12cr2mo1v steel cylinder segment forge piece and preparation method thereof

Abstract

This invention provides a 12Cr2Mo1V steel cylindrical section forging and its preparation method, relating to the field of forging technology. By increasing the forging ratio in the final forging pass, this invention helps to refine the grains, thereby improving the internal structure of the forging, eliminating structural defects, and enhancing the strength and impact toughness of the forging. Through quenching and tempering the forging, and controlling the quenching temperature at a relatively low level, this invention retains some undissolved VC particles in the matrix, which can pin grain boundaries and inhibit austenite grain growth, thus improving the impact toughness of the cylindrical section forging. Furthermore, controlling the quenching temperature at a low level reduces the solid solution V content, lowering the risk of complex carbide precipitation along grain boundaries during subsequent cooling, which is beneficial for improving the strength of the cylindrical section forging. In summary, the 12Cr2Mo1V cylindrical section forging prepared using the method of this invention exhibits high strength and high impact toughness.

Description

Technical Field

[0001] This invention relates to the field of forging technology, and more specifically, to a 12Cr2Mo1V steel cylinder section forging and its preparation method. Background Technology

[0002] 12Cr2Mo1V steel is a typical low-alloy heat-resistant steel, widely used in the manufacture of cylindrical forgings for hydrogenation reactors. The main strengthening mechanism of 12Cr2Mo1V steel is the dispersion precipitation of fine carbides formed by the synergistic effect of Cr-Mo-V, which endows the material with good high-temperature strength and resistance to hydrogen corrosion. In recent years, in order to further improve the high-temperature mechanical properties of 12Cr2Mo1V steel cylindrical forgings, the V content in 12Cr2Mo1V steel has been increased to above 0.32%. However, when the V content in 12Cr2Mo1V steel is above 0.32%, the following problems are likely to occur: (1) High-temperature quenching causes excessive dissolution of V into austenite, and the composite carbides formed after cooling become crack sources, affecting the strength of the forging. (2) The tendency of austenite grain growth is intensified, leading to a decrease in the impact toughness of the forging. Therefore, for 12Cr2Mo1V steel cylindrical forgings with a V content above 0.32%, how to ensure that they have high strength and high impact toughness is a key issue. Summary of the Invention

[0003] The problem solved by this invention is: how to ensure that 12Cr2Mo1V steel cylinder section forgings with a V content of more than 0.32% have high strength and high impact toughness.

[0004] To address the above problems, this invention provides a method for preparing 12Cr2Mo1V steel cylinder section forgings, comprising: Step S1: Remove the waste material from the sprue and riser ends of the steel ingot to obtain a billet; the steel ingot is made of 12Cr2Mo1V steel; by weight percentage, the chemical composition of the 12Cr2Mo1V steel includes: C: 0.12% to 0.13%; Si: 0 to 0.10%; Mn: 0.40% to 0.45%; P: 0 to 0.005%; S: 0 to 0.003%; Cr: 2.53% to 2.55%; Mo: 1.12% to 1.15%; V: 0.32% to 0.35%; Ni: 0.15% to 0.20%; Cu: 0 to 0.06%; Nb: 0.045%-0.50%; the balance is Fe and unavoidable impurities; Step S2, First forging: The billet is heated to the first forging temperature, held at the temperature, and then upsetting and punching are performed to obtain the first intermediate forging; Step S3, Second forging: The first intermediate forging is heated to the first forging temperature, held at the temperature, and then the mandrel is drawn to obtain the second intermediate forging; Step S4, Third Forging: The second intermediate forging is heated to the first forging temperature, held for heat treatment, and then leveled and expanded by the lever to obtain the third intermediate forging; Step S5, Fourth Forging: The third intermediate forging is heated to the second forging temperature, held at the temperature, and then produced as a finished product through a cylindrical rolling mill to obtain the fourth intermediate forging; the forging ratio of the fourth forging is 1.45 to 1.47; Step S6: Perform post-forging heat treatment on the fourth intermediate forging to obtain the cylindrical section forging; In step S6, the post-forging heat treatment of the fourth intermediate forging to obtain the cylindrical section forging includes: Step S61, Quenching treatment: The fourth intermediate forging is heated to 650°C to 700°C at a first heating rate and held for 6 to 8 hours. Then, it is heated to the quenching temperature at a second heating rate and held for 6 to 8 hours. Finally, it is water-cooled to 140°C to 160°C to obtain the fifth intermediate forging. The quenching temperature is 900°C to 940°C. Step S62, Tempering treatment: The fifth intermediate forging is heated to 650°C to 700°C at the third heating rate, held at that temperature for 6 to 8 hours, and then air-cooled to room temperature to obtain the cylindrical section forging.

[0005] Optionally, in step S2, the forging ratio of the first fire forging is 1.49 to 1.51.

[0006] Optionally, in step S3, the forging ratio of the second fire forging is 1.59 to 1.61.

[0007] Optionally, in step S4, the forging ratio of the third fire forging is 1.59 to 1.61.

[0008] Optionally, in step S61, the first heating rate is 90℃ / h to 100℃ / h.

[0009] Optionally, in step S61, the second heating rate is 90℃ / h to 100℃ / h.

[0010] Optionally, in step S62, the third heating rate is 30℃ / h to 40℃ / h.

[0011] Optionally, the first forging temperature is 1245°C to 1255°C.

[0012] Optionally, the second forging temperature is 1195°C to 1205°C.

[0013] The present invention also provides a 12Cr2Mo1V steel cylinder section forging, which is made by the preparation method of the 12Cr2Mo1V steel cylinder section forging described above.

[0014] Compared with related technologies, for forging 12Cr2Mo1V steel cylindrical section forgings with a V content of 0.32% or higher, this invention, by increasing the forging ratio of the final heat treatment (finished product heat treatment) (1.45 to 1.47), helps to fully refine the grains, thereby improving the internal structure of the forging, eliminating structural defects, and improving the strength and impact toughness of the forging. This invention, through quenching and tempering of the forging, and controlling the quenching temperature at a relatively low level (900℃ to 940℃), retains some undissolved VC particles in the matrix, which can pin grain boundaries and inhibit austenite grain growth, thus improving the impact toughness of the cylindrical section forging. Furthermore, controlling the quenching temperature at a low level reduces the dissolved V content, lowering the risk of complex carbide precipitation along grain boundaries during subsequent cooling, which is beneficial for improving the strength of the cylindrical section forging. In summary, the 12Cr2Mo1V cylindrical section forgings prepared using the method of this invention have high strength and high impact toughness. Attached Figure Description

[0015] Figure 1 This is a schematic diagram of the sample after upsetting in Example 1 of the present invention; Figure 2 This is a schematic diagram of the first intermediate forging in Embodiment 1 of the present invention; Figure 3 This is a schematic diagram of the second intermediate forging in Embodiment 1 of the present invention; Figure 4 This is a schematic diagram of the third intermediate forging in Embodiment 1 of the present invention; Figure 5 This is a schematic diagram of the fourth intermediate forging in Embodiment 1 of the present invention; Figure 6 The image shows the metallographic structure of the outer wall region of the cylindrical forging obtained in Embodiment 1 of the present invention. Figure 7 The image shows the metallographic structure of the inner wall region of the cylindrical forging obtained in Embodiment 1 of the present invention. Figure 8 This is a metallographic image of the middle part of the side wall of the cylindrical forging obtained in Embodiment 1 of the present invention. Detailed Implementation To make the above-mentioned objects, features, and advantages of the present invention more apparent and understandable, specific embodiments of the present invention will be described in detail below with reference to the accompanying drawings. Although some embodiments of the present invention are shown in the drawings, it should be understood that the present invention can be implemented in various forms and should not be construed as limited to the embodiments set forth herein. Rather, these embodiments are provided to provide a more thorough and complete understanding of the present invention. It should be understood that the accompanying drawings and embodiments of the present invention are for illustrative purposes only and are not intended to limit the scope of protection of the present invention.

[0016] Unless otherwise defined, all technical and scientific terms used in this invention have the same meaning as commonly understood by one of ordinary skill in the art to which this invention pertains. The terminology used in this specification is for the purpose of describing particular embodiments only and is not intended to be limiting of the invention.

[0017] The term "comprising" and its variations as used herein are open-ended, meaning "including but not limited to"; the term "based on" means "at least partially based on"; the term "one embodiment" means "at least one embodiment"; the term "another embodiment" means "at least one additional embodiment"; the term "some embodiments" means "at least some embodiments"; and the term "optionally" means "optional embodiments". Definitions of other terms will be given in the following description. It should be noted that the concepts of "first," "second," etc., mentioned in this invention are used to distinguish different objects, not to describe a specific order or hierarchy. Furthermore, the terms "first" and "second" are used for descriptive purposes only and should not be construed as indicating or implying relative importance or implicitly specifying the number of indicated technical features. Thus, a feature defined with "first" or "second" may explicitly or implicitly include one or more of that feature. In the description of this invention, unless otherwise stated, "a plurality of" means two or more.

[0018] This invention provides a method for preparing a 12Cr2Mo1V steel cylinder section forging, comprising: Step S1: Remove the waste material from the sprue and riser ends of the steel ingot to obtain a billet; the steel ingot is made of 12Cr2Mo1V steel; by weight percentage, the chemical composition of the 12Cr2Mo1V steel includes: C: 0.12% to 0.13%; Si: 0 to 0.10%; Mn: 0.40% to 0.45%; P: 0 to 0.005%; S: 0 to 0.003%; Cr: 2.53% to 2.55%; Mo: 1.12% to 1.15%; V: 0.32% to 0.35%; Ni: 0.15% to 0.20%; Cu: 0 to 0.06%; Nb: 0.045%-0.50%; the balance is Fe and unavoidable impurities; Step S2, First forging: The billet is heated to the first forging temperature, held at the temperature, and then upsetting and punching are performed to obtain the first intermediate forging; Step S3, Second forging: The first intermediate forging is heated to the first forging temperature, held at the temperature, and then the mandrel is drawn to obtain the second intermediate forging; Step S4, Third Forging: The second intermediate forging is heated to the first forging temperature, held for heat treatment, and then leveled and expanded by the lever to obtain the third intermediate forging; Step S5, Fourth Forging: The third intermediate forging is heated to the second forging temperature, held at the temperature, and then produced as a finished product through a cylindrical rolling mill to obtain the fourth intermediate forging; the forging ratio of the fourth forging is 1.45 to 1.47; Step S6: Perform post-forging heat treatment on the fourth intermediate forging to obtain the cylindrical section forging; In step S6, the post-forging heat treatment of the fourth intermediate forging to obtain the cylindrical section forging includes: Step S61, Quenching treatment: The fourth intermediate forging is heated to 650°C to 700°C at a first heating rate and held for 6 to 8 hours. Then, it is heated to the quenching temperature at a second heating rate and held for 6 to 8 hours. Finally, it is water-cooled to 140°C to 160°C to obtain the fifth intermediate forging. The quenching temperature is 900°C to 940°C. Step S62, Tempering treatment: The fifth intermediate forging is heated to 650°C to 700°C at the third heating rate, held at that temperature for 6 to 8 hours, and then air-cooled to room temperature to obtain the cylindrical section forging.

[0019] For forging 12Cr2Mo1V steel cylindrical section forgings with a V content of 0.32% or higher, this embodiment of the invention, by increasing the forging ratio of the final heat treatment (finished product heat treatment) (1.45 to 1.47), helps to fully refine the grains, thereby improving the internal structure of the forging, eliminating structural defects, and improving the strength and impact toughness of the forging. This embodiment of the invention, by quenching and tempering the forging, and controlling the quenching temperature relatively low (900℃ to 940℃), allows some undissolved VC particles to remain in the matrix, which can pin grain boundaries and inhibit austenite grain growth, thus improving the impact toughness of the cylindrical section forging. Furthermore, controlling the quenching temperature relatively low reduces the dissolved V content, lowering the risk of complex carbide precipitation along grain boundaries during subsequent cooling, which is beneficial for improving the strength of the cylindrical section forging. In summary, the 12Cr2Mo1V cylindrical section forgings obtained using the method of this embodiment of the invention have high strength and high impact toughness.

[0020] The selection criteria for each component in the 12Cr2Mo1V steel in this embodiment are as follows: Carbon (C) is a primary strengthening element that directly affects the strength, plasticity, and toughness of forgings. When the C content is below 0.8%, the strength and hardness of the forgings increase with increasing C content. Therefore, in this embodiment of the invention, the C content is controlled to be between 0.12% and 0.13%.

[0021] Mn is a weak carbide-forming element that can improve the strength of steel without reducing its plasticity within a certain content range. Mn can form an infinite solid solution with austenite, improving the hardenability of the steel. The main use of Mn in this material is to ensure the strength of forgings. Therefore, in this embodiment of the invention, the Mn content is controlled to be between 0.40% and 0.45%.

[0022] Cr (Cr) is a carbide-forming element with a secondary hardening effect, significantly improving the hardness and wear resistance of steel. In quenched and tempered steel, the main role of Cr is to improve the hardenability of forgings, enabling them to achieve excellent comprehensive mechanical properties after quenching and tempering. Therefore, in this embodiment of the invention, the Cr content is controlled at 2.53% to 2.55%.

[0023] The main role of Mo in this material is to improve its hardenability. As the main forgings of hydrogenation reactors become increasingly larger and thicker, the tempering process becomes more challenging. Mn can significantly improve the hardenability of the forgings in this material. Therefore, in this embodiment of the invention, the Mo content is controlled at 1.12% to 1.15%.

[0024] V forms stable, refractory carbides in materials, allowing steel to maintain a fine-grained structure even at high temperatures, thus significantly reducing the steel's overheat sensitivity. Therefore, in the embodiments of this invention, the V content is controlled to be between 0.32% and 0.35%.

[0025] Ni is a non-carbide-forming element with a lattice constant similar to austenite, allowing it to form a continuous solid solution and improve the stability of austenite. Ni has a beneficial effect on plasticity and toughness, significantly improving the toughness of steel while lowering its ductile-brittle transition temperature, while maintaining a high level of strength. For large forgings requiring comprehensive mechanical properties, Ni-containing steel is generally selected. When steel contains elements such as Cr and Mo, the effect of Ni combined with Cr and Mo in improving hardenability is significantly greater than the effect of any single element. Therefore, the role of Ni in materials is to improve the plasticity, toughness, and hardenability of forgings. In the embodiments of this invention, the Ni content is controlled at 0.15% to 0.20%.

[0026] In 12Cr2Mo1V steel, nitrogen (Nb) primarily functions by forming fine, dispersed carbide precipitates, thereby refining the grain size, enhancing precipitation strengthening, and improving resistance to hydrogen embrittlement. It is one of the key microalloying elements for improving the overall mechanical properties of this type of steel. If the Nb content is too low, the number of precipitates is insufficient, making it difficult to form effective hydrogen traps, thus weakening the grain refinement and precipitation strengthening effects. If the Nb content is too high, it may lead to NbC coarsening or segregation, which in turn reduces toughness. Therefore, in the embodiments of this invention, the Nb content is controlled at 0.45% to 0.50%.

[0027] In some embodiments of the present invention, in step S2, the forging ratio of the first hot forging is 1.49 to 1.51. In this embodiment, by increasing the forging ratio of the first hot forging (1.49 to 1.51), the internal voids of the forging can be better compressed during the upsetting process, and the internal grain structure of the forging can be broken down into finer pieces, thereby helping to improve the internal structure of the forging, eliminate structural defects, and improve the strength and impact toughness of the forging. In some embodiments of the present invention, in step S3, the forging ratio of the second fire forging is 1.59 to 1.61; in step S4, the forging ratio of the third fire forging is 1.59 to 1.61.

[0028] In some embodiments of the present invention, in step S61, the first heating rate is 90℃ / h to 100℃ / h; the second heating rate is 90℃ / h to 100℃ / h. In this embodiment, by controlling both the first and second heating rates to 90℃ / h to 100℃ / h, crack-free and highly uniform austenitization of the forging under high alloy and large cross-section conditions is achieved, ensuring microstructure properties and service safety.

[0029] In some embodiments of the present invention, in step S62, the third heating rate is 30°C / h to 40°C / h. In this embodiment, by using a third heating rate of 30°C / h to 40°C / h, it is ensured that the forging gradually releases residual forging stress within a temperature range where plasticity is good.

[0030] In some embodiments of the present invention, the first forging temperature is 1245°C to 1255°C, and the second forging temperature is 1195°C to 1205°C. In this embodiment, the heating temperature is 1245°C to 1255°C during the first to third forging processes, while the heating temperature is appropriately reduced (1195°C to 1205°C) during the final forging process. This can effectively prevent excessive grain growth in the forging and is beneficial to further improving the impact toughness of the forging.

[0031] This invention also provides a 12Cr2Mo1V steel cylinder section forging, which is manufactured using the method described above for preparing 12Cr2Mo1V steel cylinder section forgings.

[0032] The present invention will be further described below with reference to specific embodiments.

[0033] Example 1 A1. Remove the waste material from the sprue and riser ends of the steel ingot to obtain the billet; the steel ingot is made of 12Cr2Mo1V steel; the chemical composition of the 12Cr2Mo1V steel includes: C: 0.125%; Si: 0.05%; Mn: 0.42%; P: 0.002%; S: 0.002%; Cr: 2.54%; Mo: 1.13%; V: 0.33%; Ni: 0.18%; Cu: 0.02%; Nb: 0.047%; the balance is Fe and unavoidable impurities.

[0034] A2. First forging: Heat the billet to 1250℃, hold for 40 hours, and upset to a height of 2250mm and a diameter of 3760mm. Figure 1 As shown, punching is then performed to obtain the first intermediate forging, as shown. Figure 2 As shown; the inner diameter of the center hole of the first intermediate forging is 1400mm, and the forging ratio of the first fire forging is 1.50.

[0035] A3. Second forging: The first intermediate forging is heated to 1250℃ and held for 8 hours, then the mandrel is drawn to obtain the second intermediate forging, as shown below. Figure 3 As shown; the inner diameter of the second intermediate forging is 1380mm, the outer diameter is 3160mm, the height is 3610mm, and the forging ratio of the second fire forging is 1.60. A4. Third Forging: The second intermediate forging is heated to 1250℃, held for 6 hours, leveled to a height of 3410mm, and then the hole is enlarged by a lever to obtain the third intermediate forging, as shown. Figure 4 As shown; the inner diameter of the fourth intermediate forging is 3200mm and the outer diameter is 4310mm, and the forging ratio of the third fire forging is 1.60.

[0036] A5. Fourth Forging: The third intermediate forging is heated to 1200℃ and held for 5 hours. The finished product is then obtained through a cylindrical rolling mill, yielding the fourth intermediate forging. Figure 5 As shown; the inner diameter of the fifth intermediate forging is 4760mm, the outer diameter is 5520mm, and the height is 3410mm; the forging ratio of the fourth fire forging is 1.46.

[0037] A6. Quenching treatment: The fourth intermediate forging is heated to 675°C at a first heating rate and held for 7 hours, then heated to the quenching temperature at a second heating rate and held for 7 hours, and then water-cooled to 150°C to obtain the fifth intermediate forging; wherein, the quenching temperature is 920°C, the first heating rate is 95°C / h, and the second heating rate is 95°C / h. A7. Tempering treatment: The fifth intermediate forging is heated to 675°C at a third heating rate, held for 7 hours, and then air-cooled to room temperature to obtain the cylindrical section forging; the third heating rate is 35°C / h.

[0038] Example 2 The difference from Example 1 is that in step A6, the quenching temperature is 900°C.

[0039] Example 3 The difference from Example 1 is that in step A6, the quenching temperature is 940°C.

[0040] Comparative Example 1 The difference from Example 1 is that in step A6, the quenching temperature is 960°C.

[0041] Comparative Example 2 The difference from Example 1 is that in step A6, the quenching temperature is 970°C.

[0042] Comparative Example 3 The difference from Example 1 is that in step A5, the fourth fire forging: the third intermediate forging is heated to 1200°C, held for 5 hours, and then produced as a finished product through a cylindrical rolling mill to obtain the fourth intermediate forging; the forging ratio of the fourth fire forging is 1.38.

[0043] Effect Example The tensile strength and impact toughness of the cylindrical forgings prepared in Examples 1 to 3 and Comparative Examples 1 to 3 were tested. The results are shown in Table 1. Compared with Comparative Examples 1 to 3, the cylindrical forgings prepared in Examples 1 to 3 not only have higher strength, but also higher impact toughness.

[0044] Table 1

[0045] It should be noted that AKv in Table 1 is used to characterize impact toughness, representing the energy absorbed by the material when subjected to impact load. The microstructure of the outer wall, inner wall, and middle part of the side wall of the cylindrical forging obtained in Example 1 was examined, and the results are shown in the figure. Figures 6 to 8 ,from Figures 6 to 8 It can be seen that the microstructure of the cylindrical section forgings prepared in Example 1 is entirely tempered martensite in the outer wall region, with uniformly dispersed carbides and a grain size of 6.5. Similarly, the microstructure of the cylindrical section forgings prepared in Example 1 is entirely tempered martensite in the inner wall region, with uniformly dispersed carbides and a grain size of 6.5. Furthermore, the microstructure of the cylindrical section forgings prepared in Example 1 in the middle of the side wall region is entirely tempered martensite, with uniformly dispersed carbides and a grain size of 6.5. Therefore, the cylindrical section forgings prepared in Example 1 also exhibit good microstructure uniformity.

[0046] While the present invention has been disclosed above, its scope of protection is not limited thereto. Those skilled in the art can make various changes and modifications without departing from the spirit and scope of the present invention, and all such changes and modifications will fall within the scope of protection of the present invention.

Claims

1. A method for preparing a 12Cr2Mo1V steel cylindrical section forging, characterized in that, include: Step S1: Remove the waste material from the sprue end and riser end of the steel ingot to obtain the billet; The steel ingot is made of 12Cr2Mo1V steel; The chemical composition of the 12Cr2Mo1V steel, by weight percentage, comprises: C: 0.12% to 0.13%; Si: 0 to 0.10%; Mn: 0.40% to 0.45%; P: 0 to 0.005%; S: 0 to 0.003%; Cr: 2.53% to 2.55%; Mo: 1.12% to 1.15%; V: 0.32% to 0.35%; Ni: 0.15% to 0.20%; Cu: 0 to 0.06%; Nb: 0.045%-0.50%; the balance being Fe and unavoidable impurities. Step S2, First forging: The billet is heated to the first forging temperature, held at the temperature, and then upsetting and punching are performed to obtain the first intermediate forging; Step S3, Second forging: The first intermediate forging is heated to the first forging temperature, held at the temperature, and then the mandrel is drawn to obtain the second intermediate forging; Step S4, Third Forging: The second intermediate forging is heated to the first forging temperature, held for heat treatment, and then leveled and expanded by the lever to obtain the third intermediate forging; Step S5, Fourth Forging: The third intermediate forging is heated to the second forging temperature, held at the temperature, and then produced as a finished product through a cylindrical rolling mill to obtain the fourth intermediate forging; the forging ratio of the fourth forging is 1.45 to 1.47; Step S6: Perform post-forging heat treatment on the fourth intermediate forging to obtain the cylindrical section forging; In step S6, the post-forging heat treatment of the fourth intermediate forging to obtain the cylindrical section forging includes: Step S61, Quenching treatment: The fourth intermediate forging is heated to 650°C to 700°C at a first heating rate and held for 6 to 8 hours. Then, it is heated to the quenching temperature at a second heating rate and held for 6 to 8 hours. Finally, it is water-cooled to 140°C to 160°C to obtain the fifth intermediate forging. The quenching temperature is 900°C to 940°C. Step S62, Tempering treatment: The fifth intermediate forging is heated to 650°C to 700°C at the third heating rate, held at that temperature for 6 to 8 hours, and then air-cooled to room temperature to obtain the cylindrical section forging.

2. The method for preparing the 12Cr2Mo1V steel cylinder section forging according to claim 1, characterized in that, In step S2, the forging ratio of the first fire forging is 1.49 to 1.

51.

3. The method for preparing the 12Cr2Mo1V steel cylinder section forging according to claim 1, characterized in that, In step S3, the forging ratio of the second fire forging is 1.59 to 1.

61.

4. The method for preparing the 12Cr2Mo1V steel cylinder section forging according to claim 1, characterized in that, In step S4, the forging ratio of the third fire forging is 1.59 to 1.

61.

5. The method for preparing the 12Cr2Mo1V steel cylinder section forging according to claim 1, characterized in that, In step S61, the first heating rate is 90℃ / h to 100℃ / h.

6. The method for preparing the 12Cr2Mo1V steel cylinder section forging according to claim 1, characterized in that, In step S61, the second heating rate is 90℃ / h to 100℃ / h.

7. The method for preparing the 12Cr2Mo1V steel cylinder section forging according to claim 1, characterized in that, In step S62, the third heating rate is 30℃ / h to 40℃ / h.

8. The method for preparing the 12Cr2Mo1V steel cylinder section forging according to claim 1, characterized in that, The first forging temperature is 1245°C to 1255°C.

9. The method for preparing the 12Cr2Mo1V steel cylinder section forging according to claim 1, characterized in that, The second forging temperature is 1195°C to 1205°C.

10. A 12Cr2Mo1V steel cylinder section forging, characterized in that, It is manufactured using the preparation method of 12Cr2Mo1V steel cylinder section forging as described in any one of claims 1 to 9.

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