CN110923412A - 14Cr1MoR (H) steel plate for ultra-large-thickness high-pressure low-temperature container and production method thereof - Google Patents
14Cr1MoR (H) steel plate for ultra-large-thickness high-pressure low-temperature container and production method thereof Download PDFInfo
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Abstract
The invention provides a 14Cr1MoR (H) steel plate for an ultra-large-thickness high-pressure low-temperature container and a production method thereof, wherein the steel plate consists of the following elements: c, Si, Mn, P, S, Ni, Cr, Cu, Mo, Al, As, Sn, Sb, O, N, H, and the balance of Fe and inevitable impurities; the steel plate is subjected to a heat treatment process of normalizing (quick cooling), quenching and tempering without increasing the alloy cost, the obtained structure is mainly a bainite tempered structure, the grain size of the steel plate can reach more than 9 grades, the high-temperature tensile property Rp0.2 at 540 ℃ reaches more than 310Mpa, the impact energy at minus 20 ℃ reaches more than 100J, the mechanical property index is far higher than the national standard, and the service performance, the mechanical property and the stability are all subjected to sharp changes, so that the steel plate has positive significance for filling up domestic blank and meeting market demands.
Description
Technical Field
The invention relates to an ultra-thick steel plate and a manufacturing method thereof, in particular to a 14Cr1MoR (H) steel plate which can meet the requirement of a high-pressure low-temperature container with the thickness of 200mm and more than 200mm and a production method thereof.
Background
The 14Cr1MoR (H) is widely applied to industries such as petroleum, chemical engineering, power stations, boilers and the like, and is used for manufacturing equipment and components such as reactors, heat exchangers, oil gas tanks, liquefied gas tanks, gasification furnaces, nuclear reactor pressure shells and the like.
The conventional 14Cr1MoR does not generally require the hydrogen-contacting performance and has no special elements such As P, S, Sn, As, Sb and the like. Along with the development of large-scale equipment, the special environment of a hydrogenation reactor is met, the requirements of high-temperature strength, tempering embrittlement resistance and hydrogen corrosion resistance are met besides the basic normal-temperature mechanical property required by relevant standards, and meanwhile, the steel plate has good processing forming property, weldability and the like, in addition, because the process difficulty of heat treatment of a thick steel plate is high, the limit of the latest national standard thickness of a commercialized 14Cr1MoR steel plate is 200mm, and the-20 ℃ impact energy of a 1/2-position is met according to the use requirement of a client; at present, the domestic production technical equipment and process technology level, the impact property of 1/2-20 ℃ and the high-temperature and high-pressure performance of the steel plate are difficult to ensure when the thickness exceeds 100mm, and the steel plate mainly depends on imported products according to the increasing demands of the market.
Disclosure of Invention
One of the objects of the present invention is to obtain a 14Cr1MoR (H) steel sheet for a high-pressure low-temperature vessel having a thickness of 200mm or more and 200mm or more.
The invention also aims to provide a production method for obtaining the 14Cr1MoR (H) steel plate with the thickness of 200mm and more than 200mm for the high-pressure low-temperature container.
The above purpose can be realized by the following technical scheme: a14 Cr1MoR (H) steel plate for an ultra-large thickness high-pressure low-temperature container, namely a hydrogen-contacting device, comprises the following elements in percentage by mass: less than or equal to 0.14 percent of C, less than or equal to 0.60 percent of Si, 0.40 to 0.65 percent of MnP, less than or equal to 0.005 percent of S, less than or equal to 0.30 percent of Ni, less than or equal to 1.15 to 1.50 percent of Cr1, less than or equal to 0.10 percent of Cu, 0.45 to 0.65 percent of Mo0.025 to 0.040 percent of Al, less than or equal to 0.012 percent of As, less than or equal to 0.005 percent of Sn, less than or equal to 0.005 percent of Sb, less than or equal to 0.003 percent of O, less than or equal to 0.008 percent of.
The action of the above chemical elements was analyzed as follows: the 14Cr1MoR for the hydrogen-contacting equipment has the requirement of tempering embrittlement resistance, and from the J coefficient formula and the X coefficient formula, the contents of Si, Mn, P, Sn, Sb and As in chemical components are main factors influencing the ultra-thick steel plate for the hydrogen-contacting equipment. It was found that the embrittlement is caused by the grain boundary segregation of a trace amount of P, and that the elements Si and Mn do not cause the embrittlement itself but promote the embrittlement of P. The converter smelting is adopted, the contents of Sn, Sb and As in the molten steel are controlled to be low, and the Mn element promotes tempering embrittlement, but is beneficial to the hardenability of a steel plate to prevent ferrite from being generated, so that the Si and P elements are controlled to be low in component design, and the Mn element is properly higher; c is the most basic strengthening element in steel, improves the strength, but the toughness is also influenced by too high content of C, and the content of C is preferably controlled to be less than or equal to 0.14 percent; the Cr and Mo elements can remarkably improve the hardenability and high-temperature performance of the steel plate, and when the Cr and Mo are compositely reinforced, the Cr and Mo contents need to be maintained at the optimal value of mutual interaction. In addition, a proper amount of Al element is added into the steel, and deoxidation is carried out when the steel is tapped at the end point of the converter, so that oxide inclusions in the steel are mainly reduced, the generation of crystal fracture caused by increase of crack sources is avoided, and the temper brittleness is further reduced. In a word, the component design requirements of 14Cr1MoR with the thickness of 200mm and more than 200mm are met through reasonable component matching, wherein the contents of impurity elements such As P, S, O, N, H, As, Sn, Sb and the like have upper limit requirements and lower limit requirements without limitation, and are reduced As far As possible under the capacity of process equipment, so that the aims of pure steel and uniform mechanical property are fulfilled.
The thickness of the 14Cr1MoR (H) steel plate is 200mm and more than 200 mm;
the production method of the steel plate comprises the following steps:
(1) smelting: smelting molten steel by a converter, ensuring that the carbon of steel tapping is more than or equal to 0.05 percent and the P of steel tapping is less than or equal to 0.012 percent, feeding the molten steel into an LF refining furnace, ensuring the temperature of a ladle is more than or equal to 1600 ℃, carrying out slagging by adopting a large amount of slag, ensuring that the white slag holding time is controlled to be 15min, then carrying out vacuum treatment by a VD furnace, controlling the holding time at the pressure of less than or equal to 67Pa according to more than or equal to 20min, and after breaking vacuum, adding Si-Ca wires at one time according to 2.7-3.0 m/ton steel;
(2) die casting and casting: the soft argon blowing time is guaranteed to be more than or equal to 5min, after argon blowing is carried out until the temperature meets the requirement of the casting temperature, argon is closed, the casting is started after 5min of sedation, the casting is poured into a water-cooled ingot mold, the casting temperature is controlled according to T1+ (35-45 ℃), wherein T1 is the liquidus temperature;
(3) heating: carrying out warm feeding, warm cleaning and warm loading on the steel ingot, and stewing the steel for 1 hour, wherein in order to ensure that alloy elements are fully dissolved in a solid solution and austenite grains are fine, low-speed steel burning is adopted, the heat preservation temperature of a soaking pit is controlled to be 1200-1300 ℃, and the heat preservation time T is 13 min/cm;
(4) rolling and cooling control: the controlled rolling adopts two-stage rolling, wherein the first-stage rolling adopts high temperature, low speed and high reduction, the initial rolling temperature is 1000-1050 ℃, the final rolling temperature is more than 950 ℃, the single-pass reduction is 40-70 mm, the cumulative reduction rate is more than or equal to 70%, the steel airing thickness is plus (60-80) mm, the second-stage rolling adopts low reduction, the initial rolling temperature is less than 900 ℃, the final rolling temperature is less than or equal to 820 ℃, and the cumulative reduction rate is more than 45%; after rolling, adopting an ACC cooling process, cooling for multiple times at a red return temperature of less than 710 ℃, wherein the cooling speed is controlled to be 1-7 ℃/s, and the red return temperature is controlled to be 650-680 ℃; after high temperature, low speed, large pressure and process, the main structure of the steel plate after controlled rolling is ferrite plus pearlite, and the grain size is grade 5;
(5) slow cooling and heap cooling: the temperature of the steel plate entering the slow cooling pit is more than or equal to 500 ℃, and the cooling time in the pile is more than or equal to 72 hours;
(6) and (3) heat treatment: the heat treatment process adopts the process mode of normalizing (quick cooling), quenching and tempering, and the normalizing and heat-preserving temperature of the general steel grade is as follows: ac3+ (30-50) DEG C, finally determining that the normalizing temperature of 14Cr1MoR with the thickness of 200mm is 930 +/-10 ℃ by using a transformation point Ac3 empirical formula, wherein the normalizing and heat-preserving time is 2.2min/mm, the temperature of the steel plate after being discharged from the furnace is controlled to be 850-; quenching is carried out, the quenching temperature is 930 +/-10 ℃, the quenching heat preservation time is 2.4min/mm, water is rapidly fed after the quenching is discharged, the quenching water temperature is controlled within 25 ℃, and circulating water is started for 250m 3/h; ensuring the temperature of water entering to be above 860 ℃, and cooling the water for 30min to normal temperature; tempering at a higher temperature of 720 +/-10 ℃ for 4.5min/mm, and air-cooling after discharging, wherein the 720 ℃ tempering ensures that the structure after the simulated welding is not changed and ensures that the strength of the welding line is not reduced. The main structure of the steel plate obtained by the process modes of normalizing (quick cooling), quenching and tempering is a tempered bainite structure, and the grain size reaches 9 grades.
The conventional 14Cr1MoR heat treatment process method is a normalizing and tempering process route, under the condition that the alloy cost is not increased, through the normalizing (quick cooling) + quenching and tempering process route, the steel plate structure is a ferrite and upper bainite structure after the normalizing and quick cooling, the grains are refined, good grain size is provided for a subsequent 14Cr1MoR steel plate, and an ideal bainite structure is further obtained through quenching, so that the hydrogen 14Cr1MoR (H) steel plate with the ultimate thickness of 200mm can meet the mechanical property of removing stress by simulating postweld heat treatment at the high temperature of 690 ℃ and with the heat preservation of 26H, the high-temperature tensile property Rp0.2 at the temperature of 540 ℃ reaches 310MPa, the impact power at the temperature of 20 ℃ reaches more than 100J, the reached mechanical property index is far higher than the national standard, and the service performance, the mechanical property and the stability are all sharply changed.
The invention designs the chemical components of the steel plate by using Cr-Mo as a basic alloy element, reduces oxide inclusions in the steel by proper component design, smelting and casting processes, avoids increasing crack sources to cause the generation of intergranular fracture, further reduces the temper brittleness, and ensures that the temper embrittlement sensitivity coefficient J is (Si + Mn) ((P + Sn) × 10)4≤100PPm,(P+Sn)≤0.014%,X=(10P+5Sb+4Sn+As)×10-2Less than or equal to 10ppm so as to meet the actual mechanical property requirement of the steel plate, and particularly further improve the actual tempering embrittlement resistance and the high-temperature corrosion resistance of the steel.
The invention determines the influence mechanism of the 14Cr1MoR steel plate rolling process for the hydrogen-contacting equipment on the austenite grain size and uniformity, ensures the internal quality by utilizing the process of high temperature, low speed and large pressure, and finally completes the ultrasonic flaw detection requirement of the steel plate; the steel plate produced by the invention is subjected to a heat treatment process mode of normalizing (quick cooling), quenching and tempering, so that the mechanical properties of the steel plate after conventional and simulated postweld heat treatment can meet the following requirements: rp0.2>310MPa,Rm515-690MPa,A≥22%,-20℃KV2More than or equal to 100J, the J coefficient is less than or equal to 100PPm, the X coefficient is less than or equal to 10PPm, and the alloy has good hydrogen corrosion resistance and embrittlement resistanceAnd (4) performance.
According to the invention, through high-temperature tempering at 720 ℃, the difference between the strength of the welded joint after simulated welding and the strength of the steel plate is small, the stress of the welded joint is greatly reduced, and all mechanical properties of the whole workpiece are ensured to be within a required range.
Drawings
FIG. 1 shows the metallographic structure at the T/2 position after minimum simulated postweld of N + Q + T + PWHT in accordance with the present invention;
FIG. 2 is a metallographic structure 2mm below the rear surface of a minimum simulated post-weld N + Q + T + PWHT structure of the present invention;
FIG. 3 shows the metallographic structure at the position T/2 after maximum simulated postweld of N + Q + T + PWHT in accordance with the present invention;
FIG. 4 shows the metallographic structure 2mm below the rear surface of the maximum simulated post-weld N + Q + T + PWHT of the present invention.
Detailed Description
A14 Cr1MoR (H) steel plate for an ultra-large thickness high-pressure low-temperature container, namely a hydrogen-contacting device, comprises the following elements in percentage by mass: less than or equal to 0.14 percent of C, less than or equal to 0.60 percent of Si, 0.40 to 0.65 percent of MnP, less than or equal to 0.005 percent of S, less than or equal to 0.30 percent of Ni, less than or equal to 1.15 to 1.50 percent of Cr1, less than or equal to 0.10 percent of Cu, 0.45 to 0.65 percent of Mo0.025 to 0.040 percent of Al, less than or equal to 0.012 percent of As, less than or equal to 0.005 percent of Sn, less than or equal to 0.005 percent of Sb, less than or equal to 0.003 percent of O, less than or equal to 0.008 percent of.
The thickness of the 14Cr1MoR (H) steel plate is 200mm and more than 200 mm;
the production method of the steel plate comprises the following steps:
(1) smelting: smelting molten steel by a converter, ensuring that the carbon of steel tapping is more than or equal to 0.05 percent and the P of steel tapping is less than or equal to 0.012 percent, feeding the molten steel into an LF refining furnace, ensuring the temperature of a ladle is more than or equal to 1600 ℃, carrying out slagging by adopting a large amount of slag, ensuring that the white slag holding time is controlled to be 15min, then carrying out vacuum treatment by a VD furnace, controlling the holding time at the pressure of less than or equal to 67Pa according to more than or equal to 20min, and after breaking vacuum, adding Si-Ca wires at one time according to 2.7-3.0 m/ton steel;
(2) die casting and casting: the soft argon blowing time is guaranteed to be more than or equal to 5min, after argon blowing is carried out until the temperature meets the requirement of the casting temperature, argon is closed, the casting is started after 5min of sedation, the casting is poured into a water-cooled ingot mold, the casting temperature is controlled according to T1+ (35-45 ℃), wherein T1 is the liquidus temperature;
(3) heating: carrying out warm feeding, warm cleaning and warm loading on the steel ingot, and stewing the steel for 1 hour, wherein in order to ensure that alloy elements are fully dissolved in a solid solution and austenite grains are fine, low-speed steel burning is adopted, the heat preservation temperature of a soaking pit is controlled to be 1200-1300 ℃, and the heat preservation time T is 13 min/cm;
(4) rolling and cooling control: the controlled rolling adopts two-stage rolling, wherein the first-stage rolling adopts high temperature, low speed and high reduction, the initial rolling temperature is 1000-1050 ℃, the final rolling temperature is more than 950 ℃, the single-pass reduction is 40-70 mm, the cumulative reduction rate is more than or equal to 70%, the steel airing thickness is plus (60-80) mm, the second-stage rolling adopts low reduction, the initial rolling temperature is less than 900 ℃, the final rolling temperature is less than or equal to 820 ℃, and the cumulative reduction rate is more than 45%; after rolling, adopting an ACC cooling process, cooling for multiple times at a red return temperature of less than 710 ℃, wherein the cooling speed is controlled to be 1-7 ℃/s, and the red return temperature is controlled to be 650-680 ℃; after high temperature, low speed, large pressure and process, the main structure of the steel plate after controlled rolling is ferrite plus pearlite, and the grain size is grade 5;
(5) slow cooling and heap cooling: the temperature of the steel plate entering the slow cooling pit is more than or equal to 500 ℃, and the cooling time in the pile is more than or equal to 72 hours;
(6) and (3) heat treatment: the heat treatment process adopts the process mode of normalizing (quick cooling), quenching and tempering, and the normalizing and heat-preserving temperature of the general steel grade is as follows: ac3+ (30-50) DEG C, finally determining that the normalizing temperature of 14Cr1MoR with the thickness of 200mm is 930 +/-10 ℃ by using a transformation point Ac3 empirical formula, wherein the normalizing and heat-preserving time is 2.2min/mm, the temperature of the steel plate after being discharged from the furnace is controlled to be 850-; quenching is carried out, the quenching temperature is 930 +/-10 ℃, the quenching heat preservation time is 2.4min/mm, water is rapidly fed after the quenching is discharged, the quenching water temperature is controlled within 25 ℃, and circulating water is started for 250m 3/h; ensuring the temperature of water entering to be above 860 ℃, and cooling the water for 30min to normal temperature; tempering at a higher temperature of 720 +/-10 ℃ for 4.5min/mm, and air-cooling after discharging, wherein the 720 ℃ tempering ensures that the structure after the simulated welding is not changed and ensures that the strength of the welding line is not reduced. The main structure of the steel plate obtained by the process modes of normalizing (quick cooling), quenching and tempering is a tempered bainite structure, and the grain size reaches 9 grades.
The conventional 14Cr1MoR heat treatment process method is a normalizing and tempering process route, under the condition that the alloy cost is not increased, through the normalizing (quick cooling) + quenching and tempering process route, the steel plate structure is a ferrite and upper bainite structure after the normalizing and quick cooling, the grains are refined, good grain size is provided for a subsequent 14Cr1MoR steel plate, and an ideal bainite structure is further obtained through quenching, so that the hydrogen 14Cr1MoR (H) steel plate with the ultimate thickness of 200mm can meet the mechanical property of removing stress by simulating postweld heat treatment at the high temperature of 690 ℃ and with the heat preservation of 26H, the high-temperature tensile property Rp0.2 at the temperature of 540 ℃ reaches 310MPa, the impact power at the temperature of 20 ℃ reaches more than 100J, the reached mechanical property index is far higher than the national standard, and the service performance, the mechanical property and the stability are all sharply changed.
The invention designs the chemical components of the steel plate by using Cr-Mo as a basic alloy element, reduces oxide inclusions in the steel by proper component design, smelting and casting processes, avoids increasing crack sources to cause the generation of intergranular fracture, further reduces the temper brittleness, and ensures that the temper embrittlement sensitivity coefficient J is (Si + Mn) ((P + Sn) × 10)4≤100PPm,(P+Sn)≤0.014%,X=(10P+5Sb+4Sn+As)×10-2Less than or equal to 10ppm so as to meet the actual mechanical property requirement of the steel plate, and particularly further improve the actual tempering embrittlement resistance and the high-temperature corrosion resistance of the steel.
The invention determines the influence mechanism of the 14Cr1MoR steel plate rolling process for the hydrogen-contacting equipment on the austenite grain size and uniformity, ensures the internal quality by utilizing the process of high temperature, low speed and large pressure, and finally completes the ultrasonic flaw detection requirement of the steel plate; the steel plate produced by the invention is normalized (fast cooling) and quenchedThe heat treatment process mode of tempering ensures that the mechanical properties after conventional and simulated postweld heat treatment meet the following requirements: rp0.2>310MPa,Rm515-690MPa,A≥22%,-20℃KV2The J coefficient is not less than 100J, the J coefficient is not more than 100PPm, the X coefficient is not more than 10PPm, and the hydrogen corrosion resistance and the embrittlement resistance are good.
The 14Cr1MoR (H) steel plate with the element composition shown in the table 1 and used for the high-pressure low-temperature container with the thickness of 200mm is obtained through converter smelting, LF refining, vacuum refining, die casting pouring, heating, controlled rolling and controlled cooling, slow cooling and stack cooling and heat treatment.
TABLE 1200 mm-thick 14Cr1MoR (H) Steel sheet for high-pressure cryogenic vessel having respective component contents and temper embrittlement sensitivity coefficient (wt%)
And (3) performing mechanical property tests on the middle part of the alloy in batches, preparing tensile samples according to a GB/T228 metal standard material room temperature tensile test method, and performing room temperature X-direction tensile tests, Y-direction tensile tests and Z-direction tensile tests respectively, wherein the test results are shown in Table 2.
TABLE 214 tensile mechanical Properties at Room temperature of Cr1MoR (H)
Experimental results show that the steel plate produced by the method has good comprehensive mechanical properties, high strength, good toughness and excellent fatigue resistance, can completely meet the requirements of steel for hydrogen-contacting equipment, and is suitable for mass production. The X-direction, Y-direction and Z-direction normal temperature tensile properties of the steel plate for the test are higher than the technical requirements, and the data are stable, so that the tensile mechanical properties of the steel plate are proved to have no directionality.
Tensile samples were prepared according to the room temperature tensile test method of GB/T4338 metal standard materials and were respectively subjected to the tensile tests at 454 ℃, 482 ℃ and 540 ℃, and the results are shown in Table 3.
TABLE 314 Cr1MoR (H) high temperature tensile Strength test
Test temperature | Yield strength Rp0.2(MPa) | Tensile Strength Rm (MPa) |
454℃ | 356 | 521 |
482℃ | 341 | 494 |
540℃ | 310 | 383 |
The experimental result shows that the yield strength and tensile strength of the steel plate produced by the method have larger margin at the test temperature of 454 ℃, 482 ℃ and 540 ℃.
Preparing an impact sample according to a GB/T229 metal Charpy notched impact test method, KV2The impact test temperature is-20 ℃, and the sampling positions are at the positions 1.6mm, T/4, T/2 and 3T/4 from the upper surface and 1.6mm from the lower surface in the thickness direction of the steel plate. The results of the impact test are shown in Table 4.
TABLE 4 impact test results
Experimental results show that the AKV absorption power of the steel plate produced by the method at the temperature of-20 ℃ is far higher than the technical condition requirement, and the distribution dispersion is small, which shows that the steel plate is positioned in an upper platform area at the temperature of-20 ℃ and has very good impact toughness.
After the product is manufactured, a final post-weld heat treatment is performed to eliminate residual welding stress and diffused hydrogen, i.e., a simulated post-weld heat treatment process (min.
FIGS. 1-2 are schematic diagrams of the minimum simulated post-weld T/2 metallographic structure and the 2mm lower rear surface metallographic structure of the present invention after N + Q + T + PWHT, and FIGS. 3-4 are schematic diagrams of the maximum simulated post-weld T/2 metallographic structure and the 2mm lower rear surface metallographic structure of the present invention after N + Q + T + PWHT
And (3) performing heat treatment after minimum simulation welding: cooling the furnace at 690 +/-15 ℃ for 8h to 400 ℃ and taking out of the furnace for air cooling
Carrying out heat treatment after the maximum simulation welding: cooling the furnace at 690 +/-15 ℃ for 26h to 400 ℃ and taking out of the furnace for air cooling
TABLE 5 normalizing, tempering, and simulated post-weld mechanical properties
After the steel plate is subjected to N + T + PWHT, the crystal grains are fine, the grain size is 9.0 grade, the steel plate structure is uniform, and the structure bainite tempering structure is the main structure. Wherein "N" represents normalizing; "Q" means quenching; "T" represents tempering; "PWHT" means a simulated post-weld heat treatment.
From the above facts, it can be seen that: the steel plate obtained by the method has good conventional performance, good simulated low-temperature impact performance at the position of 1/2 ℃ below zero after welding, large allowance of each item, 100% of performance quality rate, flaw detection according to JB/T2970 plus 2004, 80% of first-class rate and 100% of third-class rate, and the expected effect is achieved.
Claims (4)
1. A14 Cr1MoR (H) steel plate for an ultra-large thickness high-pressure low-temperature container is characterized in that: the steel plate comprises the following components in percentage by mass: less than or equal to 0.14 percent of C, less than or equal to 0.60 percent of Si, 0.40 to 0.65 percent of MnP, less than or equal to 0.005 percent of S, less than or equal to 0.30 percent of Ni, less than or equal to 0.15 to 1.50 percent of Cr1, less than or equal to 0.10 percent of Cu, 0.45 to 0.65 percent of Mo0.025 to 0.040 percent of Al, less than or equal to 0.012 percent of As, less than or equal to 0.005 percent of Sn, less than or equal to 0.005 percent of Sb, less than or equal to 0.003 percent of O, less than or equal to 0.008 percent of N, less than or equal to 0.0002 percent of H, and; the steel plate is subjected to a heat treatment process of normalizing, quenching and tempering, and the obtained structure is mainly a bainite tempered structure.
2. The 14Cr1MoR (H) steel plate for the ultra-large thickness high-pressure low-temperature container as claimed in claim 1, wherein the thickness of the steel plate is 200mm and more than 200mm, and the high-temperature tensile property Rp0.2 at 540 ℃ reaches 310MPa, and the impact energy at-20 ℃ reaches more than 100J.
3. The 14Cr1MoR (H) steel plate for the ultra-large thickness high-pressure low-temperature container as claimed in claim 1, wherein the grain size of the steel plate can reach more than 9 grades.
4. The production method of the 14Cr1MoR (H) steel plate for the ultra-large thickness high-pressure low-temperature container, which is disclosed by the claim 1, comprises the steps of smelting, die casting, heating, controlled rolling and controlled cooling, slow cooling and stack cooling and heat treatment; the method is characterized in that:
(1) smelting: smelting molten steel by a converter, ensuring that the carbon of steel tapping is more than or equal to 0.05 percent and the P of steel tapping is less than or equal to 0.012 percent, feeding the molten steel into an LF refining furnace, ensuring the temperature of a ladle is more than or equal to 1600 ℃, slagging by adopting a large amount of slag, ensuring that the white slag holding time is controlled to be more than 15min, carrying out vacuum treatment by a VD furnace, controlling the holding time at the pressure of less than or equal to 67Pa according to more than or equal to 20min in the vacuum refining, and adding Si-Ca wires at one time according to 2.7-3.0 m/ton;
(2) die casting and casting: the soft argon blowing time is guaranteed to be more than or equal to 5 min; blowing argon until the temperature meets the casting temperature requirement, closing the argon, calming for 5min, then casting, and pouring into a water-cooled ingot mold, wherein the casting temperature is T1+ (35-45 ℃), and T1 is the liquidus temperature;
(3) heating: carrying out warm feeding, warm cleaning and warm loading on the steel ingot, stewing the steel for 1 hour, adopting low-speed steel burning, controlling the heat preservation temperature of a soaking pit at 1200-1300 ℃, and keeping the heat preservation time T at 13 min/cm;
(4) rolling and cooling control: two-stage rolling is adopted, wherein the first-stage rolling adopts high temperature, low speed and high pressure, the initial rolling temperature is 1000-1050 ℃, the final rolling temperature is more than 950 ℃, the single-pass reduction is 40-70 mm, the cumulative reduction rate is more than or equal to 70%, the airing steel thickness is plus (60-80) mm of the finished product thickness, the second-stage rolling adopts low pressure, the initial rolling temperature is less than 900 ℃, the final rolling temperature is less than or equal to 820 ℃, the cumulative reduction rate is more than 45%, an ACC cooling process is adopted after rolling, the temperature of red return is less than 710 ℃, the cooling speed is controlled at 1-7 ℃/s for multiple times, and the temperature of red return is controlled at 650 plus 680 ℃;
(5) slow cooling and heap cooling: the temperature of the steel plate entering the slow cooling pit is more than or equal to 500 ℃, and the cooling time in the pile is more than or equal to 72 hours;
(6) and (3) heat treatment: the heat treatment process adopts a process mode of normalizing (quick cooling), quenching and tempering, wherein the normalizing temperature is 930 +/-10 ℃, the normalizing heat preservation time is 2.2min/mm, the steel plate is quickly poured into water after being discharged from a furnace, the water inlet temperature is controlled at 850-550 ℃, and the steel plate is cooled by 200S (the temperature for returning red is controlled at 520-550 ℃); quenching at 930 + -10 deg.C for 2.4min/mm, rapidly introducing water after discharging to ensure the temperature of the introduced water is above 860 deg.C, controlling the temperature of quenching water within 25 deg.C, and starting circulating water for 250m3Water cooling for 30min to normal temperature; the tempering temperature is 720 +/-10 ℃, the tempering heat preservation time is 4.5min/mm, and the steel is cooled in air after being discharged.
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