Classifications

• • 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
• • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
  • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
• • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
  • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
  • C21D8/0221—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
  • C21D8/0226—Hot rolling
• • 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 of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment
  • C21D8/02—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
  • C21D8/0247—Modifying the physical properties of ferrous metals or ferrous alloys by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
• • 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
• • 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
• • 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
• • 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
• • 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
• • 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
• • 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
• • 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
• • 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
• • 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
  • C21D2211/004—Dispersions; Precipitations
• • 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
• • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
  • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
  • Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
  • Y02P10/00—Technologies related to metal processing
  • Y02P10/20—Recycling

Definitions

• the present invention relates to the technical field of offshore steel, and in particular to a low yield strength ratio offshore steel with a yield strength of ⁇ 750MPa and a production process thereof.
• marine structural steel As a key structural material for marine engineering equipment, steel is widely used in offshore oil drilling platforms, offshore wind power, submarine pipelines and other facilities.
• the service environment of marine structural steel is harsh. In addition to gravity loads, it also has to withstand wind loads, wave loads, ice loads, and earthquake loads. In addition, due to the difficulty of maintenance, the service life of marine engineering equipment is also long, and the requirements for steel are higher.
• marine structural steel plates are gradually developing in the direction of high strength, large thickness, and large specifications.
• yield ratio the ratio of its yield strength to tensile strength
• the present invention has developed a low yield ratio marine steel with a yield strength ⁇ 750MPa, a tensile strength ⁇ 1050MPa, a yield ratio ⁇ 0.72, and a -40°C lateral impact energy ⁇ 100J.
• the Chinese patent application with application number 202010235198.7 discloses "a kind of high-strength steel plate with a yield strength of 690MPa and a low yield ratio and a method for manufacturing the same".
• a tempered bainite + bainite complex structure is obtained, with a yield strength of ⁇ 690MPa, a tensile strength of ⁇ 770MPa, and a yield ratio of ⁇ 0.88.
• This method adopts a secondary quenching process to heat the steel plate twice, which consumes a lot of energy during the production process and has low production efficiency.
• its C content is controlled at 0.1%-0.2%, which is difficult to meet the requirements of marine steel for welding, and the welding of steel plates is difficult.
• the yield ratio of its steel plate is ⁇ 0.88, but it can be seen from the examples that the yield ratio of the steel plates produced by it is higher than 0.86, which is significantly different from the yield ratio of the steel plate of the present invention ( ⁇ 0.72), and it is difficult to ensure that the marine facilities absorb more energy during plastic deformation.
• the Chinese patent application with application number 202110035527.8 discloses "a low yield ratio marine steel plate with excellent low temperature toughness and its manufacturing method".
• a steel plate with a yield ratio ⁇ 0.8 is obtained.
• Its Si content is controlled at 0.2%-0.4%. If the content is too high, the plasticity and toughness of the heat affected zone of the steel plate will be reduced.
• Its Mn content is controlled at 1.45%-1.65%. If the content is too high, it will aggravate the segregation of the continuous casting billet and reduce the uniformity of the organization.
• Its Cu content is controlled at 0.15%-0.3%.
• the yield strength of the steel plate produced by this method is above 420MPa, which is more than two steel grades lower than the yield strength of the steel plate produced by the method of the present invention with a yield strength of more than 750MPa, and it is difficult to meet the high strength requirements.
• the Chinese patent application with application number 201780071626.3 discloses "a low yield ratio ultra-high strength steel and its manufacturing method", which uses two cooling rates, that is, cooling the steel plate to below the A r3 temperature first and then cooling it to below the B s temperature to obtain a steel plate with a yield ratio ⁇ 0.85 and a tensile strength ⁇ 800MPa.
• the cooling process of this method is relatively complicated, and it is difficult to accurately control the termination temperature of the first cooling in actual on-site production; and the cooling rate of the second cooling needs to be greater than 30°C/s, which has high requirements on equipment capacity and poor process applicability.
• the addition of Mn to the steel will aggravate the segregation of the continuous casting billet and reduce the uniformity of the structure.
• the Chinese patent application with application number 202111254001.5 discloses "a method for preparing medium and thick steel plates with high strength and toughness and low yield ratio of 690MPa yield strength".
• the hot-rolled plate is pre-heated at 300-650°C for more than 60min, then water-quenched after heat preservation in the two-phase region for 30-120min, and finally heated to 200-450°C for medium-low temperature tempering, and a steel plate with a yield strength ⁇ 690MPa and a yield ratio ⁇ 0.85 is obtained.
• the addition of Mn in the steel will aggravate the segregation of the continuous casting billet and reduce the uniformity of the structure.
• the addition of Cu is low, and the improvement of the strength and strain strengthening ability of the steel plate by Cu is limited.
• V is high, the size of the V-containing precipitates is too large, and the ability to hinder dislocation movement is weak, and the strain strengthening ability of the steel plate cannot be improved; and the large amount of V deteriorates the impact toughness of the heat-affected zone of the steel plate, and will increase the alloy cost.
• this method heats the hot-rolled plate twice, and the production cycle of the steel plate is long and the production cost is high.
• the Chinese patent application with application number 201210348440.7 discloses "an ultra-high strength and high toughness steel plate for marine engineering and its production method".
• the ultra-high strength and high toughness steel plate for marine engineering is obtained by quenching in the austenite phase above A c3 , the quenching temperature is 900-920°C, and tempering at 600-630°C after quenching.
• the yield strength of the steel plate is 710-800MP, the tensile strength is 770-840MPa, and the transverse impact energy at -40°C is ⁇ 90J.
• This method adopts a quenching and tempering process to heat the steel plate twice, which consumes a lot of energy in the production process and has low production efficiency; Cu is added in small amounts, and it is impossible to improve the strength and strain strengthening ability of the steel plate by forming a nano-scale Cu-rich phase.
• the Chinese patent application with application number 202111253774.1 discloses "a low yield ratio marine steel plate with a yield strength of 960MPa and a preparation method thereof".
• a high-strength and toughness low yield ratio medium and thick steel plate with a compressive strength ⁇ 960MPa, a tensile strength ⁇ 1100MPa, and -40°C impact toughness ⁇ 69J is prepared through two-phase annealing + complete austenitization quenching + medium and low temperature tempering treatment process.
• This method heats the steel plate multiple times, the production process is complicated, the energy consumption in the production process is high, and the production efficiency is low; the amount of Cu added is small, and the strength and strain strengthening ability of the steel plate cannot be improved by forming a nano-scale Cu-rich phase.
• the Chinese patent application with application number 202210648955.2 discloses "A high-strength steel resistant to marine atmospheric corrosion and its production method".
• a marine atmospheric corrosion-resistant steel with high strength, low yield ratio and excellent toughness is obtained.
• the yield strength of the steel is 600-700MPa
• the tensile strength is 750-850MPa
• the impact energy at -20°C is ⁇ 100J.
• the Si content in this method is 0.6%-0.8%. If the content is too high, the plasticity and toughness of the weld metal will be reduced.
• the Mn content is controlled at 1.4%-1.7%. If the content is too high, the segregation of the continuous casting billet will be aggravated and the uniformity of the organization will be reduced.
• the addition of Cu is low, and the improvement of the strength and strain strengthening ability of the steel plate by Cu is limited.
• the present invention provides a low yield ratio marine engineering steel with a yield strength of ⁇ 750MPa and a production process thereof.
• the microstructure of the produced steel plate is a mixed structure of martensite (hard phase)-bainite (soft phase)-nanoscale precipitates, which has higher strain strengthening ability and lower yield ratio, and has good weldability.
• the TMCP process is adopted, and no complicated quenching and tempering process is required, so the production cost is low and the efficiency is high.
• a low yield ratio marine steel with a yield strength ⁇ 750MPa the chemical composition of the steel plate is as follows by weight percentage: C 0.06% ⁇ 0.10%, Si 0.1% ⁇ 0.2%, Mn 0.60% ⁇ 1.0%, P ⁇ 0.015%, S ⁇ 0.005%, Cu 0.62% ⁇ 1.20%, Cr 0.20% ⁇ 0.50%, Ni 0.50% ⁇ 1.20%, Mo 0.30% ⁇ 0.70%, Nb ⁇ 0.06%, V 0.02% ⁇ 0.05%, Ti ⁇ 0.02%, Al ⁇ 0.04%, and the balance is Fe and unavoidable impurity elements.
• the microstructure of the steel plate is a mixed structure of martensite + bainite + nanoscale precipitates, wherein the martensite structure accounts for 35% to 45% and the bainite structure accounts for 55% to 65%; the martensite structure is evenly distributed in the bainite matrix, and the nanoscale precipitates are evenly dispersed in the entire microstructure.
• the steel plate has a yield strength of ⁇ 750 MPa, a tensile strength of ⁇ 1050 MPa, a yield strength ratio of ⁇ 0.72, and a transverse impact energy of ⁇ 100 J at -40°C.
• a production process of low yield strength ratio marine engineering steel with a yield strength of ⁇ 750MPa comprising: smelting, continuous casting, slow cooling of ingot, reheating of ingot, controlled rolling and controlled cooling, and stacking and slow cooling; wherein:
• the present invention has the following beneficial effects:
• the key to reducing the yield strength ratio of the steel plate is to adjust the ratio of the soft phase and the hard phase in its microstructure, and make the structure have a higher strain hardening ability; at the same time, in order to ensure the high yield strength, high tensile strength and high toughness of the steel plate, the strength of the soft and hard phases in the steel and the matching between the phases also need to be precisely controlled; the present invention uses Cu-Mo-Nb-V-Ti composite strengthening and adjusts the controlled rolling and controlled cooling parameters to make the microstructure of the produced steel plate a mixed structure of martensite (hard phase)-bainite (soft phase)-nanoscale precipitates, wherein the martensite accounts for 35%-45%, the bainite accounts for 55%-65%, the martensite structure is uniformly distributed in the bainite matrix, and the nanoscale precipitates are uniformly dispersed in the entire microstructure, which has a higher strain hardening ability and a lower yield strength ratio, and has good weldability; the yield strength of the steel plate
• the present invention adopts the TMCP process, which does not require a complicated quenching and tempering process, has low production cost and high efficiency;
• the present invention is not only applicable to marine engineering steel, but also to other high-strength steel plates, such as steel for high-rise buildings, steel for bridges, steel for engineering machinery, steel for pressure vessels, etc.
• the low yield ratio marine steel with a yield strength of ⁇ 750MPa described in the present invention has the following chemical compositions by weight: C 0.06%-0.10%, Si 0.1%-0.2%, Mn 0.60%-1.0%, P ⁇ 0.015%, S ⁇ 0.005%, Cu 0.62%-1.20%, Cr 0.20%-0.50%, Ni 0.50%-1.20%, Mo 0.30%-0.70%, Nb ⁇ 0.06%, V 0.02%-0.05%, Ti ⁇ 0.02%, Al ⁇ 0.04%, and the remainder is Fe and unavoidable impurity elements.
• the microstructure of the steel plate is a mixed structure of martensite + bainite + nanoscale precipitates, wherein the martensite structure accounts for 35% to 45% and the bainite structure accounts for 55% to 65%; the martensite structure is evenly distributed in the bainite matrix, and the nanoscale precipitates are evenly dispersed in the entire microstructure.
• the yield strength of the steel plate is ⁇ 750MPa
• the tensile strength is ⁇ 1050MPa
• the yield strength ratio is ⁇ 0.72
• the transverse impact energy at -40°C is ⁇ 100J.
• the production process of a low yield strength ratio marine engineering steel with a yield strength of ⁇ 750MPa described in the present invention comprises: smelting, continuous casting, slow cooling of ingots, reheating of ingots, controlled rolling and controlled cooling, and stacking and slow cooling; wherein:
• Carbon C is the main element in steel after Fe, which directly affects the strength, plasticity, toughness and weldability of steel plates. C can effectively improve the strength and hardenability of steel plates, but too high a C content will have a negative impact on the plasticity, toughness and weldability of steel plates. Therefore, the present invention sets the C content range to 0.06% to 0.10%.
• Si is an important reducing agent and deoxidizer in the steelmaking process, and can improve the hardness and strength of the steel plate through solid solution strengthening. However, if the Si content is too high, the plasticity and toughness of the weld metal will be reduced. Therefore, the present invention sets the Si content range to 0.1% to 0.2%.
• Mn can be infinitely dissolved with Fe, which can improve the strength of the steel plate while ensuring that the steel has sufficient plasticity and toughness. Therefore, Mn is a strengthening element widely used in steel. Mn can react with the S element in steel to form MnS, which can eliminate the harmful effects of S. However, too high a Mn content will aggravate the segregation of the continuous casting billet, increase the grade of the banded structure of the steel plate, and cause the uniformity of the steel plate structure to deteriorate, which is unfavorable to the lamellar tearing resistance, plasticity, low-temperature toughness and welding performance of the steel plate. For this reason, the present invention sets the Mn content range to 0.6% to 1.0%.
• Niobium Nb is one of the most important microalloying elements. Part of Nb is dissolved in the matrix to play a role in solid solution strengthening. During the controlled rolling process, the solid solution Nb significantly increases the recrystallization temperature of the steel plate, which can complete the rolling process of the steel plate in a higher temperature range, thereby reducing the internal stress of the steel plate; the remaining part of Nb forms fine carbides and nitrides, inhibits the recrystallization of austenite, maintains the deformation effect, and refines the ferrite grains, which can improve the strength and impact toughness of the steel plate and reduce The brittle transition temperature is lowered.
• the nano-scale Nb-containing precipitate phase can hinder dislocation movement and improve the strain strengthening ability of the steel plate.
• the present invention selects the Nb content to be no higher than 0.06%.
• Vanadium V is a strong carbonitride-forming element, which has the effects of refining the structure and grains, improving strength and toughness, improving welding performance, and reducing overheat sensitivity. Nano-scale V-containing precipitates can hinder dislocation movement and improve the strain strengthening ability of steel plates. However, when the V content is too high, the V-containing precipitates are large in size, which is harmful to the strain strengthening ability of the steel plate and will deteriorate the impact toughness of the welding heat-affected zone. Therefore, the present invention selects a V content range of 0.02% to 0.05%.
• Titanium Ti is a strong carbonitride-forming element.
• the Ti-containing precipitate phase can effectively pin the grain boundary, hinder the growth of austenite, refine the grains, and improve the toughness and low-temperature toughness of the steel plate.
• the nano-scale Ti-containing precipitate phase can hinder the dislocation movement and improve the strain strengthening ability of the steel plate.
• the present invention selects a Ti content of no more than 0.02%.
• Copper Cu can improve the strength and hardenability of the steel plate, and can inhibit the ferrite transformation during the cooling process of the steel plate, and has no adverse effect on the welding performance.
• the Cu content exceeds a certain amount, a nano-sized Cu-rich phase will be generated in the steel plate, which will increase the strength of the steel plate, hinder the dislocation movement during deformation, and improve the strain strengthening ability of the steel plate.
• the present invention selects a Cu content range of 0.62% to 1.20%.
• Chromium Cr can increase the hardenability, strength, hardness and wear resistance of the steel plate, but it will reduce the elongation and cross-sectional shrinkage. If too much Cr is added, during the welding thermal cycle, Cr-containing carbides will precipitate and aggregate and grow at the original austenite grain boundaries, seriously damaging the low-temperature toughness and weldability of the steel plate. Therefore, the present invention selects the Cr content range of 0.20% to 0.50%.
• Nickel Ni has the function of stabilizing austenite and improving hardenability. Adding a certain amount of Ni to steel can improve strength, toughness, corrosion resistance, and reduce the tough-brittle transition temperature. Ni-containing steel is generally not easy to overheat. It can prevent the growth of grains at high temperatures and keep the fine grain structure. However, considering the cost factor, the present invention selects the Ni content range of 0.50% to 1.20%.
• Molybdenum can improve the hardenability and heat resistance of steel and inhibit the ferrite transformation during the cooling process of the steel plate. It can increase the dislocation density inside the grains within a larger cooling range and improve the strain strengthening ability of the steel plate. However, when the Mo content is too high, it is not good for weldability and will increase the alloy cost.
• the present invention selects the Mo content range of 0.30% to 0.70%.
• Aluminum Al is a necessary deoxidizing element, and can refine grains and fix N in steel, thereby significantly improving the impact toughness of steel plates and reducing cold brittleness and aging tendencies; Al can also improve the corrosion resistance of steel, especially when used in combination with Mo, Cu, Si, Cr and other elements, the effect is better; but too high Al content is prone to hot cracks in the casting. Therefore, the Al content range selected in the present invention is not higher than 0.04%.
• Phosphorus P is brought into steel from ores and is one of the harmful elements, similar to S. Although P can increase the strength and The hardness increases, but the plasticity and impact toughness decrease significantly. Especially at low temperatures, it makes the steel material significantly brittle. The higher the P content, the greater the cold brittleness. However, removing P to a lower level will significantly increase the steelmaking cost. Therefore, the present invention selects a P content range of no more than 0.015%.
• Sulfur S comes from steelmaking ore and fuel coke, and is one of the most common harmful elements in steel. It is detrimental to the ductility, toughness, weldability and corrosion resistance of steel. If S exists in the form of FeS in steel, it can also cause hot brittleness during hot working.
• the present invention selects the S content range to be no higher than 0.005%.
• the present invention adopts elements such as Cu, Mo, Nb, V, and Ti to realize the composite strengthening of steel, controls the heating temperature of the continuous casting billet between 1150 and 1250°C, and the total furnace time between 3 and 6 hours, which can ensure that the precipitation phase of the alloy elements is fully dissolved back into the austenite, and fully exerts the beneficial effects of inhibiting recrystallization, solid solution strengthening, precipitation strengthening, grain refinement, and improving the strain strengthening ability of the steel plate in the subsequent controlled rolling process, so as to prepare the composition and temperature for obtaining the final organizational structure.
• the solid solution will be insufficient, which will affect the final strength and strain strengthening ability of the steel plate; if the heating time and heating temperature are higher than the selected range, the original austenite grains of the continuous casting billet are prone to be too coarse, which is not conducive to the control of the toughness of the steel plate.
• the continuous casting billet After the continuous casting billet is discharged from the furnace, it is first descaled with high-pressure water to ensure the surface quality of the steel plate after rolling. If the temperature after descaling is lower than 1120°C, the rolling load in the rolling stage will increase, and the austenite recrystallization effect will be reduced, affecting the grain refinement. Finer austenite grains can ensure that during the laminar cooling process and after the bainite transformation is completed, the untransformed austenite in the steel plate still has enough grain boundaries for martensite nucleation, and finally the martensite is evenly distributed in the bainite.
• the rough rolling stage is rolling in the austenite recrystallization temperature zone.
• the rolling is completed above 1000°C to avoid entering the partial recrystallization temperature zone and causing uneven grain size.
• the rolling is completed in a higher temperature zone, and the deformation conditions of the rolled piece are good, which is conducive to increasing the pass reduction.
• the intermediate billet with a thickness not less than 2 times that of the finished steel plate is selected to ensure the cumulative reduction of the second stage rolling, so that the recrystallized austenite grains are fully flattened, which is conducive to subsequent organizational transformation and grain refinement.
• the finishing rolling stage is rolling in the non-recrystallization zone, and the rolling temperature range is selected to be 850-900°C.
• the temperature is higher than 900°C, the rolled piece may enter the partial recrystallization zone, resulting in uneven grains.
• the temperature is lower than 850°C, it is difficult to ensure the starting temperature required for subsequent direct accelerated cooling.
• the cooling method adopts laminar cooling to ensure that the steel plate is transformed into a mixed structure of martensite and bainite, ensuring that martensite accounts for 35% to 45%, bainite accounts for 55% to 65%, and the martensite structure is evenly distributed in the bainite matrix.
• the cooling rate is too high, the martensite content in the steel plate is too high, and the final material has a high yield strength ratio and poor low-temperature toughness; if the cooling rate is too low, the steel plate is not undercooled enough, and martensite is difficult to produce, which ultimately leads to low tensile strength of the steel plate.
• the red-return temperature of the steel plate is controlled at 300-350°C.
• the fast-cooling structure is low-temperature tempered to reduce the carbon content in martensite and bainite, release the residual stress in the steel, and produce Cu-rich nano-precipitates uniformly dispersed throughout the microstructure.
• the temperature is higher than the selected red-return temperature, it is difficult to ensure the integrity of the phase transformation, which affects the strength and toughness matching and organizational regulation of the final steel plate. If the temperature is lower than the selected red-returning temperature and the selected slow cooling time, the low-temperature tempering effect cannot be achieved, the dispersed Cu-rich nano-precipitates in the steel plate are insufficient, the processing strengthening ability of the steel plate cannot be guaranteed, and the residual stress in the steel cannot be released, resulting in poor toughness of the steel plate.
• the smelting process includes molten iron pretreatment, converter smelting, refining outside the furnace and vacuum treatment.
• the continuous casting is fully protected and cast, and one or more of electromagnetic stirring, light pressure or heavy pressure is put into use.
• Table 1 shows the chemical composition of the steel plate in this embodiment
• Table 2 shows the rolling and heat treatment process parameters of the steel plate in this embodiment
• Table 3 shows the mechanical properties of the steel plate in this embodiment.
• the steel plate prepared by the production process of the present invention has a yield strength of ⁇ 750MPa, a tensile strength of ⁇ 1050MPa, a yield strength ratio of ⁇ 0.72, and a transverse impact energy of -40°C ⁇ 100J. It has a lower yield strength ratio and fluctuates less within the entire process window.

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• 2022
  • 2022-10-19 CN CN202211276285.2A patent/CN115558863B/zh active Active
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