CN114395733B - Production method of low-cost low-temperature high-strength steel 07MnNiVDR for container - Google Patents
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/002—Bainite
Abstract
The invention discloses a production method of low-cost low-temperature high-strength container steel 07MnNiVDR, wherein the thickness of the steel plate is less than or equal to 60mm, the internal structure is tempered sorbite and bainite, and the steel plate comprises the following chemical components: C. si, mn, P, S, als, ni, cr, mo and V, and the balance of Fe and residual elements, wherein the welding crack sensitivity coefficient Pcm is less than or equal to 0.21; the production method comprises heating, controlled rolling and controlled cooling, stacking cooling and tempering. The steel plate obtained by the invention has the thickness 1/4 position and the thickness 1/2 position, the mechanical property of the steel plate conforms to GB/T19189-2011 and the 5% strain aging impact property is ensured, the performance of the simulated postweld heat treatment at the temperature of 620 ℃ still conforms to the requirement of the GB/T19189-2011 standard, and the method specifically comprises the following steps: the yield strength is more than or equal to 490MPa, the tensile strength is 610-730MPa, the elongation is more than or equal to 17 percent, the transverse impact energy at minus 40 ℃ is more than or equal to 80J, and the transverse impact energy at minus 40 ℃ is more than or equal to 80J in 5 percent strain aging. Meanwhile, the controlled rolling and controlled cooling and tempering process is adopted to replace the traditional rolling, quenching and tempering processes, so that the quenching process is saved, the manufacturing period of the steel plate is favorably shortened and the production cost is reduced on the premise of ensuring the performance.
Description
Technical Field
The invention relates to the field of medium plate production, in particular to a production method of low-cost low-temperature high-strength steel 07MnNiVDR for a container.
Background
07MnNiVDR steel is widely used in industries such as petroleum, chemical industry, power station, and is mainly used for manufacturing equipment components such as reactor, heat exchanger, separator, spherical tank, oil gas tank, boiler drum, and has many advantages: the steel with low welding crack sensitivity has higher yield strength and tensile strength, excellent low-temperature toughness and the like. Therefore, the composite material becomes the most important structural material of the pressure container, and China is a large petroleum storage country, and the composite material has wide application range and large demand.
In the existing production method of the pressure vessel steel, in order to ensure the low-temperature performance of the steel plate, a quenching and tempering process is adopted in the steel plate heat treatment link, such as the Chinese patent CN110184531A, CN111363973B, which relatively increases the heat treatment cost of the steel plate and is not beneficial to market competition.
Disclosure of Invention
In order to solve the technical defects, the invention aims to provide a production method of low-cost low-temperature high-strength vessel steel 07MnNiVDR, which ensures the strength and low-temperature performance of a steel plate and greatly reduces the production cost.
In order to achieve the purpose, the invention adopts the technical scheme that: the production method of the low-cost low-temperature high-strength container steel 07MnNiVDR is characterized in that the thickness of a steel plate produced by the production method is less than or equal to 60mm, the internal structure is tempered sorbite and bainite, and the steel plate comprises the following chemical components in percentage by mass (unit, wt%): c:0.06-0.08%, si:0.15 to 0.25%, mn: 1.40-1.50%, P is less than or equal to 0.015%, s is less than or equal to 0.005%, als:0.015 to 0.040%, ni:0.3-0.5%, cr:0.2-0.3%, mo: 0.10-0.25%, V0.02-0.04%, and the balance Fe and residual elements;
welding crack sensitivity coefficient Pcm = C + si/30+ (Mn + Cu + Cr)/20 + Ni/60+ Mo/15+ V/10+5B (%). Is less than or equal to 0.21;
the production method of the low-cost low-temperature high-strength steel 07MnNiVDR for the container comprises the steps of heating, rolling and cooling control, cold stacking and tempering, and specifically comprises the following steps:
heating: the temperature of the preheating section is less than 1100 ℃, the temperature of the heating section is 1240-1260 ℃, the temperature of the soaking section is 1220-1240 ℃, and the heating coefficient is 10min/cm;
rolling and cooling control: two-stage rolling, wherein the initial rolling temperature of the first stage is more than 1000 ℃, the pass reduction is more than or equal to 20mm, the core grain structure of the steel billet can be fully refined, the thickness of the intermediate billet is more than 1.5 times of that of the finished steel plate, the intermediate billet enters an IC (integrated circuit) for rapid cooling, the roller speed is controlled at 0.4-1.0 m/s, and the temperature of red return is 870-900 ℃; the second stage is at the initial rolling temperature of more than 840 ℃ and the final rolling temperature of more than 780 ℃; after rolling, adopting a relaxation process, air-cooling the steel plate on a roller way for 40-60 s, then cooling the steel plate in ACC, wherein the water inlet temperature of the steel plate is 770-780 ℃, the roller speed is 0.4m/s, the cooling speed is 5-12 ℃/s, and the re-reddening temperature of the steel plate after water outlet is less than 300 ℃; it should be noted that, in order to solve the problem of mixed crystals, after rough rolling is finished, the billets enter an IC (integrated circuit) one by one for cooling, the purpose is to enable the central area of the billets to quickly enter a non-recrystallization area, and after finish rolling is finished, the steel plates are cooled and equalized in air on a roller way, so that the precipitation strengthening effect can be realized;
and (3) cooling in a heaped mode: after the steel plate is straightened, the steel plate enters a pit type slow cooling pit for heap cooling, the ambient temperature in the slow cooling pit is 300-400 ℃, and the tempering treatment is carried out after the heap cooling is carried out for 24-36 h;
tempering the method comprises the following steps: the tempering temperature is controlled according to 640-650 ℃, the total heating time is 3.0-4.0min/mm, and the steel is cooled to normal temperature after being discharged from the furnace.
The invention has the beneficial effects that: low-temperature steel burning is adopted in the heating process, and the crystal grains are controlled to be reduced in the austenite process of the original casting blank; the rolling controlled cooling process and the relaxation process are combined, the mixed crystal phenomenon is avoided, the relaxation process is adopted to ensure the precipitation strengthening effect and the uniform temperature effect of the alloy, the ACC is used for cooling the steel plate to be below 300 ℃, the tissue at the position with the thickness of 1/2 is ensured to be not different from the tissue at the position of 1/4, and the uniform and fine tempered sorbite and bainite tissue is obtained after tempering;
the controlled rolling and controlled cooling and tempering process adopted by the invention replaces the processes of rolling, quenching and tempering, can also achieve the effect of a heat treatment quenching process, and can ensure the mechanical property of a position with the thickness of 1/2;
the maximum thickness of the steel plate of the tempered sorbite and bainite tissues obtained by the method can reach 60mm;
the steel plate obtained by the invention has the thickness of 1/4 and the thickness of 1/2, the mechanical properties of the steel plate conform to GB/T19189-2011 and the 5% strain aging impact property is ensured, and the performance of the simulated postweld heat treatment at 620 ℃ still conforms to the mechanical properties in the GB/T19189-2011 standard, and the steel plate specifically comprises the following components: the yield strength is more than or equal to 490MPa, the tensile strength is 610-730MPa, the elongation is more than or equal to 17 percent, the transverse impact energy at minus 40 ℃ is more than or equal to 80J, and the transverse impact energy at minus 40 ℃ is more than or equal to 80J in 5 percent strain aging.
Drawings
The technical features of the present invention will be further described with reference to the accompanying drawings and embodiments.
FIG. 1 shows the metallographic structure (metallographic microscope X200) of the surface layer of a steel sheet having a thickness of 60mm obtained in example 2 of the present invention.
FIG. 2 shows a metallographic structure (metallographic microscope X200) at 1/4 of a steel plate having a thickness of 60mm obtained in example 2 of the present invention.
FIG. 3 shows the metallographic structure (metallographic microscope X200) at 1/2 of a steel plate having a thickness of 60mm obtained in example 2 of the present invention.
FIG. 4 shows a metallographic structure (metallographic microscope X200) of a simulated postweld heat-treated surface layer of a 60mm thick steel plate obtained in example 2 of the present invention.
FIG. 5 shows the metallographic structure (metallographic microscope X200) at 1/4 of the simulated postweld heat treatment of a 60mm thick steel plate obtained in example 2 of the present invention.
FIG. 6 shows a metallographic structure (metallographic microscope X200) at 1/2 of a simulated postweld heat treatment of a 60mm thick steel plate obtained in example 2 of the present invention.
Detailed Description
Through the technical scheme, the steel 07MnNiVDR for the low-cost low-temperature high-strength container is prepared, and the preparation method is realized through the following multiple examples:
example 1
(1) Designing components: in the technical scheme, the steel plate 07MnNiVDR for the high-strength vacuum vessel with the thickness of below 60mm contains the following chemical components in percentage by mass (unit, wt%): c:0.07%, si:0.20%, mn:1.42%, P0.012%, s 0.003%, als:0.020%, ni:0.35%, cr:0.22%, mo:0.15%, V:0.025, the balance Fe and residual elements, and the crack sensitivity coefficient Pcm =0.18.
(2) The heating process comprises the steps of producing a finished steel plate with the thickness of 15mm by adopting a billet with the section of 210mm, controlling the temperature of a preheating section at 1050 ℃, controlling the temperature of a secondary heating section at 1250 ℃, controlling the temperature of a soaking section at 1230 ℃, and heating for 210min.
(3) Rolling and cooling control, wherein the initial rolling temperature is 1100 ℃, in order to realize the core grain structure refinement of the billet, the single-pass reduction in the rough rolling link is 30mm, the airing thickness of the intermediate billet is 50mm, the IC process adopts the speed of 1.0m/s, and the temperature of the IC after red returning is 925 ℃; the finish rolling start temperature is controlled to be 850 ℃, the finish rolling temperature is 790 ℃, after finish rolling is finished, the steel plate starts to enter water after swinging for 40s on a roller way, the water entering temperature is 776 ℃, the roller speed is 0.4m/s, and the water outlet temperature of the steel plate is 180 ℃.
(4) And (3) cooling in a heaped mode: and after the steel plate is straightened, quickly unloading the steel plate to a slow cooling pit, and carrying out stack cooling, wherein the environment temperature of the slow cooling pit is 360 ℃, and carrying out tempering treatment after 24 stack cooling.
(5) Tempering: the steel plate rotating roller bottom type normalizing furnace has the temperature controlled according to 645 ℃ and the total heating time of 60min; and (5) air cooling after discharging.
Example 2
(1) Designing components: in the technical scheme, the steel plate 07MnNiVDR for the high-strength vacuum vessel with the thickness of below 60mm contains the following chemical components in percentage by mass (unit, wt%): c:0.08%, si:0.25%, mn:1.45%, P0.012%, s 0.003%, als:0.022%, ni:0.36%, cr:0.23%, mo:0.17%, V:0.030, and the balance Fe and residual elements, and the crack sensitivity coefficient Pcm =0.19.
(2) The heating process comprises adopting 300mm section steel billet to produce 60mm thick finished steel plate, controlling preheating section temperature at 1040 deg.C, secondary heating temperature at 1260 deg.C, soaking section temperature at 1250 deg.C, and heating time at 300min.
(3) Rolling and cooling control, wherein the initial rolling temperature is 1108 ℃, in order to realize the core grain structure refinement of the steel billet, the single-pass reduction in the rough rolling link is 25mm, the airing thickness of the intermediate billet is 100mm, the IC process adopts the speed of 0.4m/s, and the post-IC red return temperature is 895 ℃; the finish rolling start temperature is controlled at 841 ℃, the finish rolling temperature is 782 ℃, water is fed after the finish rolling is finished and the roller table swings for 55s, the water feeding temperature is 767 ℃, the roller speed is 0.4m/s, and the steel plate water outlet temperature is 252 ℃.
(4) And (3) cooling in a stacking manner: and (3) after the steel plate is straightened, quickly taking the steel plate out of the line to a slow cooling pit, carrying out stack cooling, wherein the environment temperature of the slow cooling pit is 350 ℃, and carrying out tempering treatment after the stack cooling is carried out for 36 hours.
(5) Tempering: the steel plate rotating roller bottom type normalizing furnace has the advantages that the temperature in the furnace is controlled according to 645 ℃, the total heating time is 240min, and air cooling is carried out after the steel plate rotating roller bottom type normalizing furnace is taken out of the furnace.
Example 3
(1) Designing components: in the technical scheme, the steel plate 07MnNiVDR for the high-strength flaw detection pressure vessel with the thickness of less than 60mm contains the following chemical components in percentage by mass (unit, wt%): c:0.08%, si:0.25%, mn:1.41%, P0.011%, s 0.003%, als:0.025%, ni:0.32%, cr:0.26%, mo:0.15%, V:0.029, and the balance Fe and residual elements, and the crack sensitivity coefficient Pcm =0.19.
(2) The heating process comprises adopting 300mm section steel billet to produce 38mm thick steel plate, controlling preheating section temperature at 1038 deg.C, heating temperature at 1255 deg.C, heating section temperature at 1247 deg.C, and heating time at 300min.
(3) Rolling and cooling are controlled, wherein the initial rolling temperature is 1110 ℃, in order to realize the core grain structure refinement of the steel billet, the single-pass reduction in the rough rolling link is 27mm, the steel airing thickness of the intermediate billet is controlled to be 80mm, the IC process adopts the speed of 0.5m/s, and the IC after-red temperature is 879 ℃; the finish rolling start temperature is controlled to be 852 ℃, the finish rolling temperature is 791 ℃, water starts to enter after the finish rolling is finished and swings for 50s on a roller way, the water entering temperature is 771 ℃, the roller speed is 0.4m/s, and the post-water temperature of the steel plate is 221 ℃.
(4) And (3) cooling in a stacking manner: and (3) after the steel plate is straightened, quickly taking the steel plate out of the cooling pit, carrying out stack cooling, wherein the ambient temperature of the cooling pit is 391 ℃, and carrying out tempering treatment after the stack cooling is carried out for 36 hours.
(5) Tempering: the steel plate rotating roller bottom type normalizing furnace has the advantages that the temperature in the furnace is controlled according to 645 ℃, the total heating time is 152min, and air cooling is carried out after the steel plate rotating roller bottom type normalizing furnace is taken out of the furnace.
The steel plate obtained in the embodiment is subjected to mechanical property detection according to GB19189-2011, and specific indexes are shown in the following table.
Metallographic structure detection is respectively carried out on the surface layer, the thickness of 1/4 and the thickness of 1/2 of a steel plate with the thickness of 60mm obtained in the embodiment 2 of the invention, as shown in the attached drawings 1-3, wherein the internal structure in the attached drawing 1 is tempered sorbite + bainite, the grain size is grade 10, the internal structure of the steel plate in the attached drawing 2 is tempered sorbite + bainite, the grain size is grade 9.5, and the internal structure of the steel plate in the attached drawing 3 is tempered sorbite + bainite, and the grain size is grade 9.
The 60mm thick steel plate obtained in example 2 of the present invention was subjected to simulated post-weld heat treatment, and the metallographic structure of the surface layer, 1/4 thickness and 1/2 thickness of the steel plate was examined, respectively, as shown in FIGS. 4 to 6.
According to the embodiment of the invention, the controlled rolling and controlled cooling and tempering process is adopted to replace the rolling, quenching and tempering processes, the effect of the heat treatment and quenching process can be achieved, the thickness 1/4 position and the thickness 1/2 position of the obtained steel plate are obtained, the mechanical property of the steel plate conforms to GB/T19189-2011 and 5% strain aging impact property is ensured, the performance of the heat treatment after the simulation welding at the temperature of 620 ℃ still conforms to the mechanical property in the GB/T19189-2011 standard, and the controlled rolling and controlled cooling and tempering process specifically comprises the following steps: the yield strength is more than or equal to 490MPa, the tensile strength is 610-730MPa, the elongation is more than or equal to 17 percent, the transverse impact energy at minus 40 ℃ is more than or equal to 80J, and the transverse impact energy at minus 40 ℃ is more than or equal to 80J in 5 percent strain aging.
Although the present invention has been described in detail with reference to the above embodiments, it should be understood by those skilled in the art that various changes may be made and equivalents may be substituted without departing from the true spirit and scope of the invention as defined in the claims.
Claims (1)
1. A production method of low-cost low-temperature high-strength container steel 07MnNiVDR is characterized by comprising the following steps: the thickness of the steel plate produced by the production method is less than or equal to 60mm, the internal structure is tempered sorbite and bainite, and the steel plate comprises the following chemical components in percentage by mass (unit, wt%): c:0.06-0.08%, si:0.15 to 0.25%, mn: 1.40-1.50%, P is less than or equal to 0.015%, S is less than or equal to 0.005%, als:0.015 to 0.040%, ni:0.3-0.5%, cr:0.2-0.3%, mo: 0.10-0.25%, V0.02-0.04%, and the balance Fe and residual elements;
welding crack sensitivity coefficient Pcm = C + Si/30+ (Mn + Cu + Cr)/20 + Ni/60+ Mo/15+ V/10+5B (%). Is less than or equal to 0.21;
the production method of the low-cost low-temperature high-strength steel 07MnNiVDR for the container comprises the steps of heating, rolling and cooling control, cold stacking and tempering, and specifically comprises the following steps:
heating: the temperature of the preheating section is less than 1100 ℃, the temperature of the heating section is 1240-1260 ℃, the temperature of the soaking section is 1220-1240 ℃, and the heating coefficient is 10min/cm;
rolling and cooling control: two-stage rolling, wherein the initial rolling temperature of the first stage is more than 1000 ℃, the pass reduction is more than or equal to 20mm, the core grain structure of the billet can be fully refined, the thickness of the intermediate billet is more than 1.5 times of that of the finished steel plate, the intermediate billet is rapidly cooled by entering an IC, the rolling speed is controlled at 0.4-1.0 m/s, and the temperature of red return is 870-900 ℃; the second stage is at the initial rolling temperature of more than 840 ℃ and the final rolling temperature of more than 780 ℃; after rolling is finished, adopting a relaxation process, air-cooling the steel plate on a roller way for 40-60 s, then cooling the steel plate by ACC, wherein the water inlet temperature of the steel plate is 770-780 ℃, the roller speed is 0.4m/s, the cooling speed is 5-12 ℃/s, and the reddening temperature of the steel plate after water outlet is less than 300 ℃; it should be noted that, in order to solve the problem of mixed crystals, after rough rolling, the billets enter the IC one by one for cooling, and the purpose is to make the central area of the billet enter the non-recrystallization area quickly, and after finish rolling, the steel plate is air-cooled and uniform-temperature on the roller way, so that the precipitation strengthening effect can be realized;
and (3) cooling in a stacking manner: after the steel plate is straightened, the steel plate enters a pit type slow cooling pit for heap cooling, the ambient temperature in the slow cooling pit is 300-400 ℃, and the tempering treatment is carried out after the heap cooling is carried out for 24-36 h;
tempering: the tempering temperature is controlled according to 640-650 ℃, the total heating time is 3.0-4.0min/mm, and the steel is cooled to normal temperature after being discharged from the furnace.
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