CN115369323B - 800 MPa-level hydrogen-induced crack resistant container steel plate and production method thereof - Google Patents
800 MPa-level hydrogen-induced crack resistant container steel plate and production method thereof Download PDFInfo
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- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
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Abstract
The invention relates to a 800 MPa-level hydrogen-induced crack resistant container steel plate and a production method thereof, wherein the steel plate comprises the chemical components of 0.2-0.25% of C, 0.15-0.35% of Si, 0.8-0.85% of Mn, less than or equal to 0.003% of P, less than or equal to 0.001% of S and less than or equal to Mo:0.03 to 0.05 percent, 0.2 to 0.3 percent of V, 0.0003 to 0.002 percent of Ca, 0.002 to 0.03 percent of Als and the balance of Fe and impurities. The steel plate tissue segregation is reduced by controlling the C, mn content in the steel, and the shape of inclusions in the steel is changed by adding Ca; the alloy element V, mo is added to refine grains, so that the steel plate has good toughness, and the steel plate is ensured to have good comprehensive performance after normalizing and simulated post-welding heat treatment through precipitation strengthening; the heat treatment mode of staged rolling and normalizing weak cooling/short-time normalizing is adopted, so that the finished steel plate is ensured to have uniform grain size and high strength in the whole thickness direction, and simultaneously has excellent hydrogen induced crack resistance.
Description
Technical Field
The invention relates to the technical field of steel plates for pressure containers, in particular to a 800 MPa-level steel plate for a container with excellent hydrogen induced cracking resistance and a production method thereof.
Background
Hydrogen sulfide is one of the most corrosive harmful mediums in oil and gas, and during the transportation of natural gas, hydrogen sulfide has a great proportion of stress corrosion to a transportation pipeline. When used in a wet hydrogen sulfide environment, can lead to Hydrogen Bubbling (HB), hydrogen Induced Cracking (HIC), and stress-induced hydrogen induced cracking (SOHIC) within carbon steel. In an acidic environment containing hydrogen sulfide or the like, cracks generated by penetration of hydrogen generated by corrosion into steel become Hydrogen Induced Cracking (HIC). In the past, it was found that the hydrogen induced properties of steel are greatly related to the strength of steel. The higher the strength of the steel sheet, the poorer the hydrogen resistance of the steel tends to be. At present, the HIC-resistant steel plate is mainly used for pipeline steel and container steel, and the normalizing performance and the subsequent welding and repairing are considered for the container steel, so that the properties of the steel plate subjected to simulated post-welding heat treatment still meet the requirements.
With the increasing economic development and energy demand, the reserve of petroleum and natural gas as strategic materials becomes one of the indexes for measuring the economic sustainable development capability of various countries, and large-scale petroleum and liquefied natural gas storage tanks are also built in succession in China. Therefore, there is a need to develop a steel plate for large liquefied petroleum gas spherical tanks, which has excellent comprehensive properties, strength and toughness superior to those of conventional steels, and welding performance and hydrogen sulfide stress corrosion resistance similar to or even better than those of conventional steels, and cost lower than those of foreign materials with the same properties.
The Chinese patent application with the application number of CN201210055848.5 discloses a steel for a hydrogen induced cracking resistant pressure vessel and a manufacturing method thereof, and relates to a low-carbon high-strength low-alloy thick steel plate with the tensile strength of more than or equal to 620MPa, wherein the steel plate comprises the following components in percentage by weight: 0.15 to 0.25 percent of Si:0.10 to 0.30 percent of Mn: 1.00-1.60%, P: less than or equal to 0.012 percent, S less than or equal to 0.002 percent, mo:0.35 to 0.60 percent, V is less than or equal to 0.05 percent, ni:0.20 to 0.80 percent of Ca:0.0013 to 0.0045% and Al: 0.002-0.050% by heat treatment process of quenching and tempering, but the heat treatment process makes the steel plate production cost higher.
The Chinese patent application with the application number of CN201310497333.5 discloses a 450 MPa-grade steel plate for a hydrogen induced cracking resistant pressure vessel and a production method thereof, wherein the steel plate comprises the following components in percentage by weight: 0.13 to 0.14 percent of Si:0.20 to 0.30 percent of Mn: chemical components of 0.90-0.95%, P less than or equal to 0.008% and S less than or equal to 0.001% are rolled by adopting control of thickness which is 2.0 times in two stages, a controlled rolling and cooling process of 10-12 ℃/S cooling speed acceleration cooling is adopted after rolling, and an off-line normalizing heat treatment process is adopted, so that the tensile strength of the steel plate reaches 450-464 MPa finally. The strength grade of the produced steel plate is low, and the aspects of long-time simulation of post-welding heat treatment performance and the like are not required.
The Chinese patent application with publication number of CN105603304A discloses a thick steel plate for a Q370R pressure vessel with good HIC and SSCC resistance and a manufacturing method thereof, wherein a vessel steel plate with the maximum thickness of 60mm is produced by adopting a normalizing and water-cooling heat treatment process, and the steel plate has good HIC and SSCC resistance through reasonable component design. In order to improve the strength of the steel sheet, a high Mn (1.40 to 1.62%) component design is used in examples. However, mn element and S element are easy to form MnS inclusion and become a hydrogen trap, so that the risk of hydrogen induced cracking is increased; meanwhile, the adopted heat treatment process of water cooling after normalizing can cause non-uniformity of tissue in the thickness direction due to the difference of cooling speed. The results of the hydrogen induced cracking resistance tests of 3 of the 6 examples show that cracks exist, and the stability of the HIC resistance of the steel plate is relatively poor. In the embodiment, the maximum steel plate thickness is only 60mm, and the use requirement of a large-scale pressure vessel in the petrochemical industry cannot be met.
In view of the above, there is a need to develop a high strength pressure vessel steel sheet having good hydrogen induced cracking resistance through a novel composition design and a matched process.
Disclosure of Invention
The invention provides a 800 MPa-level hydrogen-induced crack resistant container steel plate and a production method thereof, wherein the content of C, mn in steel is controlled, the tissue segregation of the steel plate is reduced, and the shape of inclusions in the steel is changed by adding Ca; the alloy element V, mo is added to refine grains, so that the steel plate has good toughness, and the steel plate is ensured to have good comprehensive performance after normalizing and simulated post-welding heat treatment through precipitation strengthening; the production process matched with the steel plate component adopts a heat treatment mode of staged rolling and normalizing weak cooling/short-time normalizing, ensures that the finished steel plate has uniform grain size and high strength in the whole thickness direction and has excellent hydrogen-induced crack resistance.
In order to achieve the above purpose, the invention is realized by adopting the following technical scheme:
the 800 MPa-level hydrogen-induced crack resistant container steel plate comprises, by weight, 0.2% -0.25% of C, 0.15% -0.35% of Si, 0.8% -0.85% of Mn, less than or equal to 0.003% of P, less than or equal to 0.001% of S and less than or equal to Mo:0.03 to 0.05 percent, 0.2 to 0.3 percent of V, 0.0003 to 0.002 percent of Ca, 0.002 to 0.003 percent of Als and the balance of Fe and unavoidable impurities.
The production process of 800MPa level hydrogen-induced cracking resistant container steel plate includes smelting, continuous casting, heating, rolling and heat treatment; the method comprises the following steps:
1) Continuous casting process: the pouring temperature of the tundish molten steel is less than or equal to 1560 ℃, and an electromagnetic stirring or continuous casting billet light pressing process is adopted, so that the pressing rate is controlled to be 6-9%;
2) Heating procedure: the heating temperature of the continuous casting blank is 1150-1200 ℃, and the soaking time is 1-3 h;
3) And (3) rolling: adopting a two-stage controlled rolling process; wherein the finishing temperature of the first stage is more than or equal to 1050 ℃, and the single pass reduction rate is 8-11%; the two-stage initial rolling temperature is more than or equal to 970 ℃, and the single-pass rolling reduction rate is 5-8%;
4) And (3) a heat treatment procedure: the thickness of the finished steel plate is 40-100 mm; different heat treatment processes are selected for the rolled steel plate according to the thickness; wherein, the steel plate with t less than or equal to 40mm and less than 60mm adopts a normalizing weak cold and hot treatment process, the steel plate with t less than or equal to 60mm and less than or equal to 100mm adopts a short-time normalizing heat treatment process, and t is the thickness of the steel plate.
Further, the smelting process adopts a smelting process of electric furnace smelting and VOD vacuum treatment.
Further, in the heat treatment procedure, the normalizing weak cold and hot treatment process comprises the following steps: the heat treatment temperature is controlled between 880 and 890 ℃, the temperature rising rate is 1.1 to 1.3min/mm, the net heat preservation time is 0.5 to 0.6min/mm, the furnace is taken out and weakly cooled after reaching the temperature, and the cooling rate is 1.6 to 2.0 ℃/s; the redback temperature is 330-340 ℃.
Further, in the heat treatment procedure, the short-time normalizing heat treatment process comprises the following steps: the heat treatment temperature is controlled to 860-880 ℃, the temperature rising rate is 1.2-1.4 min/mm, the furnace is taken out for air cooling after reaching the temperature, and the total furnace time is less than or equal to 2h.
Further, the microstructure of the finished steel plate is ferrite, pearlite and a small amount of evenly dispersed bainite.
Further, the properties of the finished steel sheet are as follows: the yield strength is 444-453 MPa, the tensile strength is 806-828 MPa, and the elongation after fracture is more than or equal to 24%; charpy impact energy AV at-20 ℃ of 3 samples 2 The average value is more than or equal to 242J, b=2a, and the 180-degree cold bending test d=3a is qualified; hydrogen induced cracking experiments were performed according to GB/T8650-2006, and qualified according to NACE TM0284 assessment method for hydrogen induced cracking resistance of pipeline Steel and pressure vessel Steel.
Compared with the prior art, the invention has the beneficial effects that:
1) The design aspect of steel grade components: the composition design is simple and reasonable, the segregation degree of the steel plate is light by reasonably controlling the C, mn content in the steel in order to ensure the hydrogen-induced cracking resistance of the steel plate, and Ca is added to change the shape of inclusions in the steel; in order to ensure that the steel plate has good toughness, alloy elements V, mo are added into the steel, crystal grains are thinned, and the steel plate is ensured to have good comprehensive performance after normalizing and simulated post-welding heat treatment through precipitation strengthening;
2) In terms of production process: the multi-pass rolling small deformation rolling is adopted, which is favorable for refining grain structure; the heat treatment mode of staged rolling and normalizing weak cooling/short-time normalizing is adopted, so that the finished steel plate is ensured to have uniform grain size and high strength in the whole thickness direction, and simultaneously has excellent hydrogen induced crack resistance.
Drawings
FIG. 1 is a photograph of a metallographic structure of an 800 MPa-grade hydrogen induced cracking resistant container steel plate according to the present invention.
Detailed Description
The 800 MPa-level hydrogen-induced crack resistant container steel plate comprises, by weight, 0.2% -0.25% of C, 0.15% -0.35% of Si, 0.8% -0.85% of Mn, less than or equal to 0.003% of P, less than or equal to 0.001% of S and less than or equal to Mo:0.03 to 0.05 percent, 0.2 to 0.3 percent of V, 0.0003 to 0.002 percent of Ca, 0.002 to 0.003 percent of Als and the balance of Fe and unavoidable impurities.
The invention relates to a production method of 800 MPa-level hydrogen-induced crack resistant container steel plate, wherein the production process of the steel plate comprises smelting, continuous casting, heating, rolling and heat treatment; the method comprises the following steps:
1) Continuous casting process: the pouring temperature of the tundish molten steel is less than or equal to 1560 ℃, and an electromagnetic stirring or continuous casting billet light pressing process is adopted, so that the pressing rate is controlled to be 6-9%;
2) Heating procedure: the heating temperature of the continuous casting blank is 1150-1200 ℃, and the soaking time is 1-3 h;
3) And (3) rolling: adopting a two-stage controlled rolling process; wherein the finishing temperature of the first stage is more than or equal to 1050 ℃, and the single pass reduction rate is 8-11%; the two-stage initial rolling temperature is more than or equal to 970 ℃, and the single-pass rolling reduction rate is 5-8%;
4) And (3) a heat treatment procedure: the thickness of the finished steel plate is 40-100 mm; different heat treatment processes are selected for the rolled steel plate according to the thickness; wherein, the steel plate with t less than or equal to 40mm and less than 60mm adopts a normalizing weak cold and hot treatment process, the steel plate with t less than or equal to 60mm and less than or equal to 100mm adopts a short-time normalizing heat treatment process, and t is the thickness of the steel plate.
Further, the smelting process adopts a smelting process of electric furnace smelting and VOD vacuum treatment.
Further, in the heat treatment procedure, the normalizing weak cold and hot treatment process comprises the following steps: the heat treatment temperature is controlled between 880 and 890 ℃, the temperature rising rate is 1.1 to 1.3min/mm, the net heat preservation time is 0.5 to 0.6min/mm, the furnace is taken out and weakly cooled after reaching the temperature, and the cooling rate is 1.6 to 2.0 ℃/s; the redback temperature is 330-340 ℃.
Further, in the heat treatment procedure, the short-time normalizing heat treatment process comprises the following steps: the heat treatment temperature is controlled to 860-880 ℃, the temperature rising rate is 1.2-1.4 min/mm, the furnace is taken out for air cooling after reaching the temperature, and the total furnace time is less than or equal to 2h.
Further, the microstructure of the finished steel plate is ferrite, pearlite and a small amount of evenly dispersed bainite.
Further, the properties of the finished steel sheet are as follows: the yield strength is 444-453 MPa, the tensile strength is 806-828 MPa, and the elongation after fracture is more than or equal to 24%; charpy impact energy AV at-20 ℃ of 3 samples 2 The average value is more than or equal to 242J, b=2a, and the 180-degree cold bending test d=3a is qualified; hydrogen induced cracking experiments were performed according to GB/T8650-2006, and qualified according to NACE TM0284 assessment method for hydrogen induced cracking resistance of pipeline Steel and pressure vessel Steel.
The invention relates to a 800 MPa-level hydrogen-induced crack resistant container steel plate, which is designed according to the chemical composition and the action principle as follows:
c often forms carbides with other alloying elements in the steel, which act as reinforcement for the steel. From the viewpoint of ensuring the strength of the steel sheet, it is desirable that the C content is kept at a high level, but the high C content tends to cause segregation in the steel, resulting in a significant decrease in the toughness and plasticity of the steel sheet. The invention adopts VC/N refined grains to solve the problem. Therefore, on the premise of ensuring the strength of the steel plate, the content of C is controlled to be 0.2-0.25%.
Si has deoxidizing and desulfurizing effects in steel and can improve the strength of steel sheet by solid solution strengthening. Si is an inexpensive alloying element, and addition of Si in an appropriate amount to steel can improve the hardness and strength of ferrite in the steel. Si can increase the elastic limit, yield strength and yield ratio, and fatigue strength and fatigue ratio of steel, and can increase strength and improve local corrosion resistance to a certain extent. However, if the Si content is high, the impact toughness of the heat affected zone is negatively affected, so the Si content is limited to 0.35-0.50% in the invention.
Mn element is a common desulfurizing agent in steel, and Mn and S are easy to form MnS inclusion; the martensite and bainite of the hard phase with high strength and low toughness, which are generated by the segregation of Mn in steel, increase the cracking tendency after welding and adversely affect the hydrogen cracking resistance, so that the Mn content is not easy to be excessively high. The Mn content is limited to 0.8-0.85% by comprehensively considering factors of the strength, toughness and hydrogen induced cracking resistance of the steel plate.
P, S is an embrittling element in steel and is also an extremely segregation element, so that the lower the content is, the better. The two components have great damage to the low-temperature toughness of steel, but the content of P, S is controlled below 0.003 percent and below 0.001 percent respectively in consideration of the operability of steel making, the steel making cost, the requirement of use and other factors.
Mo: is a weak solid solution strengthening element, and has the main function of increasing the supercooling capability of austenite in steel, thereby refining the structure, obtaining the strengthening effect and having good influence on impact toughness and brittle transition temperature. In addition, mo has a significant positive impact on PWHT performance at high temperature and long time; however, mo adversely affects the weldability of the steel sheet, and is a noble metal, and is expensive. Therefore, the invention controls the content of Mo to be 0.03-0.05%.
V: the main element in the steel of the present invention is a strong carbonitride forming element. Firstly, V is an element far from iron on the left side in the periodic table of elements, stable carbide (VC) is easy to form, the formed titanium carbide is difficult to dissolve when being heated, the expansion of grain boundaries can be effectively inhibited, the growth of austenite grains is strongly hindered, meanwhile, the formation of ferrite is promoted, and for this reason, the steel plate is difficult to overheat when being heated by heat treatment, which is beneficial to the heat treatment operation. Second, V can fix the N element in the steel. The content of V (C, N) in the alloy is precisely controlled by reasonably controlling the content of Ti element. During rolling, a certain amount of deformation energy storage can be generated on the steel plate rolled in an austenite region, and the deformation energy storage with different degrees can have different degrees of influence on the kinetics of precipitation and precipitation of V (C, N) in austenite. In the experiment, the VC particles are promoted to be separated out in the high-temperature and low-temperature stages of an austenite region respectively by increasing deformation energy storage, so that austenite recrystallization can be better inhibited, and the growth of austenite grains is prevented. Meanwhile, the critical nucleation size of the VC in the austenitic region, particularly in the high-temperature region, is greatly reduced, the precipitation strengthening effect of the VC is improved, and the purposes of improving the strength of the steel plate and ensuring the toughness are achieved. The stable VC plays a role of fixing C, reduces the reaction of free C and H in steel, namely reduces the generation of harmful substances such as methane and the like, reduces decarburization, swelling and cracking tendency of the steel plate, and ensures the excellent hydrogen induced cracking resistance of the steel plate. However, researches show that excessive V can cause abnormal growth of crystal grains, so that the content of V is controlled within the range of 0.2-0.3%.
Ca: the composition plays a role in controlling the form of sulfide in steel, and has an effect of suppressing the formation of MnS by the formation of CaS. In order to obtain this effect, the Ca content needs to be 0.0003% or more. In addition, if the Ca content exceeds 0.005%, the CaS size formed is too large, and brittleness is also increased, which tends to become a starting point of fracture crack sources. Therefore, the Ca content is limited to 0.0003% -0.002%.
Als: as deoxidizing element in steel, alN is formed in steel, so that grains can be effectively refined, and the content of AlN is controlled to be 0.002% -0.003%.
The invention relates to a production method of 800 MPa-level hydrogen-induced crack resistant container steel plates, which comprises the working procedures of smelting, continuous casting, heating, rolling, heat treatment and the like, and the specific design principle is as follows:
1. adopting electric furnace smelting and VOD vacuum treatment process smelting.
2. By adopting a continuous casting process, the process is mainly to control the casting temperature, namely the casting temperature of the molten steel of the tundish is less than or equal to 1560 ℃, and the original cast structure can be thinned by low-temperature casting. In order to control center segregation and porosity of the continuous casting billet, an electromagnetic stirring or continuous casting billet light reduction process is adopted, wherein the reduction rate is controlled to be 6% -9%.
3. The heating temperature of the continuous casting blank is 1150-1200 ℃, and the soaking time is 1-3 h. When the heating temperature is lower than 1150 ℃, coarse precipitates in the continuous casting blank cannot be dissolved, austenitizing of the steel plate is incomplete, and the finishing temperature of the first stage cannot be ensured; when the heating temperature is higher than 1200 ℃, fine precipitates in the continuous casting blank are easy to redissolve, and the crystal grains are excessively grown.
3. The continuous casting billet rolling adopts a two-stage rolling control process. The final rolling temperature at one stage is more than or equal to 1050 ℃, and the high deformation is adopted for rapid rolling at the stage, the single pass reduction rate is 8-11%, and the near surface of the steel plate is ensured to be completely and dynamically recrystallized; the initial rolling temperature of the two stages is more than or equal to 970 ℃, the small deformation is adopted for rapid rolling in the stage, the single-pass rolling reduction rate is 5-8%, and the near surface of the steel plate is ensured not to be recrystallized.
4. And the rolled steel plate adopts two processes of normalizing weak cooling and short-time normalizing according to the plate thickness specification. Wherein, the steel plate with the thickness of 40-60 mm adopts normalizing weak cooling, and the steel plate with the thickness of 60-100 mm adopts short-time normalizing heat treatment process. The short-time normalizing heat treatment process is that the heat treatment temperature is 860-880 ℃, the heating rate is 1.2-1.4 min/mm, the furnace is taken out for air cooling after reaching the temperature, and the total furnace time is 1-1.2 h. The normalizing weak cold and hot treatment process is that the heat treatment temperature is controlled to 880-890 ℃, the heating rate is 1.1-1.3 min/mm, the net heat preservation time is 0.5-0.6 min/mm, the furnace is taken out after the temperature reaches the temperature, the weak cold is realized, and the reddening temperature is 330-340 ℃.
The following examples are given by way of illustration of detailed embodiments and specific procedures based on the technical scheme of the present invention, but the scope of the present invention is not limited to the following examples.
[ example ]
Table 1 shows the chemical composition of the steel plate, table 2 shows the continuous casting and rolling process parameters of the steel plate, table 3 shows the post-rolling heat treatment process parameters of the steel plate, table 4 shows the mechanical properties of the steel plate for simulating post-welding heat treatment, table 5 shows the grain size and nonmetallic inclusion test results, and table 6 shows the hydrogen induced cracking resistance detection results of the steel plate.
TABLE 1 chemical composition (wt%) of steel plate
| Examples | C | Si | Mn | P | S | Mo | V | Ca | Als |
| 1 | 0.21 | 0.16 | 0.81 | 0.0028 | 0.0008 | 0.035 | 0.26 | 0.00036 | 0.0023 |
| 2 | 0.20 | 0.34 | 0.83 | 0.0015 | 0.0005 | 0.041 | 0.29 | 0.00042 | 0.0021 |
| 3 | 0.20 | 0.29 | 0.85 | 0.0019 | 0.0009 | 0.038 | 0.30 | 0.00036 | 0.0020 |
| 4 | 0.23 | 0.22 | 0.85 | 0.0010 | 0.0010 | 0.045 | 0.20 | 0.001 | 0.0026 |
| 5 | 0.25 | 0.32 | 0.82 | 0.0019 | 0.0007 | 0.039 | 0.28 | 0.0011 | 0.0024 |
| 6 | 0.24 | 0.35 | 0.83 | 0.0020 | 0.0008 | 0.048 | 0.25 | 0.0012 | 0.0023 |
Table 2 continuous casting and rolling process parameters of steel sheet
Table 3 heat treatment process parameters of steel sheet
Table 4 mechanical properties of the steel sheet for simulating post-weld heat treatment
In table 4, reL is yield strength, rm is tensile strength, a is elongation after break; in the cold bending test, b is the sample width, a is the nominal thickness, and d is the core diameter.
TABLE 5 grain size and nonmetallic inclusion test results
Table 6 results of testing hydrogen induced cracking resistance of steel sheet
FIG. 1 is a photograph of metallographic structure of a finished steel plate produced in example 1, wherein the steel plate structure is ferrite, pearlite and a small amount of evenly dispersed bainite, and the degree of structure segregation in the steel is low.
The foregoing is only a preferred embodiment of the present invention, but the scope of the present invention is not limited thereto, and any person skilled in the art, who is within the scope of the present invention, should make equivalent substitutions or modifications according to the technical scheme of the present invention and the inventive concept thereof, and should be covered by the scope of the present invention.
Claims (3)
1. A production method of 800 MPa-grade hydrogen-induced crack resistant container steel plate is characterized in that the steel plate comprises the following chemical components, by weight, 0.2% -0.25% of C, 0.15% -0.35% of Si, 0.81% -0.85% of Mn, less than or equal to 0.003% of P, less than or equal to 0.001% of S and less than or equal to Mo:0.03 to 0.05 percent, 0.25 to 0.3 percent of V, 0.0003 to 0.002 percent of Ca, 0.002 to 0.003 percent of Als and the balance of Fe and unavoidable impurities;
the production process of the steel plate comprises smelting, continuous casting, heating, rolling and heat treatment; the method comprises the following steps:
1) Continuous casting process: the pouring temperature of the tundish molten steel is less than or equal to 1560 ℃, and an electromagnetic stirring or continuous casting billet light pressing process is adopted, so that the pressing rate is controlled to be 6-9%;
2) Heating procedure: the heating temperature of the continuous casting blank is 1150-1200 ℃, and the soaking time is 1-3 h;
3) And (3) rolling: adopting a two-stage controlled rolling process; wherein the finishing temperature of the first stage is more than or equal to 1050 ℃, and the single pass reduction rate is 8-11%; the two-stage initial rolling temperature is more than or equal to 970 ℃, and the single-pass rolling reduction rate is 5-8%;
4) And (3) a heat treatment procedure: the thickness of the finished steel plate is 40-100 mm; different heat treatment processes are selected for the rolled steel plate according to the thickness; wherein, the steel plate with t less than or equal to 40mm and less than 60mm adopts a normalizing weak cold and hot treatment process, the steel plate with t less than or equal to 60mm and less than or equal to 100mm adopts a short-time normalizing heat treatment process, and t is the thickness of the steel plate;
the normalizing weak cold and hot treatment process comprises the following steps: the heat treatment temperature is controlled at 882-890 ℃, the heating rate is 1.1-1.3 min/mm, the net heat preservation time is 0.5-0.6 min/mm, the furnace is taken out and weakly cooled after reaching the temperature, and the cooling rate is 1.6-2.0 ℃/s; the redback temperature is 330-340 ℃;
the short-time normalizing heat treatment process comprises the following steps: the heat treatment temperature is controlled to 860-880 ℃, the temperature rising rate is 1.2-1.4 min/mm, the furnace is taken out for air cooling after reaching the temperature, and the total furnace time is less than or equal to 2h.
2. The method for producing 800 MPa-level hydrogen-induced cracking resistant container steel plate according to claim 1, wherein the smelting process adopts a smelting process of electric furnace smelting and VOD vacuum treatment.
3. The method for producing 800 MPa-grade hydrogen induced cracking resistant container steel sheet according to claim 1, wherein the properties of the finished steel sheet are as follows: the yield strength is 444-453 MPa, the tensile strength is 806-828 MPa, and the elongation after fracture is more than or equal to 24%; charpy impact energy kV at-20 ℃ of 3 samples 2 The average value is more than or equal to 242J, b=2a, and the 180-degree cold bending test d=3a is qualified; hydrogen induced cracking experiments were performed according to GB/T8650-2006, and qualified according to NACE TM0284 assessment method for hydrogen induced cracking resistance of pipeline Steel and pressure vessel Steel.
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Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2011001607A (en) * | 2009-06-19 | 2011-01-06 | Sumitomo Metal Ind Ltd | Thick steel plate having excellent hydrogen-induced cracking resistance and brittle crack arrest property |
| CN103556047A (en) * | 2013-10-22 | 2014-02-05 | 首钢总公司 | 450MPa-grade hydrogen-induced-cracking-resistant pressure vessel steel plate and production method thereof |
| CN105603313A (en) * | 2016-01-25 | 2016-05-25 | 宝山钢铁股份有限公司 | Steel for petroleum casing pipe with low yield ratio, manufacturing method of steel and production method of casing pipe |
| CN108411196A (en) * | 2018-03-27 | 2018-08-17 | 武汉钢铁有限公司 | Tensile strength is 680MPa grades of large-scale mobile steelss for pressure vessel use and production method |
| CN109694991A (en) * | 2017-10-20 | 2019-04-30 | 鞍钢股份有限公司 | A kind of tank plate that hydrogen induced cracking resistance can be excellent |
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Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2011001607A (en) * | 2009-06-19 | 2011-01-06 | Sumitomo Metal Ind Ltd | Thick steel plate having excellent hydrogen-induced cracking resistance and brittle crack arrest property |
| CN103556047A (en) * | 2013-10-22 | 2014-02-05 | 首钢总公司 | 450MPa-grade hydrogen-induced-cracking-resistant pressure vessel steel plate and production method thereof |
| CN105603313A (en) * | 2016-01-25 | 2016-05-25 | 宝山钢铁股份有限公司 | Steel for petroleum casing pipe with low yield ratio, manufacturing method of steel and production method of casing pipe |
| CN109694991A (en) * | 2017-10-20 | 2019-04-30 | 鞍钢股份有限公司 | A kind of tank plate that hydrogen induced cracking resistance can be excellent |
| CN108411196A (en) * | 2018-03-27 | 2018-08-17 | 武汉钢铁有限公司 | Tensile strength is 680MPa grades of large-scale mobile steelss for pressure vessel use and production method |
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