; the rolling pressure is 2000–3000 kN. For example, in the first hot rolling, the rolling speed is 1 m / s, 2 m / s, 4 m / s, 6 m / s, 8 m / s, or 10 m / s; the rolling pressure is 2000 kN, 2200 kN, 2400 kN, 2600 kN, 2800 kN, or 3000 kN.

[0075] Preferably, in the first hot rolling, the number of rolling passes is 13 to 18, and the reduction rate varies as follows: for the first to fifth passes, the reduction rate is controlled at 15 to 20%; for the sixth to tenth passes, the reduction rate is controlled at 10 to 15%; and for the eleventh to the last pass, the reduction rate is controlled at 5 to 10%.

[0076] Preferably, after the first hot rolling is completed, water cooling is used to cool the product, and the water cooling time after rolling is controlled to be ≤5s.

[0077] In some embodiments, during the second hot rolling in step S2, the thin slab is loaded into a heating furnace for online heating, wherein the online heating temperature is (0.9~0.95)T. 初熔 Insulation time t 22 ≥5δ 21 , t 22 The unit is min, δ 21 The thickness of the slab obtained from the first hot rolling is in mm; after online reheating, a second hot rolling is performed, with a cumulative reduction rate of 65-80%. Preferably, the thickness of the coil obtained from the second hot rolling is 4-6 mm, for example, 4.0 mm, 4.5 mm, 5.0 mm, 5.5 mm, or 6.0 mm.

[0078] For example, in the second hot rolling in step S2, the online reheating temperature is 0.9T. 初熔 0.91T 初熔 0.92T 初熔 0.93T 初熔0.94T 初熔 0.95T 初熔 Insulation time t 22 5.0δ 21 ~10.0δ 21 Insulation time t 22 5.0δ 21 5.1δ 21 5.2δ 21 5.3δ 21 5.4δ 21 5.5δ 21 5.7δ 21 6.0δ 21 6.5δ 21 7.0δ 21 7.5δ 21 8.0δ 21 9.0δ 21 10.0δ 21 .

[0079] Preferably, in the second hot rolling, the online reheating temperature is (0.93~0.94)T. 初熔 During online warming, the holding time is t. 22 5.0δ 21 ~5.5δ 21 .

[0080] Preferably, in the second hot rolling, the final rolling temperature is (0.65~0.70)T. 初熔 For example, in the first hot rolling, the final rolling temperature is 0.65T. 初熔 0.66T 初熔 0.67T 初熔 0.68T 初熔 0.69T 初熔 0.70T 初熔 .

[0081] Preferably, in the second hot rolling, the rolling speed is 1–10 m / s; the rolling pressure is 3000–5000 kN. For example, in the second hot rolling, the rolling speed is 1 m / s, 2 m / s, 4 m / s, 6 m / s, 8 m / s, or 10 m / s; the rolling pressure is 3000 kN, 3400 kN, 3800 kN, 4200 kN, 4600 kN, or 5000 kN.

[0082] Preferably, in the second hot rolling, the number of rolling passes is 10 to 12, and the reduction rate varies as follows: for the first to fifth passes, the reduction rate is controlled at 15 to 20%; for the sixth to the last pass, the reduction rate is controlled at 5 to 15%.

[0083] It should be noted that by optimizing the hot rolling process parameters of the coil as described above, it is possible to better achieve the smooth forming of hot-rolled coils and improve the yield, thus providing a good foundation for the high quality and high dimensional accuracy of subsequent processes and the final product.

[0084] In some embodiments, in the solution treatment of the rolled blank in step S3, the solution treatment temperature is (0.80~0.95)T. 初熔 Insulation time t3≥5δ 22 t3 is in min, δ 22 The thickness of the coil obtained from the second hot rolling is in mm.

[0085] For example, in the solution treatment of the rolled blank in step S3, the solution treatment temperature is 0.80T. 初熔 0.82T 初熔 0.84T 初熔 0.85T 初熔 0.86T 初熔 0.87T 初熔 0.88T 初熔 0.89T 初熔 0.90T 初熔 0.92T 初熔 0.94T 初熔 0.95T 初熔 The heat preservation time t3 is 5.0δ. 22 ~10.0δ 22 The heat preservation time t3 is 5.0δ. 22 5.1δ 22 5.2δ 22 5.3δ 22 5.4δ 22 5.5δ 22 5.7δ 22 6.0δ 22 6.5δ 22 7.0δ 22 7.5δ 22 8.0δ 22 9.0δ 22 10.0δ 22 .

[0086] Preferably, in the solution treatment of step S3, the furnace is preheated. Preferably, the solution treatment temperature is (0.85~0.9)T. 初熔 Insulation time t3=(5~5.5)δ 22 After the solution treatment and heat preservation are completed, rapid water cooling is performed, and the water cooling time after solution treatment is controlled to be ≤5s.

[0087] It should be noted that by optimizing the solution treatment process parameters of the hot-rolled coil, the hot-rolled coil can be softened, providing good plastic deformation conditions for cold rolling, thus providing a good foundation for the high quality and high dimensional accuracy of subsequent processes and the final product.

[0088] After the solution treatment in step S3 is completed, the surface treatment includes using an acid pickling line to remove the oxide scale from the surface of the roll blank, thereby improving the surface quality and providing a good foundation for subsequent processing and treatment.

[0089] In some embodiments, during the single-pass cold rolling process in step S4, the reduction rate decreases with each pass, and the reduction rate of each pass is controlled between 5% and 15%.

[0090] For example, the cumulative reduction rate of the single-pass cold rolling process is 25%, 30%, 35%, 40%, 45%, and 50%.

[0091] Preferably, in the single-pass cold rolling process of step S4, the number of passes is 5 to 8.

[0092] Preferably, in the cold rolling of the coil semi-finished product in step S4, the rolling speed is 1-5 m / s; the rolling pressure is 600-800 tons of force; 1 ton of force equals 1000 kilograms of force (kgf), that is, the gravitational force exerted on 1 ton of mass on the Earth's surface. For example, in the cold rolling of the coil semi-finished product in step S4, the rolling speed is 1 m / s, 2 m / s, 3 m / s, 4 m / s, or 5 m / s, and the rolling pressure is 650 tons of force, 700 tons of force, 750 tons of force, or 800 tons of force.

[0093] In some embodiments, in the intermediate annealing process of step S4, the intermediate annealing temperature is (0.80~0.95)T. 初熔 The heat preservation time t4 ≥ 4δ4, where t4 is in min and δ4 is the thickness of the coil after one cold rolling process before the intermediate annealing treatment, in mm.

[0094] For example, in the intermediate annealing process of step S4, the intermediate annealing temperature is 0.80T. 初熔 0.82T 初熔 0.84T 初熔 0.85T 初熔 0.86T 初熔 0.87T 初熔 0.88T 初熔 0.89T 初熔 0.90T 初熔 0.92T 初熔 0.94T 初熔 0.95T 初熔. The heat preservation time t4 is 4δ4~10δ4; the heat preservation time t3 is 4.0δ4, 4.1δ4, 4.2δ4, 4.3δ4, 4.4δ4, 4.5δ4, 4.7δ4, 5.0δ4, 6δ4, 7.0δ4, 7.5δ4, 8.0δ4, 9.0δ4, 10.0δ4.

[0095] Preferably, in the intermediate annealing process of step S4, the furnace is warmed. Preferably, the intermediate annealing temperature is (0.85~0.9)T. 初熔 The holding time is t4 = (4~4.5)δ4. After intermediate annealing, the mixture is air-cooled.

[0096] Furthermore, after the intermediate annealing process in step S4 is completed, the surface treatment includes removing the oxide scale from the surface of the coil semi-finished product using an online grinding line, ensuring that the surface roughness Ra value of the coil semi-finished product blank after grinding is 0.3 to 0.5 μm.

[0097] It should be noted that by controlling the cold rolling process parameters of the semi-finished coil and optimizing the intermediate annealing process parameters, the thickness and its variation of the plate can be effectively reduced, the uniformity of the structure can be improved, the dimensional accuracy of the final product can be improved, residual stress can be significantly reduced, the generation of microcracks can be reduced, and the surface quality can be improved.

[0098] In some embodiments, during the cold rolling of the coil semi-finished product in step S5, the total cold rolling reduction rate is 30-60%, the reduction rate decreases with each pass, and the reduction rate of each pass is controlled between 5-15%.

[0099] For example, in step S5, the total cold rolling reduction rate during the cold rolling of the coil semi-finished product is 30%, 35%, 40%, 45%, 50%, 55%, or 60%.

[0100] Preferably, in step S5, the total number of cold rolling passes for the semi-finished coil is 4 to 6. Preferably, the total cold rolling reduction rate is 35% to 45%.

[0101] Preferably, in step S5, the rolling speed of the semi-finished coil is 1-5 m / s and the rolling pressure is 800-1000 tons of force.

[0102] For example, in step S5, the rolling speed of the coil semi-finished product is 1m / s, 2m / s, 3m / s, 4m / s, and 5m / s, and the rolling pressure is 800 tons, 850 tons, 900 tons, 950 tons, and 1000 tons, respectively.

[0103] In some embodiments, the solution treatment temperature in step S5 is (0.8~0.95)T. 初熔The heat preservation time t5≥4δ5, where t5 is in min and δ5 is the thickness of the finished coil in mm.

[0104] For example, in the solution treatment of step S5, the solution treatment temperature is 0.80T. 初熔 0.82T 初熔 0.84T 初熔 0.85T 初熔 0.86T 初熔 0.87T 初熔 0.88T 初熔 0.89T 初熔 0.90T 初熔 0.92T 初熔 0.94T 初熔 0.95T 初熔 . The heat preservation time t5 is 4δ4~10δ4; the heat preservation time t3 is 4.0δ4, 4.1δ4, 4.2δ4, 4.3δ4, 4.4δ4, 4.5δ4, 4.7δ4, 5.0δ4, 6δ4, 7.0δ4, 7.5δ4, 8.0δ4, 9.0δ4, 10.0δ4.

[0105] Preferably, in the solution treatment of step S5, the furnace is preheated. Preferably, the solution treatment temperature is (0.85~0.95)T. 初熔 The heat preservation time is t5 = (4~5)δ5. After the heat preservation is completed, air cooling is performed.

[0106] After the solution treatment in step S5 is completed, the surface treatment includes removing the oxide scale from the surface of the finished coil using an online grinding line, ensuring that the surface roughness Ra value of the finished coil blank after grinding is ≤0.1μm.

[0107] It should be noted that by controlling the cold rolling process parameters of the finished coil and optimizing the solution treatment process parameters, it is possible to effectively ensure that the final product's microstructure uniformity, dimensional accuracy, plate shape, and surface quality meet high standards, thereby better meeting the stringent requirements of aerospace, nuclear power, and other fields.

[0108] In some embodiments, during the slab pretreatment, the forged slab has a thickness of 180–200 mm, a width of 1020–1060 mm, and a length of 1700–2000 mm.

[0109] It is worth noting that the width of the large-weight, wide-width high-temperature alloy coil obtained by the preparation method of the present invention is 1000-1100 mm, the thickness is 0.5-2.0 mm, the single coil weight is ≥3t, the thickness accuracy of the coil is within ±3%δ of the thickness, and the surface roughness Ra value of the coil is ≤0.1μm, where δ is the thickness of the large-weight, wide-width high-temperature alloy coil.

[0110] Secondly, the present invention provides a large-weight, wide-width high-temperature alloy coil obtained according to the preparation method described in the first aspect. The large-weight, wide-width high-temperature alloy coil has a width of 1000–1100 mm, a thickness of 0.5–2.0 mm, a single coil weight ≥ 3 t, a thickness accuracy within ±3%δ of the thickness, and a surface roughness Ra value ≤ 0.1 μm, where δ is the thickness of the large-weight, wide-width high-temperature alloy coil.

[0111] It should be noted that the large-weight, wide-width high-temperature alloy coils described in this invention have good microstructure uniformity, and their mechanical properties can all reach the following levels: at room temperature, tensile strength R... m ≥825MPa, specified plastic elongation strength R p0.2 ≥420MPa; elongation after fracture 60%~70%.

[0112] In some embodiments, the large-weight, wide-width high-temperature alloy coils described in this invention are nickel-based high-temperature alloys, such as GH3625 alloy. The composition of the large-weight, wide-width high-temperature alloy coils, in mass percentage, is as follows: C: ≤0.10%, Cr: 20-23%, Co: ≤1%, Mo: 8-10%, Fe: ≤5%, Al: ≤0.40%, Ti: ≤0.40%, Nb: 3.15-4.15%, Si: ≤0.50%, Mn: ≤0.50%, S: ≤0.015%, P: ≤0.015%, Cu: ≤0.07%, with Ni as the balance.

[0113] For example, in the composition of GH3625 alloy, C is 0.002% to 0.10%, such as 0.002%, 0.01%, 0.02%, 0.04%, 0.06%, 0.08%, and 0.10%. Cr is 20%, 21%, 22%, and 23%. Co is 0.05% to 1.00%, such as 0.05%, 0.08%, 0.1%, 0.2%, 0.4%, 0.6%, 0.8%, and 1.0%. Mo is 8%, 8.5%, 9.0%, 9.5%, and 10.0%. Fe is 0.1% to 5.0%, such as 0.1%, 0.5%, 1.0%, 2.0%, 3.0%, 4.0%, and 5.0%.

[0114] In some embodiments, the large-weight, wide-width high-temperature alloy coils described in this invention are cobalt-based high-temperature alloys, such as Hastelloy C276 alloy; the composition of the large-weight, wide-width high-temperature alloy coils, in mass percentage, is: Cr: 14.5–16.5%, Mo: 15.0–17.0%, Fe: 4.0–7.0%, W: 3.0–4.5%, C: ≤0.01%, Mn: ≤1.0%, Si: ≤0.08%, P: ≤0.04%, S: ≤0.03%, Co: ≤2.5%, V: ≤0.35%, with Ni as the balance.

[0115] For example, in the composition of Hastelloy C276 alloy, Cr is 14.5%, 15.0%, 15.5%, 16.0%, and 16.5%; Mo is 15.0%, 15.5%, 16.0%, 16.5%, and 17.0%; Fe is 4.0%, 4.5%, 5.0%, 5.5%, 6.0%, 6.5%, and 7.0%; W is 3.0%, 3.5%, 4.0%, and 4.5%; Mn is 0.001% to 1.0%, for example, 0.005%, 0.01%, 0.05%, 0.1%, 0.5%, and 1.0%; and Si is 0.001% to 0.08%, for example, 0.005%, 0.01%, 0.02%, 0.05%, and 0.08%. V is 0.001% to 0.35%, for example 0.005%, 0.01%, 0.05%, 0.1%, 0.2%, 0.3%, and 0.35%.

[0116] The technical solution of the present invention will be further described in detail below with reference to specific embodiments and comparative examples.

[0117] Example 1:

[0118] This embodiment provides a method for preparing large-weight, wide-width high-temperature alloy coils:

[0119] The large-coil, wide-width high-temperature alloy sheet is Hastelloy C276 alloy, with the following composition by mass percentage: Cr: 16.19%, Mo: 15.42%, Fe: 6.8%, W: 3.38%, C: 0.005%, Mn: 0.48%, Si: 0.06%, P: 0.015%, S: 0.001%, Co: 0.01%, V: 0.01%, Ni as the balance; the T of this alloy composition... 初熔 =1325℃, T 终熔 =1370℃;

[0120] The method for preparing the large-weight, wide-width high-temperature alloy coil includes the following steps:

[0121] S1. Slab pretreatment:

[0122] The forged slab, with a thickness of 195 mm, a width of 1050 mm, and a length of 1950 mm, undergoes homogenization heat treatment. The forged slab is then loaded into a heating furnace, ensuring a furnace temperature of 500℃, and heated at a rate of 35℃ / h until the homogenization heat treatment temperature T is reached. 均匀化 =0.88T 初熔 The heat preservation is carried out for a time t1 = 9δ1 = 9 × 195 mm = 1755 min.

[0123] After homogenization heat treatment, the surface of the slab is ground to achieve a state free of defects such as cracks, corner cracks, and scabs. After grinding, the surface roughness Ra value of the slab is 0.8 to 1.6 μm.

[0124] S2, Hot-rolled coil:

[0125] The pretreated slab is hot-rolled into a thin slab in the first hot rolling process; the thin slab is then hot-rolled into a coil in the second hot rolling process.

[0126] In the first hot rolling, the slab pretreated in step S1 is loaded into the heating furnace, ensuring a furnace loading temperature of 500°C. The furnace temperature is increased at a rate of 60°C / h until the first hot rolling heating temperature of 0.95T is reached. 初熔 Insulate for heat preservation, heat preservation time t 21 =9δ1=9×195mm=1755min; After the heat preservation is completed, the first hot rolling is carried out. The cumulative reduction rate of the first hot rolling is 90%, that is, from the thickness δ1=195mm, the slab thickness is reduced to the thickness δ after the first hot rolling. 21 =19.5mm. Specifically, in the first hot rolling, there are 14 rolling passes. For passes 1-5, the reduction rate is controlled at 15-20%; for passes 6-10, the reduction rate is controlled at 10-15%; and for passes 11-14, the reduction rate is controlled at 5-10%. The rolling speed is 10m / s, the rolling pressure is 3000KN, and the final rolling temperature is 0.70T. 初熔 After the first hot rolling is completed, water cooling is used to cool the roll, and the water cooling time is controlled to be 5 seconds.

[0127] In the second hot rolling process, the thin slab is loaded into a heating furnace for online heating compensation at a temperature of 0.9T. 初熔 Insulation time t 22 =7δ 21 =7×19.5mm=136.5min; After online heating is completed, a second hot rolling is performed. The cumulative reduction rate of the second hot rolling is 71%, from the thickness δ 21 =19.5mm, after a second hot rolling process, the slab thickness δ is reduced. 22=5.5mm. Specifically, in the second hot rolling, there are 10 rolling passes. For passes 1-5, the reduction rate is controlled at 15-20%; for passes 6-10, the reduction rate is controlled at 5-15%. The rolling speed is 10m / s, the rolling pressure is 3000KN, and the final rolling temperature is 0.65T. 初熔 After the second hot rolling is completed, air cooling is performed.

[0128] S3. Solution treatment and surface treatment of rolled blanks:

[0129] The hot-rolled coil is first subjected to solution treatment, and then surface treatment to obtain intermediate coil products.

[0130] In the solution treatment of the rolled blank, the solution treatment temperature is 0.95T before charging into the furnace. 初熔 Insulation time t3=7δ 22 =7×5.5mm=38.5min. After the solution treatment and heat preservation are completed, rapid water cooling is performed, and the water cooling time after solution treatment is controlled to be 5s.

[0131] After the solution treatment is completed, the surface treatment includes removing the oxide scale from the surface of the coil using an acid pickling line;

[0132] S4. Cold rolling and intermediate annealing of semi-finished coils:

[0133] The intermediate coil is subjected to a single-pass cold rolling process with a cumulative reduction rate of 41.8%, a rolling pass of 5.5mm-4.4mm-4.18mm-3.84mm-3.38mm-3.20mm (target thickness δ4), and a pass reduction rate of 20%-5%-8%-12%-5.3%; the rolling speed is 3m / s, and the rolling pressure is 700 tons of force.

[0134] The coils that have undergone the first cold rolling process are then subjected to intermediate annealing at a temperature of 0.8T. 初熔 The heat preservation time t4 = 6.0δ4 = 6 × 3.2 mm = 19.2 min;

[0135] After intermediate annealing, the coils that have reached the target thickness are surface treated. An online grinding line is used to remove the oxide scale from the surface of the semi-finished coils, ensuring that the surface roughness Ra value of the semi-finished coil blank after grinding is 0.3 to 0.5 μm, thus obtaining the semi-finished coil.

[0136] S5. Cold rolling and processing of finished coils:

[0137] The semi-finished coil is cold-rolled to obtain the finished coil; the finished coil is then subjected to solution treatment and surface treatment in sequence to obtain the large-weight, wide-width high-temperature alloy coil.

[0138] In the process of cold rolling the semi-finished coil, the total cold rolling reduction rate is 37.5%, the rolling pass is 3.2mm-2.56mm-2.25mm-2.14mm-2.0mm (target thickness), the reduction rate per pass is 20%-12%-5%-7%, the rolling speed is 3m / s, and the rolling pressure is 800 tons of force.

[0139] The finished coil is subjected to solution treatment at a temperature of 0.82T. 初熔 The heat preservation time t5=7δ5=7×2.0mm=14min;

[0140] The solution-treated coil is then subjected to surface treatment, which includes removing the oxide scale from the surface of the coil using an online grinding line, ensuring that the surface roughness Ra value of the finished coil blank after grinding is ≤0.1μm.

[0141] The alloy composition and preparation steps of Examples 2 to 8 and Comparative Examples 1 to 7 are basically the same as those of Example 1, except for the specific process parameters, as shown in Table 1.

[0142] Table 1: Process parameters for the examples and comparative examples

[0143]

[0144]

[0145]

[0146] The process parameters for Examples 9 to 16 are the same as those for Examples 1 to 8, respectively, except for the alloy composition. The set temperature is based on the T value of the corresponding alloy. 初熔 and T 终熔 Conversion was performed; the alloy compositions of Examples 9 to 16 were all GH3625 alloy, specifically as follows (by mass percentage): C: 0.022%, Cr: 22.55%, Co: 0.21%, Mo: 8.54%, Fe: 0.5%, Al: 0.25%, Ti: 0.30%, Nb: 3.43%, Si: 0.14%, Mn: 0.23%, S: 0.005%, P: 0.005%, Cu: 0.006%, Ni as the balance; the T of this alloy composition... 初熔 =1290℃, T 终熔 =1350℃.

[0147] Table 2. Parameters and results of high-temperature alloy coils in the examples and comparative examples (Hastelloy C276 alloy)

[0148]

[0149]

[0150] Table 3. Parameters and test results of high-temperature alloy coils (GH3625 alloy) in the examples.

[0151] width thickness Roll weight Thickness accuracy Surface roughness Example 9 1030mm 2.0mm 3.05t ±2.7%δ 0.08μm Example 10 1030mm 2.0mm 3.05t ±2.3%δ 0.08μm Example 11 1030mm 2.0mm 3.05t ±2.5%δ 0.07μm Example 12 1030mm 2.0mm 3.05t ±2.3%δ 0.07μm Example 13 1030mm 2.0mm 3.05t ±2.6%δ 0.08μm Example 14 1030mm 2.0mm 3.05t ±2.5%δ 0.07μm Example 15 1030mm 2.0mm 3.05t ±2.3%δ 0.07μm Example 16 1030mm 0.5mm 3.05t ±2.1%δ 0.07μm

[0152] The mechanical properties of embodiments 1-16 of the present invention are as follows: R m ≥825MPa, specified plastic elongation strength R p0.2 ≥420MPa; elongation after fracture 60%–70%. From Figure 2 It can be seen that the high-temperature alloy coils with large roll weight and wide width obtained in the embodiments of the present invention have good microstructure uniformity.

[0153] The above description is only a preferred embodiment of the present invention, but the scope of protection of the present invention is not limited thereto. Any changes or substitutions that can be easily conceived by those skilled in the art within the scope of the technology disclosed in the present invention should be included within the scope of protection of the present invention.

Claims

1. A method for preparing large-weight, wide-width high-temperature alloy coils, characterized in that, Includes the following steps: S1. Slab pretreatment: The forged slab, i.e. the forged plate blank, is subjected to homogenization heat treatment, the forged plate blank is loaded into a heating furnace, the loading temperature is ensured to be ≤700℃, the furnace is heated at a rate of 30~50℃ / h until the homogenization heat treatment temperature T 均匀化 =0.88T 初熔 ~0.92T 终熔 is reached, and then the temperature is kept constant for a time t1≥7δ1, the unit of t1 is min, and δ1 is the thickness of the forged plate blank and the unit is mm; S2, Hot-rolled coil: The pretreated slab is hot-rolled into a thin slab in the first hot rolling process; the thin slab is then hot-rolled into a coil in the second hot rolling process. In the first hot rolling process, the pretreated slab is loaded into the heating furnace, ensuring that the furnace loading temperature is ≤700℃. The temperature is then increased with the furnace at a rate of 50~60℃ / h until the first hot rolling heating temperature = (0.9~0.95)T is reached. 初熔 Insulate for heat preservation, heat preservation time t 21 ≥7δ1,t 21 The unit is min, δ1 is the thickness of the forged slab in mm, and the final rolling temperature is (0.65~0.70) T. 初熔 ; In the second hot rolling process, the thin slab is loaded into a heating furnace for online heating compensation at a temperature of (0.9~0.95)T. 初熔 Insulation time t 22 ≥5δ 21 , t 22 The unit is min, δ 21 The thickness of the slab obtained from the first hot rolling is in mm, and the final rolling temperature is (0.65~0.70) T. 初熔 ; S3. Solution treatment and surface treatment of rolled blanks: The hot-rolled coil is first subjected to solution treatment, and then to surface treatment to obtain an intermediate coil product; the solution treatment temperature in the coil is (0.80~0.95)T. 初熔 Insulation time t3≥5δ 22 t3 is in min, δ 22 The thickness of the coil obtained from the second hot rolling is in mm; S4. Cold rolling and intermediate annealing of semi-finished coils: The intermediate coil is subjected to a single-pass cold rolling process, with a cumulative reduction rate of 25% to 50%. The coil after the single-pass cold rolling process is then subjected to intermediate annealing. This process of single-pass cold rolling and intermediate annealing is repeated until the coil reaches the target thickness. The coil that has reached the target thickness undergoes surface treatment to obtain a semi-finished coil product. The intermediate annealing temperature is (0.80~0.95)T. 初熔 The heat preservation time t4≥4δ4, where t4 is in min and δ4 is the thickness of the coil after one cold rolling process before the intermediate annealing process, and the unit is mm. S5. Cold rolling and processing of finished coils: The semi-finished coil is cold-rolled to obtain the finished coil; the finished coil is then subjected to solution treatment and surface treatment in sequence to obtain the large-weight, wide-width high-temperature alloy coil; in the solution treatment, the solution treatment temperature is (0.8~0.95)T. 初熔 The heat preservation time t5≥4δ5, where t5 is in min and δ5 is the thickness of the finished coil in mm.

2. The method for preparing large-weight, wide-width high-temperature alloy coils according to claim 1, characterized in that, In the first hot rolling process of step S2, the pretreated slab is loaded into the heating furnace, ensuring the furnace loading temperature is 600~700℃, and the temperature is increased with the furnace at a rate of 50~55℃ / h until the first hot rolling heating temperature = (0.91~0.93)T is reached. 初熔 Insulate for heat preservation, heat preservation time t 21 For 7δ1~8δ1, t 21 The unit is min, and δ1 is the thickness of the forged slab in mm; after the heat preservation is completed, the first hot rolling is carried out, and the cumulative reduction rate of the first hot rolling is 80~95%.

3. The method for preparing large-weight, wide-width high-temperature alloy coils according to claim 1, characterized in that, In the second hot rolling process of step S2, the thin slab is loaded into a heating furnace for online heating compensation, and the online heating compensation temperature is (0.91~0.94)T. 初熔 Insulation time t 22 5.0δ 21 ~10.0δ 21 , t 22 The unit is min, δ 21 The thickness of the slab obtained from the first hot rolling is in mm; after the online reheating is completed, a second hot rolling is carried out, and the cumulative reduction rate of the second hot rolling is 65~80%.

4. The method for preparing large-weight, wide-width high-temperature alloy coils according to claim 1, characterized in that, In the first hot rolling process of step S2, the final rolling temperature is (0.66~0.69)T. 初熔 ; and / or, In the second hot rolling process of step S2, the final rolling temperature is (0.66~0.69)T. 初熔 .

5. The method for preparing large-weight, wide-width high-temperature alloy coils according to claim 1, characterized in that, In step S3, the solution treatment temperature for the rolled blank is (0.82~0.94)T. 初熔 The heat preservation time t3 is 5.0δ. 22 ~10.0δ 22 t3 is in min, δ 22 The thickness of the coil obtained from the second hot rolling is in mm.

6. The method for preparing large-weight, wide-width high-temperature alloy coils according to claim 1, characterized in that, In the intermediate annealing process described in step S4, the intermediate annealing temperature is (0.82~0.94)T. 初熔 The heat preservation time t4 is 4δ4~10δ4, where t4 is in min and δ4 is the thickness of the coil after one cold rolling process before the intermediate annealing treatment, in mm.

7. The method for preparing large-weight, wide-width high-temperature alloy coils according to claim 1, characterized in that, In step S5, the total cold rolling reduction rate of the coil semi-finished product is 30-60%, the reduction rate decreases with each pass, and the reduction rate of each pass is controlled at 5-15%.

8. The method for preparing large-weight, wide-width high-temperature alloy coils according to claim 1, characterized in that, In the solution treatment in step S5, the solution treatment temperature is (0.85~0.95)T. 初熔 The heat preservation time t5 is (4~5)δ5, where t5 is in min and δ5 is the thickness of the finished coil in mm.

9. The method for preparing large-weight, wide-width high-temperature alloy coils according to claim 1, characterized in that, The width of the large-weight, wide-width high-temperature alloy coil is 1000~1100mm, the thickness is 0.5~2.0mm, the single coil weight is ≥3t, the thickness accuracy of the coil is within ±3%δ of the thickness, and the surface roughness Ra value of the coil is ≤0.1μm, where δ is the thickness of the large-weight, wide-width high-temperature alloy coil.

10. A high-weight, wide-width high-temperature alloy coil obtained by the preparation method according to any one of claims 1 to 9.

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