CN114000035A - Production method of atmospheric corrosion resistant high-strength extra-thick Q390GNH steel plate - Google Patents
Production method of atmospheric corrosion resistant high-strength extra-thick Q390GNH steel plate Download PDFInfo
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
- C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
- C21C7/04—Removing impurities by adding a treating agent
- C21C7/072—Treatment with gases
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21C—PROCESSING OF PIG-IRON, e.g. REFINING, MANUFACTURE OF WROUGHT-IRON OR STEEL; TREATMENT IN MOLTEN STATE OF FERROUS ALLOYS
- C21C7/00—Treating molten ferrous alloys, e.g. steel, not covered by groups C21C1/00 - C21C5/00
- C21C7/10—Handling in a vacuum
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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
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
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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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- 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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- 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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- 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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
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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
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
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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
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
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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
- C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
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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
- C21D2211/005—Ferrite
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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
- C21D2211/008—Martensite
Abstract
The invention discloses a production method of an atmospheric corrosion resistant high-strength extra-thick Q390GNH steel plate, wherein the thickness of the steel plate is 120mm, and the steel plate contains the following chemical components: C. si, Mn, P, S, Nb, Cr, Ni, Cu, Ti, B and the balance of Fe and residual elements, the carbon equivalent Ceq is less than or equal to 0.42, the welding crack sensitivity index Pcm is less than or equal to 0.20, and the production method of the steel plate comprises the following steps: the continuous casting, controlled rolling and controlled cooling, heap cooling and heat treatment process adopts a casting blank with the thickness of 450mm to produce a steel plate with the thickness of 120mm, fully crushes dendritic crystals in the steel by matching with a large reduction of 40-50mm and a hard shell rolling method, and matches with repeated cooling, and finally the grains after recrystallization become fine, so that ideal martensite and ferrite tissues are obtained, and the advantages of corrosion resistance, toughness, low yield ratio, good welding performance and the like of the steel plate are realized.
Description
Technical Field
The invention relates to the technical field of wide and thick plate production, in particular to a production method of an atmospheric corrosion resistant high-strength extra-thick Q390GNH steel plate.
Background
The weather-resistant steel is used as a new-generation advanced steel material, the atmospheric corrosion resistance is 2-5 times that of common carbon steel, and the longer the service time is, the more prominent the corrosion resistance is. The steel structure has the characteristics of rust resistance, coating-free property, thinning and consumption reduction, labor saving and energy saving, and the like, can be applied to steel structures of buildings, vehicles, bridges, towers and the like which are exposed to the atmosphere for a long time and can also be used for manufacturing structural members of containers, railway vehicles, oil derricks, harbor buildings, oil extraction platforms and the like.
The existing Q390 weathering steel has high welding crack sensitivity, and the problems of high difficulty, special requirements on process equipment, unstable quality, long process route and the like exist in the production of crack-arresting type super-thick high-performance steel plates in the prior art.
Disclosure of Invention
The invention aims to provide a production method of an atmospheric corrosion resistant high-strength extra-thick Q390GNH steel plate, which effectively reduces the production difficulty and the production cost, has short process route, and can produce the steel plate with stable quality and higher preparation efficiency.
In order to achieve the purpose, the invention adopts the technical scheme that: a production method of an atmospheric corrosion resistant high-strength super-thick Q390GNH steel plate is disclosed, wherein the thickness of the Q390GNH steel plate is 120mm, and the steel plate comprises the following chemical components in percentage by mass (unit, wt%): 0.04-0.07% of C, less than or equal to 0.35% of Si, 1.0-1.40% of Mn, 0.090-0.110% of P, less than or equal to 0.002% of S, 0.50-0.65% of Cr, 0.40-0.50% of Ni, 0.030-0.040% of Nb, 0.30-0.45% of Cu, less than or equal to 0.015% of Ti, less than or equal to 0.0006% of B, Fe and residual elements as the others, the carbon equivalent Ceq is less than or equal to 0.42, and the welding crack sensitivity index Pcm is less than or equal to 0.20;
the production method of the Q390GNH steel plate comprises the following steps: KR molten iron pretreatment, converter smelting, argon blowing treatment, LF refining, VD refining, continuous casting, heating, controlled rolling and controlled cooling, heap cooling and heat treatment, wherein
In the continuous casting process, casting a casting blank with the thickness of 450mm, controlling the superheat degree of a tundish at 10-15 ℃, the pulling speed at 0.70-0.75m/min and the specific water amount at 0.85L/kg, controlling electromagnetic stirring according to parameters 900A and 5Hz, stirring for 30s each time, stopping stirring for 3s, then continuing stirring for 30s, and circulating according to the stirring mode;
in controlled rolling and controlled cooling, high-temperature low-speed large reduction is adopted and combined with 3 times of high-pressure water hardening surface opening, the initial rolling temperature is controlled to be 1000-1060 ℃, the reduction of each time is 40-50mm, the rotating speed of a roller is less than or equal to 20rad/min, so that the rolling force permeates into the core part of a casting blank, the final rolling temperature is 950-1020 ℃, SUPIC-L cooling is adopted after rolling is finished, the cooling is repeated for 2-4 times, the cooling speed is controlled to be 10-20 ℃/s, and the temperature of red returning is controlled to be 580-600 ℃;
in the heap cooling process, the temperature of the steel plate entering the slow cooling pit is not lower than 450 ℃, the heap cooling time is not less than 48 hours, the environment temperature in the slow cooling pit is controlled at 300-500 ℃, the heap cooling temperature and the self-tempering effect of the steel plate are ensured, and the full diffusion and overflow of H in the steel are facilitated;
in the heat treatment process, a heat treatment process of primary quenching, secondary quenching and tempering is adopted to obtain a finished steel plate with 10% -15% of ferrite and 85% -90% of martensite composite structure, wherein the primary quenching is 905-925 ℃, the heat preservation time is 2.1-2.3min/mm, the secondary quenching is 790-860 ℃, the heat preservation time is 1.5-2.3min/mm, the tempering temperature is 650-680 ℃, and the heat preservation time is 3-4 min/mm.
The steel plate obtained by the production method has the following beneficial effects:
1) a casting blank with the thickness of 450mm is adopted to produce a steel plate with the thickness of 120mm, the large reduction of 40-50mm and a hard shell rolling method are matched to fully crush dendritic crystals in the steel, the larger the deformation degree is, the larger the driving force and the density of a nucleation area are, the repeated cooling is matched after the rolling is finished, and finally, grains after recrystallization become fine, so that an ideal structure is obtained.
2) Has good obdurability and lower yield ratio. The structure of the steel plate in which martensite and ferrite are interlaced with each other is similar to a "fiber-reinforced composite material". Martensite existing on the grain boundary in the structure plays a role of strengthening the grain boundary, and is very beneficial to improving the performance. The fibrous composite structure makes it difficult for dislocations to pass through the grain boundaries and to accumulate at the interface between ferrite and martensite, thereby causing the stress required for martensitic deformation. The martensite has a dislocation subgrain structure, high strength and good toughness, so that the martensite can bear a certain amount of deformation without fracture. And the ferrite phase interface and the martensite phase interface are highly coherent, no brittle carbide is formed on the interface, the load is improved, and no local stress concentration exists. Meanwhile, the soft ferrite phase reduces the yield ratio, can also prevent the expansion of cracks and further improves the impact toughness of the steel.
3) Has higher fatigue limit resistance and stress corrosion resistance, because the martensite internal high-density dislocation and a large amount of ferrite/martensite grain boundary can effectively prevent the crack from expanding.
4) Moderate hardenability and good welding performance. Because the steel plate has a lower yield ratio, the steel can be plastically deformed when the yield ratio is lower than the fracture stress, so that the stress concentration on welding spot accessories is reduced, and the weldability is improved.
Detailed Description
The techniques and features of the present invention are further described below by way of examples.
The invention discloses a production method of an atmospheric corrosion resistant high-strength super-thick Q390GNH steel plate, wherein the thickness of the steel plate is 120mm, and the steel plate comprises the following chemical components in percentage by mass (unit, wt%): c: 0.04 to 0.07, Si: less than or equal to 0.35, Mn: 1.0 to 1.40, P: 0.090-0.110, S is less than or equal to 0.002, Cr: 0.50 to 0.65, Ni: 0.40 to 0.50, Nb: 0.030 to 0.040, Cu: 0.30-0.45 percent of Ti, less than or equal to 0.015 percent of B, less than or equal to 0.0006 percent of B, Fe and residual elements as the others, the carbon equivalent Ceq is less than or equal to 0.42, and the welding crack sensitivity index Pcm is less than or equal to 0.20.
The steel plate is realized according to the following steps:
KR molten iron pretreatment: pre-slagging and post-slagging of molten iron arriving at a station are required, the thickness of a liquid level slag layer is guaranteed to be less than or equal to 20mm, molten iron S is guaranteed to be less than or equal to 0.003 percent after being stirred and desulfurized by KR, the desulfurization period is guaranteed to be less than or equal to 21min, and the desulfurization temperature drop is guaranteed to be less than or equal to 20 ℃;
b. smelting in a converter: the converter-entering scrap steel must adopt dry and soil-free rolled steel leftover materials and must not be doped with any other scrap steel or bread iron; the S content of the molten iron fed into the furnace is required to be less than or equal to 0.015 percent, and the temperature of the molten iron is required to be more than or equal to 1250 ℃; controlling tapping P: the smelting process is carried out in advance, the converter is turned over, a high-tension complementary blowing method is adopted for controlling, the first-time turning temperature is controlled to be 1550-1600 ℃, and slag is turned over as much as possible during each converter turning; controlling the tapping temperature to be 1600-1630 ℃; the tapping needs to be carried out at the same time P before tapping, and the tapping P is ensured to be less than or equal to 0.008 percent; slag is strictly prevented in the tapping process, and molten steel can not be completely discharged in order to avoid slag; adding 200Kg of lime into a steel ladle in the tapping process; controlling tapping C: controlling the tapping C to be 0.05-0.08%, and simultaneously, not exceeding 2 times of point blowing; the molten steel is required to be hoisted to LF for refining 15min after the molten steel is treated in the argon station, so that the serious nitrogen increase of the molten steel caused by long LF refining time due to long waiting time and large temperature drop is avoided;
c. argon blowing treatment: adding an aluminum wire into an argon station at one time, wherein strong argon blowing is required to be performed for 3min in the argon station, the flow rate is 200-500NL/min, the diameter of a naked eye on the steel liquid surface is controlled to be 300-500 mm, and the temperature from the argon station is not lower than 1570 ℃;
and d, LF refining: refining requires that the white slag is manufactured and simultaneously the temperature is rapidly raised in a heating process, and the slag manufacturing requirement is as follows: heating the slag to be yellow-white and slightly thin; secondly, heating the slag to form yellow-white, light gray and light caking; thirdly, heating the mixture to be offwhite, foamed and slightly diluted, and ensuring good fluidity of the heated final slag; lifting the electrode when the temperature reaches more than 1580 ℃, sampling and testing components, and drawing an aluminum wire 950m in an LF off-station manner;
e.VD refining: standing at 1668 deg.C, pre-pumping for 5min to vacuum, maintaining pressure for 20min, breaking, soft blowing for 5min, standing at 1586 deg.C, and determining hydrogen content to be 0.79 ppm; the pressure maintaining time is required to be more than or equal to 20min under the vacuum degree of 67Pa, and the molten steel turnover effect is required to be good in the pressure maintaining process; VD leaving-station temperature: 1570-1575 ℃; after the molten steel is broken empty and before leaving the station, a sample is added for gas analysis and high-power detection; the oxygen content in the steel can be reduced from 100X 10-6 to 20X 10-6; the sulfur content can be reduced from 0.01 percent to below 0.0015 percent, and the average desulfurization rate is about 84 percent; degassing for 20-25 min, wherein the hydrogen content of the molten steel can reach 2 x 10 < -6 >, the N content fluctuation is (30-45) x 10 < -6 >, and the detected gas content is basically stable within the range of [ H ] less than or equal to 2ppm, total [ O ] less than 20ppm and [ N ] less than 45 ppm;
f. continuous casting: the bulging amount of the casting blank is controlled, and the center segregation of the casting blank can be effectively reduced. The belly amount of the casting blank is directly related to the thickness of the blank shell, the distance between the two cooling zone rollers and the hydrostatic pressure of molten steel. Therefore, the small roll diameter is adopted, the accurate radian is ensured, and the secondary cooling water parameters are suitable, so that the bulging amount of the billet can be reduced, and the center segregation of the casting blank is further reduced; the control of the superheat degree of molten steel and the withdrawal speed in the casting process is a main means for controlling the growth of columnar crystals. The casting speed is too fast in the casting process, the higher the superheat degree of the molten steel is, the more developed the columnar crystals are, and the generation ratio is higher. Therefore, the growth of columnar crystals is strictly controlled, the formation proportion of isometric crystals is promoted, the overhigh pouring temperature and the overhigh blank drawing speed are avoided in the production process, the production rhythm is reasonably allocated, and the uniformity of the pouring temperature and the process stability are ensured. Therefore, the condition of casting machine equipment is ensured to be good before steel casting, the superheat degree of the tundish is 10-15 ℃, the drawing speed is 0.70-0.75m/min, and the specific water amount is as follows: 0.85L/kg, electric stirring: 900A, 5Hz, 30s-3s-30 s.
g. Heating: according to the metallurgical principle, casting blanks have center segregation with different degrees, in order to improve the center segregation and reduce the comprehensive quality hazard of the segregation to steel, the heating link of the casting blank needs to ensure the heating temperature and sufficient heating time, so that alloy elements at the segregation parts are fully diffused and homogenized; when the heating temperature is lower than 1000 ℃, the carbonitride small particles formed by Nb and Ti microalloy elements are taken as second phase particles, are dispersed and distributed in grain boundaries and crystal interiors, have a pinning effect on austenite grain boundaries, block the migration of the austenite grain boundaries, and can effectively prevent the growth of the austenite grains so that the austenite grains grow slowly. The mixed crystal phenomenon at 1050 ℃ is caused by that the solid solution amount of Nb and Ti microalloy elements is increased along with the increase of the heating temperature, so that fine carbonitride is gradually reduced, the pinning effect on austenite grain boundaries is weakened, a part of grains obtain coarse grains in size in a swallowing mode, namely, the grains are abnormally grown, and undissolved second phase grains continue to pin the austenite grain boundaries, so that the obvious mixed crystal phenomenon is caused. When the heating temperature is higher than 1050 ℃, the carbo-nitrides of Nb and Ti are further reduced, the pinning effect on austenite crystal boundary is greatly weakened, atoms at the crystal boundary in the steel are easy to migrate and diffuse across the interface, and the crystal grains begin to grow rapidly. The steel sintering temperature is 1220 ℃, the steel sintering time is 11min/cm, the sufficient solid solution of the microalloying elements in an austenite zone is ensured, and the excessive coarsening of crystal grains is avoided.
h. Rolling and cooling control: in the cogging stage, a high-temperature low-speed high-pressure process is adopted to fully crush dendritic crystals in steel, the larger the deformation degree is, the larger the driving force and density of a nucleation region are, and the finer the crystal grains become after repeated recrystallization. The rolling is carried out by adopting a mode of high temperature, low speed and large pressure reduction in the rolling process, the requirement on the capability of a rolling mill is higher, if the capability of the rolling mill is small, the large pressure reduction cannot be realized, so that the rolling force cannot permeate into the core, the tissue unevenness in the thickness direction of the steel plate is easy to cause, and the effect of pressing residual defects in casting cannot be realized, thereby directly influencing the impact toughness and the flaw detection quality of the finished steel plate, therefore, a cogging process is adopted, the high temperature, low speed and large pressure reduction is adopted in the cogging process and combined with 3 times of high pressure water hardening surface, the cogging temperature is controlled at 1000-, after rolling, SUPIC-L cooling is adopted, and the cooling is repeated for 2-4 times, wherein the cooling speed is controlled to be 10-20 ℃/s, and the temperature for returning red is controlled to be 580-600 ℃.
i. And (3) cooling in a heaped mode: stacking slow cooling temperature is not lower than 450 ℃, meanwhile, recycled heating air is introduced into the slow cooling pit, and the heap cooling time is not less than 48 hours, so that the heap cooling temperature and the self-tempering effect of the steel plate are ensured, and the H in the steel is favorably fully diffused and overflowed;
j. and (3) heat treatment: the common low-alloy high-strength steel strengthens a matrix through controlled rolling and cooling and solute atom solid solution strengthening, and the microalloyed steel adopting the two-phase zone heat treatment process can obtain a composite structure of a soft ferrite phase and a hard phase, and has the advantages of low yield ratio, good strength and toughness matching, high initial work hardening rate and the like. The temperature is maintained at 905-925 ℃ for the first time, 2.1-2.3min/mm for the heat preservation time, 790-860 ℃ for the second time, 1.5-2.3min/mm for the heat preservation time, 650-680 ℃ for the tempering temperature and 3-4min/mm for the heat preservation time.
Examples
Through KR molten iron pretreatment, converter smelting, argon blowing treatment, LF refining, VD refining, continuous casting, heating, controlled rolling and controlled cooling, heap cooling, heat treatment and other processes, the 120mm super-thick atmospheric corrosion resistant high-strength steel plate Q390GNH with the chemical components shown in the following table 1 is obtained, wherein all process parameters and mechanical properties are shown in the following tables 1 and 2.
Chemical composition (Wt%) of Q390GNH of table 1120 mm extra-thick atmospheric corrosion resistant high-strength steel plate
Mechanical properties of Q390GNH (high strength steel plate Q390 GNH) with surface 2120 mm extra thickness and atmospheric corrosion resistance
The steel plate produced by the method meets the design requirements.
The above description is only a preferred embodiment of the present invention, and the above specific embodiments are not intended to limit the present invention, and modifications, modifications or equivalents thereof, which may occur to those skilled in the art, are included within the scope of the present invention.
Claims (1)
1. A production method of an atmospheric corrosion resistant high-strength extra-thick Q390GNH steel plate is characterized by comprising the following steps: the thickness of the Q390GNH steel plate is 120mm, and the steel plate comprises the following chemical components in percentage by mass (unit, wt%): 0.04-0.07% of C, less than or equal to 0.35% of Si, 1.0-1.40% of Mn, 0.090-0.110% of P, less than or equal to 0.002% of S, 0.50-0.65% of Cr, 0.40-0.50% of Ni, 0.030-0.040% of Nb, 0.30-0.45% of Cu, less than or equal to 0.015% of Ti, less than or equal to 0.0006% of B, Fe and residual elements as the others, the carbon equivalent Ceq is less than or equal to 0.42, and the welding crack sensitivity index Pcm is less than or equal to 0.20;
the production method of the Q390GNH steel plate comprises the following steps: KR molten iron pretreatment, converter smelting, argon blowing treatment, LF refining, VD refining, continuous casting, heating, controlled rolling and controlled cooling, stacking cooling and heat treatment,
in the continuous casting process, casting blanks with the thickness of 450mm are poured, the superheat degree of the tundish is 10-15 ℃, the pulling speed is 0.70-0.75m/min, the specific water amount is 0.85L/kg, electromagnetic stirring is controlled according to parameters of 900A and 5Hz, stirring is stopped for 3s every time for 30s, then stirring is continued for 30s, and the stirring is circulated according to the stirring mode;
in controlled rolling and controlled cooling, high-temperature low-speed large reduction is adopted and combined with 3 times of high-pressure water hardening surface opening, the initial rolling temperature is controlled to be 1000-1060 ℃, the reduction of each time is 40-50mm, the rotating speed of a roller is less than or equal to 20rad/min, so that the rolling force permeates into the core part of a casting blank, the final rolling temperature is 950-1020 ℃, SUPIC-L cooling is adopted after rolling is finished, the cooling is repeated for 2-4 times, the cooling speed is controlled to be 10-20 ℃/s, and the temperature of red returning is controlled to be 580-600 ℃;
in the heap cooling process, the temperature of the steel plate entering the slow cooling pit is not lower than 450 ℃, the heap cooling time is not less than 48 hours, the environment temperature in the slow cooling pit is controlled at 300-500 ℃, the heap cooling temperature and the self-tempering effect of the steel plate are ensured, and the full diffusion and overflow of H in the steel are facilitated;
in the heat treatment process, a heat treatment process of primary quenching, secondary quenching and tempering is adopted to obtain a finished steel plate with 10% -15% of ferrite and 85% -90% of martensite composite structure, wherein the primary quenching is 905-925 ℃, the heat preservation time is 2.1-2.3min/mm, the secondary quenching is 790-860 ℃, the heat preservation time is 1.5-2.3min/mm, the tempering temperature is 650-680 ℃, and the heat preservation time is 3-4 min/mm.
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| Publication number | Priority date | Publication date | Assignee | Title |
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