High-carbon high-chromium alloy steel wide and thick plate and rolling method thereof

Abstract

The invention discloses a high-carbon high-chromium alloy steel wide and thick plate and a rolling method thereof. The rolling method comprises the following steps that S1, raw materials are heated in an annular furnace after being pretreated; s2, the roughing mill conducts reciprocating multi-pass rolling cogging, and the head and the tail are sheared through a hydraulic shear; s3, after the stepping furnace is heated, rolling is conducted through a continuous rolling unit, and rolling of the continuous rolling unit comprises the step that the continuous rolling unit with 4-8 racks is adopted for rolling; and S4, stacking and slowly cooling the rolled finished wide and thick plate, charging, preserving heat, cooling along with the furnace, discharging and emptying to obtain the qualified wide and thick plate blank. According to the rolling method for improving corner cracking of the high-carbon and high-chromium alloy steel wide and thick plate, the quality problem of corner cracking in the production process of the high-carbon and high-chromium alloy steel wide and thick plate in China is solved, the material utilization rate is increased, and then the market competitiveness of products is improved.

Description

Technical Field

[0001] This invention relates to the field of steel rolling technology, and in particular to a high-carbon, high-chromium alloy steel wide and thick plate and its rolling method. Background Technology

[0002] High-carbon, high-chromium alloy steel is widely used in tool steel and stainless steel applications, and is the most widely used steel grade in civilian products. To avoid hot deformation and cracking, its wide and thick plates are mostly formed by upsetting and drawing on a free forging machine. With the rapid development of production technology, hot rolling equipment is further developing towards larger scale, intelligence, and automation. The production technology of roughing mills and continuous rolling mills in the domestic and foreign steel industries is constantly improving, providing favorable conditions for the production of difficult-to-deform high-carbon, high-chromium wide and thick plates.

[0003] For example, Chinese patent application publication number CN118768382A discloses a production process for rolling 150-230mm steel plates from high-alloy extra-thick slabs. The total furnace time is set at 16-23 hours based on the slab thickness; the slab is fed into the furnace at room temperature, then heated to -750℃ at a rate of 80-120℃ / h, and held at 750℃ for 2-3 hours; then heated to 750-930℃ at a rate of 60-100℃ / h, and held at 930℃ for 1-2 hours; finally, heated to 930-1220℃ at a rate of 40-80℃ / h, and held at 1220℃ for 3-7 hours; the slab undergoes one descaling process in a descaling box before rolling; and the rolling temperature is controlled... During the roughing stage at 1000-1050℃, the first pass reduction is guaranteed to be 40-50mm, followed by a reduction of 20-25mm, a rolling force of 20000-29000kN, a roll gap of 350-600mm, and 5-13 rolling passes. In the finishing stage, the reduction is 12-22mm, the rolling force is 35000-45000kN, the roll gap is 150-300mm, and 7-12 rolling passes are used. After rolling, 4-8 sets of water are turned on, and the temperature is brought back to 650-670℃. The rolled steel plate is then placed on a cooling bed for cooling. When the temperature reaches 450-550℃, it is transferred to a slow cooling pit for further cooling. This invention effectively avoids cracks caused by uneven stress and heat dissipation during the heating, rolling, and slow cooling processes of high-alloy steel, which leads to large mechanical and thermal stress gradients.

[0004] For example, Chinese patent application CN103909092A discloses a one-fire rolling method for Cr12MoV cold-work die flat steel, including furnace loading, heating, rolling, and annealing processes. Specifically, steel ingots are placed at 50-100mm intervals in a pusher-type double-slide heating furnace, and heated to 1180-1200℃ in four stages: preheating, low temperature, high temperature, and homogenization. The ingots are then removed from the furnace and fed into a rolling mill, where they undergo a vertical-to-horizontal flipping and one-fire rolling process to obtain semi-finished flat steel. After slow cooling and annealing, the finished flat steel is obtained. This invention eliminates the usual ingot billet preparation process, reducing the two-fire or even multi-fire rolling process to a single-fire rolling process, significantly shortening the process flow and improving production efficiency. The energy consumption per ton of steel, converted to standard coal, is 0.177 tons, lower than the average coal consumption level, and the production cost per ton of steel is only 800 yuan, lower than the industry standard.

[0005] For example, Chinese Patent Application Publication No. CN116511238A provides a rolling method for Cr12MoV flat steel, belonging to the field of cold work die steel processing technology. This invention involves continuously heating a Cr12MoV continuously cast billet, reciprocatingly rolling the resulting Cr12MoV ingot, and then annealing the resulting Cr12MoV rolled billet to obtain Cr12MoV flat steel. The total number of reciprocating rolling passes is n, where n = 10–16. The relative reduction rate of the first pass is 2–5%, the relative reduction rate of each pass in the 2nd–4th passes is independently 6–10%, the relative reduction rate of each pass in the 5th–(n-2)th passes is independently 15–20%, and the relative reduction rate of each pass in the (n-1)th–nth passes is independently 2–5%. This invention enables rolled Cr12MoV flat steel to have a low level of central porosity and carbide inhomogeneity, and it is produced in one firing process with a short manufacturing process and low energy consumption.

[0006] For example, Chinese patent application publication number CN103316910A discloses a rolling method for Cr12MoV flat steel. This method employs hot-feeding of ingots weighing more than 2 tons, hot-charging of ingots in a soaking furnace for heating and homogenization, secondary rolling on a primary rolling mill, and annealing, among other hot processing technologies. This solves the technical problem that Cr12MoV cold work die steel ingots could not be directly rolled into flat steel in the past. It can roll qualified Cr12MoV cold work die steel flat steel with a width of about 400mm, significantly reducing energy consumption and metallurgical manufacturing costs, thereby meeting market demand for this product.

[0007] High-carbon, high-chromium, thick plate alloy steels, represented by Cr12 series cold work die steels and 95Cr18 series stainless steels (wall thickness ≥ 50mm, width ≥ 400mm), are still mostly produced in China using free forging mills. Meanwhile, Baosteel and Hebei Iron & Steel have begun using roughing mills to roll high-carbon, high-chromium, thick plate alloy steels to reduce production costs, achieving some success. However, problems such as edge cracking and low product qualification rates have still emerged during the rolling process. A better solution to this problem has yet to be found domestically.

[0008] Therefore, proposing a rolling method to improve the edge and corner cracking of wide and thick high-carbon and high-chromium alloy steel plates is of guiding significance for special steel enterprises to reduce costs. Summary of the Invention

[0009] The main objective of this invention is to provide a high-carbon, high-chromium alloy steel wide and thick plate and its rolling method, which solves the quality problem of edge and corner cracking in the domestic production process of high-carbon, high-chromium alloy steel wide and thick plate, improves material utilization, and thus enhances the market competitiveness of the product.

[0010] According to one aspect of the present invention, a method for rolling thick plates of high-carbon, high-chromium alloy steel is provided, comprising the following steps: S1. Heating of raw materials in a ring furnace after pretreatment; S2. The roughing mill performs reciprocating multi-pass rolling for billet preparation, and the head and tail are sheared by hydraulic shears; S3. Rolling is performed on a continuous rolling mill after heating in a walking beam furnace. The continuous rolling process includes rolling using a 4-8 stand continuous rolling mill. S4. After the rolled thick plates are stacked and slowly cooled, they are loaded into the furnace, kept warm, and then cooled with the furnace before being removed from the empty furnace to obtain qualified thick plates.

[0011] According to one embodiment of the present invention, in step S1, the temperature of the first heating stage is controlled at 700~850℃, the temperature of the second heating stage is controlled at 1000~1150℃, the temperature of the third heating stage is controlled at 1220~1250℃, and the temperature of the three heat soaking stages is controlled at 1210~1235℃. The heating rate of the annular heating furnace is ≤80℃ / h.

[0012] According to one embodiment of the present invention, the walking cycle of the ring furnace is calculated as T=S*t / n; S is the billet diameter or maximum thickness, in mm; t is the thickness time coefficient, which is 5~20; n is the total number of teeth of the walking furnace.

[0013] According to one embodiment of the present invention, in step S2, the multi-pass rolling blanking includes at least two intermediate passes with a relative deformation rate ≥20%.

[0014] According to one embodiment of the present invention, preheating includes preheating the seamless steel pipe to 100~500°C.

[0015] According to one embodiment of the present invention, in step S2, the rolling speed of the roughing mill is ≥2m / s, the flow rate of the cooling water for the rolls during the rolling process is ≤50L / min, and the final rolling temperature is ≥1040℃.

[0016] According to one embodiment of the present invention, in step S3, the heating rate of the walking beam furnace is ≤80℃ / h, the first heating stage is controlled at 1100±10℃, the second heating stage is controlled at 1210±10℃, the soaking stage is controlled at 1180±10℃, and the walking cycle is 5~20min.

[0017] According to one embodiment of the present invention, in step S4, the rolled wide and thick plates are stacked and slowly cooled. After the temperature drops to 650~700℃, they are loaded into the furnace. The furnace temperature is controlled at 680±10℃. After holding at the temperature for 3~6 hours, they are slowly cooled to 200℃ with the furnace at a cooling rate of ≤30℃ / h and then removed from the furnace empty to obtain qualified wide and thick plate billets.

[0018] According to another aspect of the present invention, a thick plate of high-carbon high-chromium alloy steel is provided, which is prepared by the rolling method of the thick plate of high-carbon high-chromium alloy steel according to any one of the above technical solutions.

[0019] According to one embodiment of the present invention, in the high-carbon high-chromium alloy steel, C ≥ 0.85 wt% and Cr ≥ 12 wt%.

[0020] According to an embodiment of the present invention, a rolling method for high-carbon, high-chromium alloy steel thick plates solves the quality problem of edge and corner cracking in the domestic production process of high-carbon, high-chromium alloy steel thick plates, improves material utilization, and thus enhances the market competitiveness of the product. Attached Figure Description

[0021] To more clearly illustrate the technical solutions of the embodiments of the present invention, the accompanying drawings used in the embodiments will be briefly introduced below. Obviously, the drawings described below are only some implementation examples of the present invention. For those skilled in the art, other drawings can be obtained based on these drawings without creative effort.

[0022] Figure 1 A process flow diagram of a rolling method for a wide and thick plate of high-carbon high-chromium alloy steel according to an exemplary embodiment of the present invention is shown. Detailed Implementation

[0023] The following detailed description of the embodiments is intended to exemplify the principles of the present invention, but should not be construed as limiting the scope of the invention. The present invention can be implemented in many different forms and is not limited to the specific embodiments disclosed herein, but includes all technical solutions falling within the scope of the claims.

[0024] These embodiments are provided to make this disclosure thorough and complete, and to fully express the scope of the invention to those skilled in the art. It should be noted that, unless otherwise specifically stated, the relative arrangement of components and steps, material composition, numerical expressions, and values ​​set forth in these embodiments should be interpreted as merely exemplary and not as limiting.

[0025] It should be noted that, in the description of this invention, unless otherwise stated, "a plurality of" means two or more; the terms "upper," "lower," "left," "right," "inner," and "outer," etc., indicating orientation or positional relationships, are only for the convenience of describing this invention and simplifying the description, and do not indicate or imply that the device or element referred to must have a specific orientation, or be constructed and operated in a specific orientation, and therefore should not be construed as a limitation of this invention. When the absolute position of the described object changes, the relative positional relationship may also change accordingly.

[0026] It should also be noted that, in the description of this invention, unless otherwise explicitly specified and limited, the terms "installation," "connection," and "joining" should be interpreted broadly. For example, they can refer to a fixed connection, a detachable connection, or an integral connection; they can refer to a direct connection or an indirect connection through an intermediate medium. Those skilled in the art can understand the specific meaning of the above terms in this invention depending on the specific circumstances. When a specific device is described as being located between a first device and a second device, an intermediary device may or may not be present between the specific device and the first or second device.

[0027] All terms used in this invention have the same meaning as understood by one of ordinary skill in the art to which this disclosure pertains, unless otherwise specifically defined. It should also be understood that terms defined in general dictionaries should be interpreted as having meanings consistent with their meanings in the context of the relevant art, and not as idealized or highly formalized, unless expressly defined herein.

[0028] Techniques, methods, and equipment known to those skilled in the art may not be discussed in detail, but where appropriate, such techniques, methods, and equipment should be considered part of the specification.

[0029] like Figure 1 As shown, the present invention provides a method for rolling thick high-carbon, high-chromium alloy steel plates, which includes the following steps: S1. Heating of raw materials in a ring furnace after pretreatment; S2. The roughing mill performs reciprocating multi-pass rolling for billet preparation, and the head and tail are sheared by hydraulic shears; S3. Rolling is performed on a continuous rolling mill after heating in a walking beam furnace. The continuous rolling process includes rolling using a 4-8 stand continuous rolling mill. S4. After the rolled thick plates are stacked and slowly cooled, they are loaded into the furnace, kept warm, and then cooled with the furnace before being removed from the empty furnace to obtain qualified thick plates.

[0030] The rolling method for high-carbon, high-chromium alloy steel thick plates according to an embodiment of the present invention solves the quality problem of edge and corner cracking in the domestic production process of high-carbon, high-chromium alloy steel thick plates, improves material utilization, and thus enhances the market competitiveness of the product.

[0031] In some specific embodiments, step S1, the raw material pretreatment includes measuring the temperature of the required billet or hot-loaded billet, and then setting the charging temperature of the annular heating furnace according to the billet temperature. If the charging temperature and the billet temperature are too different, micro-cracks are easily caused at the edges and corners due to uneven thermal expansion.

[0032] Based on the above embodiments, in step S1, the temperature of the first heating stage is controlled at 700~850℃, the temperature of the second heating stage is controlled at 1000~1150℃, the temperature of the third heating stage is controlled at 1220~1250℃, and the temperature of the three heat equalization stages is controlled at 1210~1235℃. The heating rate of the annular heating furnace is ≤80℃ / h.

[0033] Three-stage heating and homogenization are used to ensure uniform temperature inside and outside the billet. Carbides in high-carbon, high-chromium steel (such as M7C3 and M23C6) need sufficient time to dissolve and distribute evenly at high temperatures; otherwise, undissolved carbides will become crack initiation sites.

[0034] The holding time in the homogenization zone of the ring furnace is ≥3.5h to ensure uniform temperature inside and outside the billet.

[0035] In some specific embodiments, the walking cycle of the ring furnace is calculated as T=S*t / n; S is the billet diameter or maximum thickness, in mm; t is the thickness time coefficient, which is 5~20; n is the total number of teeth of the walking furnace, to ensure that the heating time matches the billet size and avoid local overheating or underheating.

[0036] Based on the above embodiments, in step S2, the multi-pass rolling blanking includes at least two intermediate passes with a relative deformation rate ≥20%, which breaks down the coarse eutectic carbide network in the as-cast microstructure through intense plastic deformation. For example, after high-carbon chromium bearing steel GCr15 undergoes high-temperature diffusion annealing, large deformation rolling can refine and uniformly distribute the carbide particles, significantly reducing grain boundary brittleness and minimizing the risk of edge cracking.

[0037] In some specific embodiments, in step S2, the rolling speed of the roughing mill is ≥2 m / s, and the cooling water flow rate of the rolls during the rolling process is ≤50 L / min, which improves production efficiency and avoids excessive surface cooling. High-carbon, high-chromium steel has good plasticity at high temperatures, but rapid cooling will cause the surface layer to shrink faster than the core, generating tensile stress. Low cooling intensity can maintain the surface temperature, reduce the temperature gradient, and reduce thermal stress.

[0038] A final rolling temperature ≥1040℃ ensures that rolling is carried out within a single austenite region. Austenite has good plasticity and can effectively suppress crack initiation. If the final rolling temperature is too low, it enters a two-phase region (e.g., ferrite and austenite), increasing deformation inhomogeneity and making it easier for stress concentrations to form at the edges and corners.

[0039] Hydraulic shearing removes the head and tail of the billet, eliminating the original crack sources caused by ingot solidification shrinkage or uneven heating.

[0040] Based on the above embodiments, in step S3, the heating rate of the walking beam furnace is ≤80℃ / h, the first heating stage is controlled at 1100±10℃, the second heating stage is controlled at 1210±10℃, the soaking stage is controlled at 1180±10℃, and the walking cycle is 5~20min.

[0041] The secondary heating of the walking beam furnace further eliminates the stress that may be generated in the billet during transportation and shearing, and provides billets with uniform temperature for continuous rolling, ensuring the stability of the subsequent rolling process.

[0042] When the continuous rolling mill is used for rolling, the rolling speed is ≤1m / s.

[0043] In some specific embodiments, in step S4, the rolled thick plates are stacked and slowly cooled. After the temperature drops to 650~700℃, they are loaded into the furnace. The furnace temperature is controlled at 680±10℃. After holding at the temperature for 3~6 hours, they are slowly cooled to 200℃ with the furnace at a cooling rate of ≤30℃ / h before being removed from the empty furnace to obtain qualified thick plates.

[0044] This process reduces hardness and improves machinability and toughness. Simultaneously, the slow cooling process effectively eliminates residual rolling stress, preventing edge cracking caused by stress concentration.

[0045] This application also proposes a high-carbon, high-chromium alloy steel wide and thick plate, which is prepared by any of the rolling methods mentioned in the above technical solutions.

[0046] In some specific embodiments, the high-carbon high-chromium alloy steel contains C ≥ 0.85 wt%, Cr ≥ 12 wt%, and may contain alloying elements such as Mo, V, and Mn.

[0047] This rolling method uses 3t or larger ingots as billets and can produce the required wide and thick plates in one rolling process. Moreover, the resulting plates have good surface quality and are free from edge and corner cracks.

[0048] The present application will be further described below through specific embodiments.

[0049] Example 1 This embodiment uses 3.2t flat ingots to roll 50×650 (thickness*width) Cr12MoV wide and thick plates. The specific production steps include: Step 1: Raw material preparation Temperature was measured on each of the 3.2-ton Cr12MoV flat ingots smelted by electric furnace + LF + VD, and the surface temperature of the ingots was 635~680℃. Step 2: Heating in the Circular Furnace Heating rate is 50~60℃ / h. The temperature of the first heating stage is controlled at 700±10℃, the temperature of the second heating stage is controlled at 1050±10℃, the temperature of the third heating stage is controlled at 1230±10℃, and the temperature of the three heat-spreading stages is controlled at 1220±10℃. The stepping cycle is 10min, the number of teeth in the heat-spreading stage is 30, and the heat-spreading stage heat-spreading time is 5h. Step 3: Drafting on the roughing mill The rolls are rolled to 80×660 (thickness*width) mm in 15 passes, with the relative reduction rates of the 7th, 8th, 9th and 10th passes being 22%, 22.5%, 23.5% and 23%, respectively. The rolling speed is 2.2 m / s, the roll cooling water flow rate is 25 L / min, and the final rolling temperature is 1050~1060℃. Step 4: Hydraulic shearing The head and tail ends are cut flat using a hydraulic press to facilitate the continuous rolling mill's bite.

[0050] Step 5: Heating with a walking beam furnace Heating rate is 50~60℃ / h, heating stage 1 is controlled at 1100±10℃, heating stage 2 is controlled at 1210±10℃, heat soaking stage is controlled at 1180±10℃, stepping cycle is 15min, heat soaking stage has 10 teeth, and heat holding time is 150min.

[0051] Step Six: Rolling on the Continuous Rolling Mill The rolling process is carried out using a 6-stand continuous rolling mill (vertical-horizontal-vertical-horizontal-vertical-horizontal) at a rolling speed of 0.5 m / s.

[0052] Step 7: Annealing The rolled 50×650 (thickness*width) Cr12MoV wide and thick plates are stacked and slowly cooled. After the temperature drops to 650~700℃, they are put back into the furnace. The furnace temperature is controlled at 680±10℃. After holding at the temperature for 4 hours, they are slowly cooled to 200℃ with the furnace at a cooling rate of ≤30℃ / h. Then they are taken out of the empty furnace to obtain qualified wide and thick plate billets.

[0053] Example 2 This embodiment uses a 3.7t square ingot to roll 45×450 (thickness*width) 95Cr18MoV wide and thick plate. The specific production steps include: Step 1: Raw material preparation Temperature was measured on each of the 3.7-ton 95Cr18MoV square ingots produced by electric furnace + LF + VD smelting. The surface temperature of the ingots was 680~720℃. Step 2: Heating in the Circular Furnace Heating rate: 60~80℃ / h; heating stage 1 temperature controlled at 850±10℃; heating stage 2 temperature controlled at 1100±10℃; heating stage 3 temperature controlled at 1240±10℃; heat soaking stage 3 temperature controlled at 1230±10℃; stepping cycle: 15min; heat soaking stage: 30 teeth; heat soaking stage: 450min holding time. Step 3: Drafting on the roughing mill The rolls are rolled to 70×460 (thickness*width) mm in 17 passes, with the relative reduction rates of the 6th, 7th, 8th and 9th passes being 23%, 24.5%, 23% and 23%, respectively. The rolling speed is 2.5 m / s, the roll cooling water flow rate is 30 L / min, and the final rolling temperature is 1040~1050℃. Step 4: Hydraulic shearing The head and tail ends are cut flat using a hydraulic press to facilitate the continuous rolling mill's bite.

[0054] Step 5: Heating with a walking beam furnace Heating rate is 40~80℃ / h, heating stage 1 is controlled at 1100±10℃, heating stage 2 is controlled at 1210±10℃, heat soaking stage is controlled at 1180±10℃, stepping cycle is 12min, heat soaking stage has 10 teeth, and heat holding time is 120min.

[0055] Step Six: Rolling on the Continuous Rolling Mill The rolling process is carried out using an 8-stand continuous rolling mill with a rolling speed of 0.55 m / s.

[0056] Step 7: Annealing The rolled 45×450 (thickness*width) 95Cr18MoV wide and thick plates are stacked and slowly cooled. After the temperature drops to 650~700℃, they are put back into the furnace. The furnace temperature is controlled at 680±10℃. After holding at this temperature for 3.5h, they are slowly cooled to 200℃ with the furnace at a cooling rate of ≤30℃ / h. The empty furnace is then removed to obtain qualified wide and thick plate billets.

[0057] After implementation, this application can effectively solve the problem of edge and corner cracking in wide and thick high-carbon and high-chromium alloy steel plates, significantly reducing the scrap rate. By matching the raw material temperature with the furnace charging temperature, and using stepped heating and homogenization, the uniform temperature inside and outside the billet is ensured, avoiding micro-cracks caused by thermal stress. The intermediate passes of rough rolling have a relative deformation rate of more than 20% for more than 2 passes, breaking down coarse carbides and refining the microstructure. Combined with a rolling speed of ≥2m / s, cooling water of ≤50L / min and a final rolling temperature of ≥1040℃, cracks caused by uneven deformation and excessive surface cooling are reduced. Continuous rolling of 4-8 stands (≤1m / s) controls the temperature rise and avoids hot cracking. After slow cooling in stacks, the plate is held at 680±10℃ for 3-6 hours and then cooled in the furnace at ≤30℃ / h to release residual stress and promote carbide spheroidization, improving the toughness of the material. Hydraulic shearing removes the head and tail defect sources, and secondary heating ensures the quality of the billet. Ultimately, this improves the dimensional accuracy and pass rate of the plates, ensures stable production, and improves the processing performance of the finished products.

[0058] The above are exemplary embodiments disclosed in this invention. The order of the disclosed embodiments is merely for descriptive purposes and does not represent the superiority or inferiority of the embodiments. However, it should be noted that the discussion of any of the above embodiments is merely exemplary and is not intended to imply that the scope of the disclosed embodiments of this invention (including the claims) is limited to these examples. Various changes and modifications can be made without departing from the scope defined by the claims. The functions, steps, and / or actions of the methods according to the disclosed embodiments described herein do not need to be performed in any particular order. Furthermore, although the elements disclosed in the embodiments of this invention may be described or claimed individually, they may be understood as multiple unless explicitly limited to a singular.

[0059] Those skilled in the art should understand that the discussion of any of the above embodiments is merely exemplary and is not intended to imply that the scope of the invention (including the claims) is limited to these examples. Within the framework of the invention, technical features of the above embodiments or different embodiments can be combined, and many other variations of the different aspects of the invention as described above exist, which are not provided in the details for the sake of brevity. Therefore, any omissions, modifications, equivalent substitutions, improvements, etc., made within the spirit and principles of the invention should be included within the protection scope of the invention.

Claims

1. A rolling method of a high-carbon high-chromium alloy steel wide-thick plate material, characterized by, The method comprises the following steps: S1, pre-treating the blank and then heating it in a ring furnace; S2, repeatedly rolling the heated blank in multiple passes by a rough rolling mill; S3, heating the rolled blank in a step furnace and then rolling it by a continuous rolling mill; S4, post-treating the rolled wide and thick plate to obtain a qualified wide and thick plate blank.

2. The rolling method of a high-carbon high-chromium alloy steel wide-thick plate according to claim 1, characterized by, In step S1, the pre-treatment of the blank comprises setting the charging temperature of the ring furnace according to the temperature of the blank after temperature measurement.

3. The rolling method of a high-carbon high-chromium alloy steel wide-thick plate according to claim 1, characterized by, In step S1, heating section one, heating section two, heating section three and multiple soaking sections are sequentially performed, the temperature of the heating section one is controlled at 700-850℃, the temperature of the heating section two is controlled at 1000-1150℃, the temperature of the heating section three is controlled at 1220-1250℃, and the temperature of the multiple soaking sections is controlled at 1210-1235℃, and the heating speed of the ring furnace is ≤80℃ / h.

4. The rolling method of a high-carbon high-chromium alloy steel wide-thick plate according to claim 1, characterized by, The step period of the ring furnace is calculated as T=S*t / n; S is the diameter or maximum thickness of the blank, in mm; t is the thickness time coefficient, taking 5-20; and n is the total number of teeth of the step furnace.

5. The rolling method of a high-carbon high-chromium alloy steel wide-thick plate according to claim 1, characterized by, In step S2, the multiple-pass rolling includes at least 2 passes with a relative deformation rate ≥20% in the intermediate passes.

6. The rolling method of a high-carbon high-chromium alloy steel wide-thick plate according to claim 1, characterized by, In step S2, the rolling speed of the rough rolling mill is ≥2m / s, the rolling roll cooling water flow is ≤50L / min during the rolling process, and the finish rolling temperature is ≥1040℃; in step S3, the continuous rolling mill comprises 4-8 racks, and the rolling speed is 0.5-0.6m / s.

7. The rolling method of a high-carbon high-chromium alloy steel wide-thick plate according to claim 1, characterized by, In step S3, heating section one, heating section two and soaking section are sequentially performed, the heating speed of the step furnace is ≤80℃ / h, the temperature of the heating section one is controlled at 1100±10℃, the temperature of the heating section two is controlled at 1210±10℃, and the temperature of the soaking section is controlled at 1180±10℃, and the step period is 5-20min.

8. The rolling method of a high-carbon high-chromium alloy steel wide-thick plate according to claim 1, characterized by, In step S4, the rolled wide and thick plate is stacked and slowly cooled, the temperature is reduced to 650-700℃, then it is charged into the furnace, the furnace temperature is controlled at 680±10℃, and after 3-6h of heat preservation, it is slowly cooled at a cooling speed ≤30℃ / h with the furnace until the temperature is 200-250℃, then it is discharged from the furnace, and a qualified wide and thick plate blank is obtained.

9. A high-carbon high-chromium alloy steel wide-thick plate material, characterized by, The wide and thick plate of high-carbon high-chromium alloy steel is prepared by the rolling method according to any one of claims 1-8.

10. The high-carbon, high-chromium alloy steel plate according to claim 9, characterized in that, In the wide and thick plate of high-carbon high-chromium alloy steel, C≥0.85wt%, and Cr≥12wt%; the thickness of the wide and thick plate of high-carbon high-chromium alloy steel is ≥40mm, and the width is ≥400mm.

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