A cylinder segment forging with high impact toughness and a method for manufacturing the same

Abstract

The application provides a cylinder segment forge piece with high impact toughness and a preparation method thereof, and relates to the field of forging technology.The application can make the internal gap of the forge piece be better compressed during the upsetting process by improving the forging ratio of the first fire forging, and can make the internal grain structure of the forge piece be broken more finely, thereby helping to improve the internal structure of the forge piece, eliminate the structural defects, and be beneficial to improving the strength and impact toughness of the forge piece.In addition, the application appropriately reduces the heating temperature during the last fire forging process, which can effectively prevent the grains in the forge piece from growing excessively, and is beneficial to further improving the impact toughness of the forge piece.Finally, the application controls the quenching temperature to be 950 DEG C to 970 DEG C, which is beneficial to further ensuring that the cylinder segment forge piece has high strength and high impact toughness.In summary, the 12Cr2Mo1V cylinder segment forge piece prepared by the method of the application has high strength and high impact toughness.

Description

TECHNICAL FIELD

[0001] The present application relates to the field of forging technology, in particular to a cylinder segment forging with high impact toughness and a preparation method thereof. BACKGROUND

[0002] The cylinder segment is a core component of a hydrogenation reactor of a petroleum refining device, and its weight can account for 95% of the total weight of the hydrogenation reactor, and its main function is to support and protect the reactor. Since the hydrogenation reactor operates in a harsh condition, the core component, i.e., the cylinder segment, needs to bear a large pressure and impact during use. At present, the material of the cylinder segment forging is mainly 12Cr2Mo1V steel. In order to meet the increasing use requirements, not only is it required that the 12Cr2Mo1V steel cylinder segment forging has high strength, but also it is required that the 12Cr2Mo1V steel cylinder segment forging has high impact toughness. However, the existing 12Cr2Mo1V steel cylinder segment forging is often difficult to have both high strength and high impact toughness. SUMMARY

[0003] The problem solved by the present application is how to obtain a 12Cr2Mo1V steel cylinder segment forging with high strength and high impact toughness.

[0004] To solve the above problems, the present application provides a preparation method of a cylinder segment forging with high impact toughness, comprising the following steps:

[0005] Step S1, cutting off the scrap of the water end and the riser end of a steel ingot to obtain a blank; the material of the steel ingot is 12Cr2Mo1V steel;

[0006] Step S2, first fire forging: heating the blank to 1240-1260 DEG C, performing heat preservation treatment, then performing upsetting and punching to obtain a first intermediate forging; the forging ratio of the first fire forging is 1.50-1.54;

[0007] Step S3, second fire forging: heating the first intermediate forging to 1240-1260 DEG C, performing heat preservation treatment, and performing core rod lengthening to obtain a second intermediate forging;

[0008] Step S4, third fire forging: heating the second intermediate forging to 1240-1260 DEG C, performing heat preservation treatment, and performing flattening to obtain a third intermediate forging;

[0009] Step S5, fourth fire forging: heating the third intermediate forging to 1240-1260 DEG C, performing heat preservation treatment, and expanding the hole through a mandrel to obtain a fourth intermediate forging;

[0010] Step S6, fifth fire forging: heating the third intermediate forging to 1190-1210 DEG C, performing heat preservation treatment, and expanding the hole through a rolling mill to obtain a fifth intermediate forging;

[0011] Step S7, the fifth intermediate forgings are subjected to post-forging heat treatment to obtain cylinder segment forgings;

[0012] In the step S7, the fifth intermediate forgings are subjected to post-forging heat treatment to obtain cylinder segment forgings, which includes:

[0013] Step S71, quenching treatment: the fifth intermediate forgings are heated to 650-700 DEG C at a first heating rate, kept for 6-10 hours, then heated to quenching temperature at a second heating rate, kept for 8-10 hours, then water-cooled to 90-100 DEG C to obtain sixth intermediate forgings; wherein the quenching temperature is 950-970 DEG C;

[0014] Step S72, tempering treatment: the sixth intermediate forgings are heated to 300-400 DEG C, kept for 4-6 hours, then heated to 650-700 DEG C at a third heating rate, kept for 8-10 hours, then air-cooled to room temperature to obtain the cylinder segment forgings.

[0015] Optionally, in the step S3, the forging ratio of the second fire forging is 1.50-1.90.

[0016] Optionally, in the step S4, the forging ratio of the third fire forging is 1.04-1.06.

[0017] Optionally, in the step S5, the forging ratio of the fourth fire forging is 1.60-1.70.

[0018] Optionally, in the step S6, the forging ratio of the fifth fire forging is 1.36-1.40.

[0019] Optionally, in the step S71, the first heating rate is 80-100 DEG C / h.

[0020] Optionally, in the step S71, the second heating rate is 80-100 DEG C / h.

[0021] Optionally, in the step S72, the third heating rate is 50-70 DEG C / h.

[0022] Optionally, the chemical composition of the 12Cr2Mo1V steel includes, in percentage by weight: C: 0.14% to 0.15%; Si: 0 to 0.09%; Mn: 0.50% to 0.60%; P: 0 to 0.005%; S: 0 to 0.003%; Cr: 2.40% to 2.50%; Mo: 1.00% to 1.10%; V: 0.29% to 0.31%; Ni: 0.15% to 0.20%; Cu: 0 to 0.06%; Nb: 0.025%-0.040%; the balance being Fe and inevitable impurities; and carbon equivalent C E is greater than 0.98%.

[0023] The application further provides a cylinder segment forge piece with high impact toughness, which is prepared by the preparation method of the cylinder segment forge piece with high impact toughness.

[0024] Compared with the related art, by increasing the forging ratio (1.50 to 1.54) of the first fire forging, the application can make the internal gap of the forge piece be better compressed during the upsetting process, and make the internal grain structure of the forge piece be broken more finely, thereby helping to improve the internal structure of the forge piece, eliminate the structural defects, and be beneficial to improving the strength and impact toughness of the forge piece. In addition, by appropriately reducing the heating temperature (1190℃ to 1210℃) in the last fire forging process after the heating temperature is 1240℃ to 1260℃ in the first fire forging to the fourth fire forging process, the application can effectively prevent the grains in the forge piece from growing excessively, and be beneficial to further improving the impact toughness of the forge piece. Finally, by quenching and tempering the forge piece, and controlling the quenching temperature to be 950℃ to 970℃, the application is beneficial to further ensuring that the cylinder segment forge piece has high strength and high impact toughness. In summary, the 12Cr2Mo1V cylinder segment forge piece prepared by the application has high strength and high impact toughness. BRIEF DESCRIPTION OF DRAWINGS

[0025] Figure 1 FIG. 1 is a schematic view of a sample after upsetting in Example 1 of the application;

[0026] Figure 2 FIG. 2 is a schematic view of a first intermediate forge piece in Example 1 of the application;

[0027] Figure 3 FIG. 3 is a schematic view of a second intermediate forge piece in Example 1 of the application;

[0028] Figure 4 FIG. 4 is a schematic view of a third intermediate forge piece in Example 1 of the application;

[0029] Figure 5 FIG. 5 is a schematic view of a fourth intermediate forge piece in Example 1 of the application;

[0030] Figure 6A schematic view of the fifth intermediate forging in Example 1 of the present application. DETAILED DESCRIPTION

[0031] In order to make the above objectives, characteristics and advantages of the present application more obvious and easy to understand, the specific embodiments of the present application are described in detail below with reference to the drawings. Although some embodiments of the present application are shown in the drawings, it should be understood that the present application can be implemented in various forms, and should not be interpreted as being limited to the embodiments described herein, on the contrary, these embodiments are provided for a more thorough and complete understanding of the present application. It should be understood that the drawings and embodiments of the present application are only for exemplary purposes, and are not intended to limit the scope of protection of the present application.

[0032] Unless otherwise defined, all technical and scientific terms used herein have the same meaning as commonly understood by one of ordinary skill in the art to which this application belongs; the terminology used in the description of the application herein is for the purpose of describing particular embodiments only and is not intended to be limiting of the application;

[0033] The term "comprising" and variations thereof as used herein are open-ended, that is "including, but not limited to"; the term "based on" is "based, at least in part, 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"; the term "optionally" means "optional embodiments". Related definitions are given throughout the detailed description. It is to be noted that the terms "first", "second", and the like, as used herein do not necessarily have an ordinal meaning but are used for the purpose of nomenclature only. Also, the terms "first", "second" are used for descriptive purposes only and are not to be construed as indicating or implying relative importance or an ordered sequence. Thus, a feature defined with "first", "second" can implicitly or explicitly include one or more of the features. In the description of the application, the meaning of "a plurality" is two or more, unless otherwise specified.

[0034] The present embodiment provides a preparation method of a cylinder segment forging with high impact toughness, comprising:

[0035] Step S1, cutting off the scrap of the ingot end and the riser end of the steel ingot to obtain a blank; the material of the steel ingot is 12Cr2Mo1V steel;

[0036] Step S2, first fire forging: heating the blank to 1240-1260℃, and then performing upsetting and piercing to obtain a first intermediate forging; the forging ratio of the first fire forging is 1.50-1.54;

[0037] Step S3, second fire forging: the first intermediate forging is heated to 1240-1260 DEG C, and after holding treatment, core rod lengthening is performed to obtain a second intermediate forging;

[0038] Step S4, third fire forging: the second intermediate forging is heated to 1240-1260 DEG C, and after holding treatment, flattening is performed to obtain a third intermediate forging;

[0039] Step S5, fourth fire forging: the third intermediate forging is heated to 1240-1260 DEG C, and after holding treatment, hole expansion is performed by a mandrel to obtain a fourth intermediate forging;

[0040] Step S6, fifth fire forging: the third intermediate forging is heated to 1190-1210 DEG C, and after holding treatment, hole expansion is performed by a rolling mill to obtain a fifth intermediate forging;

[0041] Step S7, post-forging heat treatment is performed on the fifth intermediate forging to obtain a cylinder segment forging;

[0042] In the step S7, the post-forging heat treatment is performed on the fifth intermediate forging to obtain a cylinder segment forging, including:

[0043] Step S71, quenching treatment: the fifth intermediate forging is heated to 650-700 DEG C at a first heating rate, and after holding for 6-10 hours, it is heated to a quenching temperature at a second heating rate, and after holding for 8-10 hours, it is water-cooled to 90-100 DEG C to obtain a sixth intermediate forging; wherein the quenching temperature is 950-970 DEG C;

[0044] Step S72, tempering treatment: the sixth intermediate forging is heated to 300-400 DEG C, and after holding for 4-6 hours, it is heated to 650-700 DEG C at a third heating rate, and after holding for 8-10 hours, it is air-cooled to room temperature to obtain the cylinder segment forging.

[0045] The embodiment of the present application can make the internal gap of the forged piece better be compressed in the upsetting process by improving the forging ratio (1.50 to 1.54) of the first fire forging, and make the internal grain structure of the forged piece be broken more finely, thereby helping to improve the internal structure of the forged piece, eliminate the structure defects, and be beneficial to improving the strength and impact toughness of the forged piece. In addition, the heating temperature is 1240 DEG C to 1260 DEG C in the first fire forging to the fourth fire forging, and the heating temperature is appropriately reduced (1190 DEG C to 1210 DEG C) in the last fire forging, which can effectively prevent the grain in the forged piece from growing excessively, and be beneficial to further improving the impact toughness of the forged piece. Finally, the embodiment of the present application is beneficial to further ensuring that the cylinder segment forged piece has high strength and high impact toughness by quenching and tempering the forged piece and controlling the quenching temperature to 950 DEG C to 970 DEG C. In summary, the 12Cr2Mo1V cylinder segment forged piece prepared by the method of the embodiment of the present application has high strength and high impact toughness.

[0046] In some embodiments of the present application, in the step S71, the first heating rate is 80 DEG C / h to 100 DEG C / h, and the second heating rate is 80 DEG C / h to 100 DEG C / h; in the step S72, the third heating rate is 50 DEG C / h to 70 DEG C / h.

[0047] In some embodiments of the present application, in the step S3, the forging ratio of the second fire forging is 1.50 to 1.90; in the step S4, the forging ratio of the third fire forging is 1.04 to 1.06; in the step S5, the forging ratio of the fourth fire forging is 1.60 to 1.70; and in the step S6, the forging ratio of the fifth fire forging is 1.36 to 1.40.

[0048] In some embodiments of the present application, the chemical components of the 12Cr2Mo1V steel include, in terms of weight percentage, C: 0.14% to 0.15%; Si: 0 to 0.09%; Mn: 0.50% to 0.60%; P: 0 to 0.005%; S: 0 to 0.003%; Cr: 2.40% to 2.50%; Mo: 1.00% to 1.10%; V: 0.29% to 0.31%; Ni: 0.15% to 0.20%; Cu: 0 to 0.06%; Nb: 0.025%-0.040%; the balance is Fe and inevitable impurities; and the carbon equivalent CE is greater than 0.98%.

[0049] The selection of each component in the 12Cr2Mo1V steel in the embodiment is based on the following:

[0050] C element is the main strengthening element, directly affects the strength, plasticity and toughness of the forging, when C content is below 0.8%, with the increase of C content, the strength and hardness of the forging are improved. Therefore, the C element content in the embodiment of the application is controlled to be 0.14% to 0.15%.

[0051] Mn element is a weak carbide forming element, which can improve the strength of the steel, and does not reduce the plasticity of the steel within a certain content range. Mn element can form infinite solid solution with austenite, improve the hardenability of the steel, and the main use of Mn element in the material is to ensure the strength of the forging. Therefore, the Mn element content in the embodiment of the application is controlled to be 0.50% to 0.60%.

[0052] Cr element is a carbide forming element, which has a secondary hardening effect, can significantly improve the hardness and wear resistance of the steel. In the quenched and tempered steel, the main role of Cr element is to improve the hardenability of the forging, so that the forging can achieve excellent comprehensive mechanical properties after quenching and tempering. Therefore, the Cr element content in the embodiment of the application is controlled to be 2.40% to 2.50%.

[0053] The main role of Mo element in the material is to improve the hardenability of the material. With the increasing large-scale of the hydrogenation reactor main body forging, the wall thickness of the forging is also getting thicker, which brings certain difficulty to quenching and tempering, and Mn element can greatly improve the hardenability of the forging. Therefore, the Mo element content in the embodiment of the application is controlled to be 1.00 to 1.10%.

[0054] V element forms stable refractory carbide in the material, so that the steel still maintains fine grain structure at a higher temperature, greatly reducing the overheating sensitivity of the steel. Therefore, the V element content in the embodiment of the application is controlled to be 0.29% to 0.31%.

[0055] Ni element is a non-carbide forming element, the lattice constant is similar to that of austenite, can form a continuous solid solution with it, and improve the stability of austenite. Ni element has good effect on plasticity and toughness, can significantly improve the toughness of the steel and reduce the ductile-brittle transition temperature, and the strength of the steel still remains at a high level. For large forgings requiring comprehensive mechanical properties, Ni-containing steel is generally selected. When the steel contains Cr, Mo and other elements, the effect of Ni on improving the hardenability is obviously higher than that of single element. Therefore, the role of Ni element in the material is to improve the plasticity, toughness and hardenability of the forging. The Ni element content in the embodiment of the application is controlled to be 0.15% to 0.20%.

[0056] It is found through experiments that for 12Cr2Mo1V steel, when the carbon equivalent is greater than 0.98%, the impact toughness is higher.

[0057] This invention also provides a cylindrical section forging with high impact toughness, which is prepared by the method described above for preparing a cylindrical section forging with high impact toughness.

[0058] The present invention will be further described below with reference to specific embodiments.

[0059] Example 1

[0060] A1. The waste material at the sprue and riser ends of the steel ingot is removed to obtain a billet; the billet has a height of 3120mm and a diameter of 3150mm; the steel ingot is made of 12Cr2Mo1V steel; the chemical composition of the 12Cr2Mo1V steel includes: C: 0.15%; Si: 0.05%; Mn: 0.60%; P: 0.003%; S: 0.002%; Cr: 2.50%; Mo: 1.10%; V: 0.30%; Ni: 0.18%; Cu: 0.03%; Nb: 0.035%; the balance is Fe and unavoidable impurities.

[0061] A2. First forging: Heat the billet to 1250℃, hold for 40 hours, and upset to a height of 2050mm and a diameter of 3810mm. 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 1.52.

[0062] 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 3030mm, the height is 3750mm, and the forging ratio of the second fire forging is 1.82.

[0063] A4. Third Forging: Heat the second intermediate forging to 1240℃ to 1260℃, hold for 6 hours, and level it to a height of 3550mm to obtain the third intermediate forging. Figure 4 As shown; the forging ratio of the third forging is 1.05.

[0064] A5. Fourth Forging: The third intermediate forging is heated to 1250℃ and held for 7 hours. The hole is then enlarged using a lever to obtain the fourth intermediate forging, as shown below. Figure 5 As shown; the inner diameter of the fourth intermediate forging is 3200mm and the outer diameter is 4200mm, and the forging ratio of the fourth fire forging is 1.65.

[0065] A6, fifth fire forging: heating the third intermediate forge piece to 1200 °C, holding for 5 h, expanding by rolling mill to obtain a fifth intermediate forge piece, as shown in Figure 6 the fifth intermediate forge piece has an inner diameter of 4465 mm, an outer diameter of 5185 mm, and a height of 3550 mm.

[0066] A7, quenching treatment: heating the fifth intermediate forge piece to 675 °C at a rate of 100 °C / h, holding for 8 h, then heating to a quenching temperature at a rate of 100 °C / h, holding for 8 h to 10 h, then water cooling to 90 °C to obtain a sixth intermediate forge piece; wherein the quenching temperature is 960 °C;

[0067] A8, tempering treatment: heating the sixth intermediate forge piece to 350 °C, holding for 5 h, then heating to 690 °C at a rate of 70 °C / h, holding for 10 h, then air cooling to room temperature to obtain the cylinder segment forge piece.

[0068] Example 2

[0069] The difference from Example 1 is that step A6, fifth fire forging: heating the third intermediate forge piece to 1190 °C, holding for 5 h, expanding by rolling mill to obtain a fifth intermediate forge piece; the fifth intermediate forge piece has an inner diameter of 4465 mm, an outer diameter of 5185 mm, and a height of 3550 mm.

[0070] Example 3

[0071] The difference from Example 1 is that step A6, fifth fire forging: heating the third intermediate forge piece to 1210 °C, holding for 5 h, expanding by rolling mill to obtain a fifth intermediate forge piece; the fifth intermediate forge piece has an inner diameter of 4465 mm, an outer diameter of 5185 mm, and a height of 3550 mm.

[0072] Comparative Example 1

[0073] The difference from Example 1 is that step A2, first fire forging: heating the blank to 1250 °C, holding for 40 h, upsetting to a height of 2400 mm and a diameter of 3520 mm, then punching to obtain a first intermediate forge piece; the first intermediate forge piece has a center hole with an inner diameter of 1400 mm, and the forging ratio of the first fire forging is 1.30. Step A6, fifth fire forging: heating the third intermediate forge piece to 1250 °C, holding for 5 h, expanding by rolling mill to obtain a fifth intermediate forge piece; the fifth intermediate forge piece has an inner diameter of 4465 mm, an outer diameter of 5185 mm, and a height of 3550 mm.

[0074] Comparative Example 2

[0075] The difference between the example 1 and the comparative example 1 is that, in the step A6, the fifth fire forging, the third intermediate forging is heated to 1240℃, and is kept for 5h, and is expanded by a rolling mill to obtain the fifth intermediate forging; the inner diameter of the fifth intermediate forging is 4465mm, the outer diameter is 5185mm, and the height is 3550mm.

[0076] Comparative example 3

[0077] The difference between the example 1 and the comparative example 1 is that, in the step A6, the fifth fire forging, the third intermediate forging is heated to 1260℃, and is kept for 5h, and is expanded by a rolling mill to obtain the fifth intermediate forging; the inner diameter of the fifth intermediate forging is 4465mm, the outer diameter is 5185mm, and the height is 3550mm.

[0078] Comparative example 4

[0079] The difference between the example 1 and the comparative example 1 is that, in the step A7, the quenching temperature is 940℃.

[0080] Comparative example 5

[0081] The difference between the example 1 and the comparative example 1 is that, in the step A7, the quenching temperature is 1000℃.

[0082] Experimental example

[0083] The tensile strength and impact toughness of the cylinder segment forgings prepared in the example 1 to 3 and the comparative examples 1 to 5 are detected, and the results are shown in Table 1. Compared with the comparative examples 1 to 3, the cylinder segment forgings prepared in the example 1 to 3 not only have higher strength, but also have higher impact toughness. Compared with the example 1 to 3, the cylinder segment forgings prepared in the comparative example 4 have higher impact toughness, but the strength is too low. Compared with the example 1 to 3, the cylinder segment forgings prepared in the comparative example 5 have higher strength, but the impact toughness is too low. It can be seen that, compared with the comparative examples 1 to 5, the cylinder segment forgings prepared in the example 1 can ensure that both the strength and the impact toughness are suitable.

[0084] Table 1

[0085] Sample Tensile strength (Mpa) AKv(J) Example 1 651 210 Example 2 654 208 Example 3 656 212 Comparative Example 1 626 182 Comparative Example 2 624 186 Comparative Example 3 627 188 Comparative Example 4 632 212 Comparative Example 5 670 196

[0086] It should be noted that AKv in Table 1 is used to represent the impact toughness, which represents the energy absorbed by the material when subjected to impact load.

[0087] Although the present application is disclosed as above, the protection scope of the present application is not limited to this. Those skilled in the art can make various changes and modifications without departing from the spirit and scope of the present application, and these changes and modifications will fall within the protection scope of the present application.

Claims

1. A method of producing a cylinder segment forging having high impact toughness, characterized by, The utility model relates to a kind of 12Cr2Mo1V steel tube segment forging method, including: Step S1, the scrap of the nozzle end and the riser end of ingot is cut off, and blank is obtained; The material of the ingot is 12Cr2Mo1V steel; The chemical composition of the 12Cr2Mo1V steel includes, by weight percentage: C: 0.14% to 0.15%; Si: 0 to 0.09%; Mn: 0.50% to 0.60%; P: 0 to 0.005%; S: 0 to 0.003%; Cr: 2.40% to 2.50%; Mo: 1.00% to 1.10%; V: 0.29% to 0.31%; Ni: 0.15% to 0.20%; Cu: 0 to 0.06%; Nb: 0.025%-0.040%; the balance is Fe and inevitable impurities; carbon equivalent CE is greater than 0.98%; Step S2, first fire forging: the blank is heated to 1240℃ to 1260℃, and heat preservation treatment is carried out, then upsetting and punching are carried out, and first intermediate forging is obtained;The forging ratio of the first fire forging is 1.50 to 1.

54. Step S3, second fire forging: the first intermediate forging is heated to 1240℃ to 1260℃, and heat preservation treatment is carried out, and core rod lengthening is carried out, and second intermediate forging is obtained; Step S4, third fire forging: the second intermediate forging is heated to 1240℃ to 1260℃, and heat preservation treatment is carried out, and flattening is carried out, and third intermediate forging is obtained; Step S5, fourth fire forging: the third intermediate forging is heated to 1240℃ to 1260℃, and heat preservation treatment is carried out, and hole expansion is carried out through mandrel, and fourth intermediate forging is obtained; Step S6, fifth fire forging: the third intermediate forging is heated to 1190℃ to 1210℃, and heat preservation treatment is carried out, and hole expansion is carried out through rolling mill, and fifth intermediate forging is obtained; Step S7, post-forging heat treatment is carried out on the fifth intermediate forging, and cylinder segment forging is obtained; In the step S7, the post-forging heat treatment is carried out on the fifth intermediate forging, and cylinder segment forging is obtained, including: Step S71, quenching treatment: the fifth intermediate forging is heated to 650℃ to 700℃ at a first heating rate, and heat preservation is carried out for 6h to 10h, then heated to quenching temperature at a second heating rate, and heat preservation is carried out for 8h to 10h, then water-cooled to 90 to 100℃, and sixth intermediate forging is obtained;The quenching temperature is 950℃ to 970℃. Step S72, tempering treatment: the sixth intermediate forging is heated to 300℃ to 400℃, and heat preservation is carried out for 4h to 6h, then heated to 650℃ to 700℃ at a third heating rate, and heat preservation is carried out for 8h to 10h, then air-cooled to room temperature, and the cylinder segment forging is obtained.

2. The method of manufacturing a cylinder segment forging having high impact toughness according to claim 1, wherein In the step S3, the forging ratio of the second fire forging is 1.50 to 1.

90.

3. The method of manufacturing a cylinder segment forging having high impact toughness according to claim 1, wherein In the step S4, the forging ratio of the third fire forging is 1.04 to 1.

06.

4. The method of producing a cylinder segment forging having high impact toughness according to claim 1, wherein In the step S5, the forging ratio of the fourth fire forging is 1.60 to 1.

70.

5. The method of manufacturing a cylinder segment forging having high impact toughness according to claim 1, wherein In the step S6, the forging ratio of the fifth fire forging is 1.36 to 1.

40.

6. The method of producing a cylinder segment forging having high impact toughness according to claim 1, wherein In the step S71, the first heating rate is 80℃ / h to 100℃ / h.

7. The method of producing a cylinder segment forging having high impact toughness according to claim 1, wherein In the step S71, the second temperature increasing rate is 80-100°C / h.

8. The method of producing a cylinder segment forging having high impact toughness according to claim 1, wherein In the step S72, the third temperature increasing rate is 50-70°C / h.

9. A cylinder segment forging having high impact toughness, characterized in that The barrel segment forgings with high impact toughness are prepared by the method according to any one of claims 1-8.

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