A kind of yield strength 1100MPa grade Cu-containing low alloy high-strength steel and its manufacturing method

Abstract

The invention relates to a Cu-containing low-alloy high-strength steel with a yield strength of 1100MPa and a manufacturing method thereof. The chemical components of the steel are C: 0.015%-0.050%, Si: 0.85%-0.95%, Mn: 0.45%-0.65%, P≤0.010%, S≤0.005%, Cr: 0.85%-1.00%, Ni: 2.30%-2.70%, Cu: 2.25%-2.65%, Zr: 0.105%-0.180%, Mo: 0.15%-0.30%, Alt: 0.195%-0.295%, Ni / Cu ratio is controlled at 1-1.2, and the remainder is Fe and impurities. Through the synergistic effect of elements such as Cu, Al, Mn, Ni, Si, Mo, and Zr, the "offline quenching + high temperature tempering" process is adopted to form the dispersion precipitation of Cu-containing nano-metastable phase and the precipitation of Zr and / or Mo carbides, combined with solid solution strengthening, so that the produced steel plates have excellent high strength, excellent low-temperature toughness, welding performance and cold forming performance.

Description

Technical Field

[0001] The present invention relates to the technical field of low alloy high strength steel production, and in particular to a Cu-containing low alloy high strength steel with a yield strength of 1100 MPa and a manufacturing method thereof. Background Art

[0002] Traditional high-strength steel mainly obtains a good match of strength and toughness by adding a large amount of alloy elements and increasing the carbon content, but high carbon content and alloy content will lead to serious deterioration of weldability. With the vigorous development of microalloying technology, the design concept and performance of low-alloy high-strength steel are also constantly developing and improving. The upgraded low-alloy high-strength steel is widely used in many fields such as oil pipelines, high-rise building structures, bridges, railway transportation and excavation equipment due to its relatively low cost, high strength, high toughness, easy welding and easy processing. It can not only increase the load capacity of components and improve safety performance, but also reduce its own weight, which meets the requirements of energy-saving and environmental protection development.

[0003] A Chinese patent application with publication number CN 114058815 A discloses "a 1150MPa grade high-strength, high-toughness, easy-to-weld nano steel and its preparation method", which uses Cu-containing nanophase precipitation strengthening, Nb and Ti microalloy strengthening and tempering treatment to achieve strength and toughness matching, with a yield strength higher than 1150MPa, but the Ni content in the steel is higher than 6%, and the production cost is relatively high.

[0004] The Chinese patent application with publication number CN 110358970 A discloses a "welded structural bainitic high-strength steel with a yield strength of 1100 MPa and its preparation method". The product has a Cu--Ni-Al component system and adopts an online quenching + aging treatment process to obtain a nano-scale precipitation strengthening phase to achieve the yield strength requirement of 1100 MPa, but its low-temperature impact toughness at -40°C is less than 60J, and the toughness is poor.

[0005] The Chinese patent application with publication number CN 110358971 A discloses "a low-carbon ultra-high-strength steel with a yield strength of 1300 MPa and a preparation method thereof". The product has a Cu--Ni-Cr-Al component system and uses an online quenching + aging treatment process to obtain a nano-scale precipitation strengthening phase to achieve the yield strength requirement of 1300 MPa, but its low-temperature impact toughness at -60°C is less than 50J, and the toughness is poor.

[0006] A Chinese patent application with publication number CN 104513936 A discloses "a quenched and tempered high-strength steel with a yield strength of 1100 MPa and a production method thereof". The C content in the steel is 0.17-0.21%. The high carbon content will significantly deteriorate the welding performance of ultra-high-strength steel.

[0007] The Chinese patent application with publication number CN 106834942 A discloses "a copper-containing nanophase reinforced medium manganese steel and its preparation method". The steel plate belongs to medium manganese automobile steel with a strength-plasticity product of more than 30GPa% and a tensile strength of more than 1400MPa. However, the Mn content in the steel is greater than 6% and the Ni, W, Mo and Al contents are relatively high, resulting in high production costs.

[0008] The steel types and production methods involved in the above-mentioned patent documents have certain defects and cannot fully meet the use requirements of high-strength steel in different fields. How to use suitable chemical composition and reasonable production process to produce a high-strength, excellent toughness and ductility Cu-containing low-alloy high-strength steel plate is one of the technical difficulties that need to be solved urgently in this field. Summary of the invention

[0009] The present invention provides a Cu-containing low-alloy high-strength steel with a yield strength of 1100MPa and a manufacturing method thereof. Through the synergistic effect of elements such as Cu, Al, Mn, Ni, Si, Mo, and Zr, an "offline quenching + high-temperature tempering" process is adopted to form a Cu-containing nano-metastable phase dispersion precipitation and Zr and / or Mo carbide precipitation precipitation, and combined with solid solution strengthening, the produced steel plate has high strength, excellent low-temperature toughness, good welding performance and cold forming performance, and at the same time has a cost advantage over traditional high-strength alloy steels.

[0010] In order to achieve the above object, the present invention adopts the following technical solutions:

[0011] A Cu-containing low-alloy high-strength steel with a yield strength of 1100 MPa. The chemical components of the steel are, by weight percentage, C: 0.015%-0.050%, Si: 0.85%-0.95%, Mn: 0.45%-0.65%, P≤0.010%, S≤0.005%, Cr: 0.85%-1.00%, Ni: 2.30%-2.70%, Cu: 2.25%-2.65%, Zr: 0.105%-0.180%, Mo: 0.15%-0.30%, Alt: 0.195%-0.295%; the Ni / Cu ratio is controlled at 1-1.2; the balance is Fe and unavoidable impurities.

[0012] Furthermore, the steel contains Cu nano-metastable phase dispersion precipitation and Zr / Mo carbide precipitation precipitation.

[0013] Furthermore, the yield strength of the finished steel plate is ≥1100MPa, the tensile strength is ≥1140MPa, the elongation after fracture is ≥16%, the cross-sectional shrinkage is ≥55%, and the longitudinal impact energy KV2 at -60°C is ≥80J.

[0014] A method for manufacturing Cu-containing low-alloy high-strength steel with a yield strength of 1100 MPa, the production process includes smelting, continuous casting, heating, rolling and heat treatment; the specific control process is as follows:

[0015] 1) Smelting;

[0016] It includes hot metal pretreatment, converter smelting, LF refining and RH vacuum treatment process; among which, before LF refining, the ladle is purged with argon statically, the argon blowing time is greater than 15 minutes, and the RH cycle time is greater than 12 minutes;

[0017] 2) Continuous casting;

[0018] The superheat of the tundish is controlled at 19-22°C, and dynamic soft reduction and electromagnetic stirring are applied; the continuous casting billet is slowly cooled at a temperature of 480-500°C and a slow cooling time of more than 72 hours;

[0019] 3) heating;

[0020] The heating rate of the preheating section is 7-9°C / min; the heating rate of the heating section is 10-13°C / min, and the heating temperature is 1245-1280°C; the holding time of the soaking section is greater than 36 minutes; the total heating time is 212-260 minutes;

[0021] 4) rolling;

[0022] Two-stage controlled rolling is adopted; the rough rolling and final rolling temperature is 1083-1123℃; the finishing rolling temperature is 820-940℃, and the finishing rolling temperature is 785℃-837℃; the finishing rolling reduction rate is controlled at 66%-72%;

[0023] 5) Heat treatment;

[0024] The offline quenching + high temperature tempering process is adopted; the quenching temperature is 880-900℃, and after keeping warm for 40-80min, it is water-cooled to room temperature; tempering is carried out at 500-520℃, the holding time is 80-120mm / min, and finally air-cooled to room temperature.

[0025] Compared with the prior art, the present invention has the following beneficial effects:

[0026] 1) Through the synergistic effect of elements such as Cu, Al, Mn, Ni, Si, Mo, and Zr, the "offline quenching + high temperature tempering" process is adopted to form the dispersion precipitation of Cu-containing nano-metastable phase and the precipitation precipitation of Zr and / or Mo carbides, combined with solid solution strengthening, so that the produced steel plate has excellent high strength, excellent low temperature toughness and good welding performance;

[0027] 2) The yield strength of the finished steel plate shall be ≥1100MPa, the tensile strength shall be ≥1140MPa, the elongation after fracture shall be ≥16%, the cross-sectional shrinkage shall be ≥55%, and the longitudinal impact energy KV2 at -60℃ shall be ≥80J. DETAILED DESCRIPTION

[0028] The invention discloses a Cu-containing low-alloy high-strength steel with a yield strength of 1100 MPa. The chemical components of the steel are, by weight percentage, C: 0.015%-0.050%, Si: 0.85%-0.95%, Mn: 0.45%-0.65%, P≤0.010%, S≤0.005%, Cr: 0.85%-1.00%, Ni: 2.30%-2.70%, Cu: 2.25%-2.65%, Zr: 0.105%-0.180%, Mo: 0.15%-0.30%, Alt: 0.195%-0.295%; the Ni / Cu ratio is controlled at 1-1.2; the balance is Fe and unavoidable impurities.

[0029] Furthermore, the steel contains Cu nano-metastable phase dispersion precipitation and Zr and / or Mo carbide precipitation precipitation.

[0030] Furthermore, the yield strength of the finished steel plate is ≥1100MPa, the tensile strength is ≥1140MPa, the elongation after fracture is ≥16%, the cross-sectional shrinkage is ≥55%, and the longitudinal impact energy KV2 at -60°C is ≥80J.

[0031] The present invention discloses a method for manufacturing a Cu-containing low-alloy high-strength steel with a yield strength of 1100 MPa. The production process includes smelting, continuous casting, heating, rolling and heat treatment. The specific control process is as follows:

[0032] 1) Smelting;

[0033] It includes hot metal pretreatment, converter smelting, LF refining and RH vacuum treatment process; among which, before LF refining, the ladle is purged with argon statically, the argon blowing time is greater than 15 minutes, and the RH cycle time is greater than 12 minutes;

[0034] 2) Continuous casting;

[0035] The superheat of the tundish is controlled at 19-22°C, and dynamic soft reduction and electromagnetic stirring are applied; the continuous casting billet is slowly cooled at a temperature of 480-500°C and a slow cooling time of more than 72 hours;

[0036] 3) heating;

[0037] The heating rate of the preheating section is 7-9°C / min; the heating rate of the heating section is 10-13°C / min, and the heating temperature is 1245-1280°C; the holding time of the soaking section is greater than 36 minutes; the total heating time is 212-260 minutes;

[0038] 4) rolling;

[0039] Two-stage controlled rolling is adopted; the rough rolling and final rolling temperature is 1083-1123℃; the finishing rolling temperature is 820-940℃, and the finishing rolling temperature is 785℃-837℃; the finishing rolling reduction rate is controlled at 66%-72%;

[0040] 5) Heat treatment;

[0041] The offline quenching + high temperature tempering process is adopted; the quenching temperature is 880-900℃, and after keeping warm for 40-80min, it is water-cooled to room temperature; tempering is carried out at 500-520℃, the holding time is 80-120mm / min, and finally air-cooled to room temperature.

[0042] The working principle of each chemical component in the Cu-containing low alloy high-strength steel with a yield strength of 1100 MPa described in the present invention is as follows:

[0043] C is a major solid solution strengthening element. Too high a C content will deteriorate the welding performance and toughness and plasticity of the steel plate, and may form carbide precipitation with strong carbide alloy elements. The present invention controls the C content to be 0.015% to 0.050%.

[0044] Si is a ferrite-forming element, which can effectively reduce the austenite phase region and expand the ferrite phase region, and is an important solid solution strengthening element; too high Si content will reduce the toughness of the steel plate and form iron oxide scale that is difficult to remove during the rolling process; the present invention controls the Si content to 0.85% to 0.95%.

[0045] The main function of Mn in steel is solid solution strengthening. It is an austenite forming element. At the same time, Mn and Ni elements can be compositely precipitated in the Cu-containing nano-metastable phase, which can improve the strength and low-temperature toughness of the steel plate. However, excessive Mn content will seriously reduce the plasticity of the steel. The present invention controls the Mn content to be 0.45% to 0.65%.

[0046] P is an impurity element in steel, which will deteriorate the toughness, plasticity and welding performance of the steel. The P content is controlled below 0.010% in the present invention.

[0047] S is an impurity element in steel, which can significantly reduce the plasticity, toughness and welding performance of the steel. The present invention controls the S content to be below 0.005%.

[0048] Cr is a ferrite-forming element, which can effectively reduce the austenite phase area and expand the ferrite phase area, and can prevent the precipitation of Cu-containing nanophase during the cooling process after rolling or austenitization, as well as the nucleation and growth of Cu-containing nanophase, and significantly improve the hardenability of steel and the tempering stability after heat treatment; Cr is also an effective element for improving the weather resistance of steel. However, too high Cr content will deteriorate the welding performance of the steel plate. The present invention controls the Cr content to 0.85% to 1.00%.

[0049] Ni can significantly improve the low-temperature impact toughness and hardenability of steel plates, promote the Cu-Ni enriched phase in the steel to be retained in the oxide layer in a granular form, and improve the hot brittleness problem of Cu-containing steel; when the Ni / Cu ratio is above 1, liquid Cu will not appear; Ni in solid solution can improve the strength of ferrite; Ni can act as a nucleation particle to promote the precipitation of Cu nanometastable phase, and can also be compounded with Mn and Al in Cu-containing nanometastable phases to precipitate, optimizing the strength and low-temperature toughness of steel plates; in addition, Ni is an important element for improving the seawater corrosion resistance of steel. However, too high a Ni content will cause residual austenite in the steel, resulting in uneven organization, increasing costs and affecting welding performance. The present invention controls the Ni content to be between 2.30% and 2.70%.

[0050] Cu is an important strengthening element in the steel of the present invention. The solid solubility of Cu in austenite and ferrite is very different. Under certain heat treatment conditions, the dispersion and precipitation of Cu-containing nanophases of different shapes, sizes, quantities and distribution positions can be controlled to effectively improve the strength of the steel, improve the low-temperature toughness of the steel, and improve the welding and seawater corrosion resistance of the steel. The present invention controls the Cu content to be 2.25% to 2.65%.

[0051] Zr is a ferrite forming element with excellent hardenability; it is a strong carbonitride forming element, and Zr carbonitride is precipitated during the tempering isothermal transformation process; Zr and Mo elements are precipitated in the form of second phase particles of (Zr, Mo) C, which prevents grain boundary growth, refines grains, and pins dislocations to increase the strength of steel, while improving the low-temperature toughness of steel and the welding performance of steel. The present invention controls the Zr content to 0.105% to 0.180%.

[0052] Mo is a ferrite-forming element that can improve the hardenability and tempering stability of steel. MoC is formed during the isothermal transformation of steel, and precipitates with Zr in the form of (Zr, Mo)C to improve the strength and low-temperature toughness of steel. Mo acts together with Cr during tempering at different temperatures to ensure the stability of the tempered structure, including the nano-metastable phase of Cu contained in the precipitate, so that the steel plate obtains excellent comprehensive mechanical properties. However, when the Mo content is too high, the production cost will increase and the welding performance of the steel will be affected. In the present invention, the Mo content is controlled at 0.15% to 0.30%.

[0053] Al is a ferrite-forming element and a commonly used deoxidizer in steel. It can improve the corrosion resistance of steel and has a better effect when used in combination with Cr-Mo-Cu-Si. Al in Cu-containing steel can promote the precipitation of Cu-containing nanophases. Al can also be compounded with Mn or Ni in Cu-containing nanometastable phases to ensure the strength of steel. Al first exists as a deoxidizer in steel, then combines with N to form AlN, and finally compounded with Mn or Ni in Cu-containing nanometastable phases. However, too high Al content will affect the low-temperature toughness of steel, and oxides are easily formed during the smelting process, causing flocculent flow, which seriously affects production. The present invention controls the Alt content to be between 0.195% and 0.295%.

[0054] The manufacturing method of the Cu-containing low alloy high-strength steel with a yield strength of 1100 MPa described in the present invention has a typical production process flow of: molten iron pretreatment → converter smelting → refining outside the furnace (LF) → RH vacuum treatment → continuous casting (electromagnetic stirring) → slab continuous casting → slab stacking → slab cleaning → heating → rolling → flaw detection → heat treatment → inspection → storage. Among them:

[0055] 1. Smelting process: Before LF refining, ensure that the static argon blowing time of the ladle is greater than 15 minutes, and the RH cycle time is greater than 12 minutes; through LF+RH double refining, it can ensure that non-metallic inclusions are fully floated, greatly reduce the inclusion content in the molten steel, and at the same time ensure that the nitrogen, hydrogen and oxygen contents are at extremely low levels.

[0056] 2. Continuous casting process: The superheat of the tundish is controlled at 19-22°C, and dynamic light pressure and electromagnetic stirring are applied; the continuous casting billet enters the slow cooling pit for slow cooling, the slow cooling temperature is 480-500°C, and the slow cooling time is greater than 72h. After leaving the slow cooling pit, it is cleaned in time. In conjunction with the continuous casting process, the qualified rate of steel plate flaw detection can be improved and the crack defects on the rolling edge can be reduced.

[0057] 3. Heating process: The heating rate of the preheating section is 7-9℃ / min, the heating rate of the heating section is 10-13℃ / min, the heating temperature is 1245-1280℃, the holding time of the soaking section is greater than 36min, and the total heating time is 212-260min. The heating speed should be slowed down in the preheating stage to prevent the continuous casting billet from cracking due to excessive heating. The heating rate in the heating section is increased to improve the heating efficiency. The higher heating temperature combined with sufficient soaking section holding time and total heating time can make the alloy elements fully dissolved and evenly distributed, and the segregated elements in the center of the billet are fully diffused to ensure the ideal billet heating organization state.

[0058] 4. Rolling: Two-stage controlled rolling is adopted, the rough rolling and final rolling temperature is 1083-1123℃, to ensure that the steel plate is rolled in the recrystallized state; the finishing rolling temperature is 820-940℃, the finishing rolling temperature is controlled at 785℃-837℃, and the finishing rolling reduction rate is controlled at 66%-72%; after two-stage rolling, a uniform rolled structure is obtained, ready for heat treatment.

[0059] 5. Heat treatment: The "offline quenching + high temperature tempering" process is adopted, the quenching temperature is 880-900℃, and after keeping warm for 40-80min, it is quickly cooled to room temperature by water. The quenched structure is obtained by rapid cooling. Cu exists in the form of supersaturated solid solution, and the dislocation density in the steel is extremely high, which provides a large number of nucleation points for the precipitation of Cu-containing phase during the tempering process. The cooling rate can also make Zr, Cu, and Al in solid solution, which is convenient for obtaining nano-scale precipitation strengthening phase during subsequent tempering. The offline quenched steel plate has good uniformity and high comprehensive performance; the tempering temperature is 500-520℃. The tempering temperature is the most important process parameter to ensure the comprehensive performance of the steel plate. During the tempering process, the Cu-containing nano-metastable phase is dispersed and precipitated in the ferrite matrix, dislocation lines, and grain boundaries. uThe nano-metastable phase continuously nucleates, precipitates, and grows, losing the coherence relationship with the matrix, weakening the strengthening effect on the steel part and greatly enhancing the toughness. It is in a semi-coherent or incoherent state with the ferrite matrix and exists in the form of clusters, dots, small blocks, etc., with a size distribution of approximately 1-25nm. At the same time, Zr or Mo carbides precipitate in the ferrite matrix and dislocation lines to compensate for the strength drop caused by the over-aging of the Cu nano-metastable phase due to tempering, ensuring that the steel plate has high strength and toughness. The tempering time is 80-120mm / min. Sufficient tempering time can ensure the uniformity and stability of the steel plate's organizational properties. Too long tempering time not only coarsens the precipitated phase but also reduces production efficiency and increases costs; air cooling to room temperature after tempering saves furnace cooling time and increases production efficiency.

[0060] The following embodiments are implemented on the premise of the technical solution of the present invention, and provide detailed implementation methods and specific operation processes, but the protection scope of the present invention is not limited to the following embodiments.

[0061] [Example]

[0062] In this embodiment, the production process flow of Cu-containing low-alloy high-strength steel with a yield strength of 1100 MPa is: molten iron pretreatment → converter smelting → refining outside the furnace (LF) → RH vacuum treatment → continuous casting (electromagnetic stirring) → slab continuous casting → slab stacking → slab cleaning → heating → rolling → flaw detection → heat treatment → inspection → warehousing.

[0063] The chemical composition of the steel in each embodiment is shown in Table 1, the smelting and continuous casting process parameters are shown in Table 2, the heating process parameters are shown in Table 3, the rolling and heat treatment process parameters are shown in Table 4, and the properties of the finished steel plate are shown in Table 5.

[0064] Table 1 Chemical composition of steel in each example (wt%)

[0065] Example C Si Mn P S Cr Ni Cu Zr Mo Alt Ni / Cu 1 0.022 0.90 0.51 0.008 0.003 0.91 2.43 2.31 0.129 0.21 0.211 1.052 2 0.016 0.85 0.49 0.007 0.003 0.85 2.37 2.26 0.132 0.19 0.203 1.049 3 0.027 0.88 0.48 0.008 0.004 0.89 2.50 2.29 0.153 0.18 0.237 1.092 4 0.019 0.87 0.46 0.006 0.004 0.87 2.61 2.47 0.141 0.27 0.229 1.057 5 0.020 0.92 0.47 0.008 0.003 0.93 2.60 2.51 0.161 0.23 0.243 1.036 6 0.033 0.86 0.45 0.007 0.003 0.90 2.56 2.39 0.159 0.22 0.264 1.071 7 0.044 0.89 0.52 0.006 0.003 0.98 2.59 2.43 0.169 0.24 0.253 1.066 8 0.039 0.93 0.59 0.007 0.002 0.94 2.63 2.57 0.180 0.27 0.277 1.023 9 0.049 0.91 0.61 0.007 0.003 0.95 2.64 2.60 0.173 0.29 0.295 1.015 10 0.045 0.95 0.65 0.006 0.004 1.00 2.69 2.58 0.179 0.28 0.289 1.043 11 0.047 0.94 0.63 0.006 0.003 0.97 2.67 2.62 0.176 0.29 0.283 1.019 12 0.048 0.95 0.64 0.007 0.004 0.99 2.70 2.64 0.177 0.30 0.291 1.023

[0066] Table 2 Smelting and continuous casting process parameters of each example steel

[0067] Example Argon blowing time, min RH cycle time, min Superheat, ℃ Slow cooling temperature, ℃ Slow cooling time, h 1 17 13 20 500 72 2 17 14 20 500 72 3 17 13 20 500 72 4 17 14 20 500 72 5 17 14 20 500 72 6 17 13 21 500 72 7 16 13 21 500 72 8 16 13 21 500 72 9 16 14 20 500 72 10 16 14 21 500 72 11 16 14 21 500 72 12 16 14 21 500 72

[0068] Table 3 Heating process parameters of each example steel

[0069]

[0070] Table 4 Rolling and heat treatment process parameters of each example steel

[0071]

[0072] Table 5 Mechanical properties of finished steel plates of various embodiments

[0073]

[0074] In Table 5, R eH is the upper yield strength, R m is the tensile strength, A is the elongation after fracture, and Z is the cross-sectional shrinkage.

[0075] The above description is only a preferred specific implementation manner of the present invention, but the protection scope of the present invention is not limited thereto. Any technician familiar with the technical field can make equivalent replacements or changes according to the technical scheme and inventive concept of the present invention within the technical scope disclosed by the present invention, which should be covered by the protection scope of the present invention.

Claims

1. A method for manufacturing Cu-containing low alloy high-strength steel with a yield strength of 1100 MPa, characterized in that: The chemical composition of the steel by weight percentage is C: 0.015% ~ 0.049%, Si: 0.85% ~ 0.95%, Mn: 0.45% ~ 0.59%, P ≤ 0.010%, S ≤ 0.005%, Cr: 0.85% ~ 1.00%, Ni: 2.30% ~ 2.70%, Cu: 2.25% ~ 2.65%, Zr: 0.105% ~ 0.180%, Mo: 0.15% ~ 0 .30%, Alt: 0.195%~0.295%; Ni / Cu ratio is controlled at 1~1.2; the balance is Fe and unavoidable impurities; the steel contains Cu nano-metastable phase dispersion and Zr and / or Mo carbide precipitation; the yield strength of the finished steel plate is ≥1100MPa, the tensile strength is ≥1140MPa, the elongation after fracture is ≥16%, the cross-sectional shrinkage is ≥55%, and the longitudinal impact energy KV2 at -60℃ is ≥80J; The production process includes smelting, continuous casting, heating, rolling and heat treatment; each process is controlled as follows: 1) Smelting; It includes hot metal pretreatment, converter smelting, LF refining and RH vacuum treatment process; among which, before LF refining, the ladle is purged with argon statically, the argon blowing time is greater than 15 minutes, and the RH cycle time is greater than 12 minutes; 2) Continuous casting; The superheat of the tundish is controlled at 19-22°C, and dynamic soft reduction and electromagnetic stirring are applied; the continuous casting billet is slowly cooled at a temperature of 480-500°C and a slow cooling time of more than 72 hours; 3) Heating; The heating rate of the preheating section is 7-9°C / min; the heating rate of the heating section is 10-13°C / min, and the heating temperature is 1245-1280°C; the holding time of the soaking section is greater than 36 minutes; the total heating time is 212-260 minutes; 4) rolling; Two-stage controlled rolling is adopted; the rough rolling and final rolling temperature is 1083~1123℃; the finishing rolling temperature is 820~940℃, and the finishing rolling temperature is 785℃~837℃; the finishing rolling reduction rate is controlled at 66%~72%; 5) Heat treatment; The offline quenching + high temperature tempering process is adopted; the quenching temperature is 880-900℃, and after keeping warm for 40-80min, it is water-cooled to room temperature; tempering is carried out at 500-520℃, the holding time is 80-120min, and finally air-cooled to room temperature.

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