CN108950383B - Cold-rolled steel plate for high-strength high-plasticity reinforced guard plate and production process thereof - Google Patents
Cold-rolled steel plate for high-strength high-plasticity reinforced guard plate and production process thereof 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
- 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
- C21D8/0205—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
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0236—Cold 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
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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
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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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
- C22C38/18—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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- 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
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
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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
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Abstract
A high-strength high-plasticity cold-rolled steel plate for reinforcing a guard plate is prepared by smelting, refining, continuous casting, rough rolling, finish rolling, cold rolling and annealing, wherein the grain size of a microstructure of the annealed cold-rolled steel plate for reinforcing the guard plate is 30-40 mu m, the average grain size of carbides is 20-50nm, a Cu-rich phase is separated out, and the microstructure comprises 70-75% of ferrite, 20-25% of martensite and less than or equal to 5% of residual austenite and bainite in percentage by volume; the yield strength is 800-900MPa, the tensile strength is 1000-1150MPa, and the elongation is 20-25%.
Description
Technical Field
The invention belongs to the technical field of steel materials, and particularly relates to a cold-rolled steel plate for a high-strength high-plasticity reinforced guard plate and a production process thereof.
Background
With the enhancement of awareness of energy conservation, weight reduction, safety and environmental protection of automobiles, a large amount of high-strength steel is used in the automobile industry, such as dual-phase steel, TRIP steel and the like. The composite material is mostly applied to inner plates or structural members and reinforcing members of cars. On the premise of ensuring the stamping requirement, the strength of the material for the outer plate of the car is further improved, the dent resistance and the corrosion resistance of the outer part of the car are further enhanced, and a novel enhanced guard plate updating material is sought to become one of the targets pursued by material suppliers and car design engineers.
High-strength steel generally contains more alloy elements, and composition segregation is easy to occur in the casting process, so that the local deformability of subsequent materials is reduced due to non-uniform composition and structure, namely, the hole expansion rate and the cold bending property are poor. In addition, the steel is inevitably provided with inclusions, and plastic inclusions can extend in the rolling process of the steel and become sources of micro-cracks, so that the local forming capability of the steel is further reduced. The high-strength steel has the possibility of delayed cracking, and the steel plate generally has internal stress after being formed, so that the cracks can be expanded, and the 'delayed cracking phenomenon' of gradual crack expansion and final cracking is shown under the action of the internal stress. Delayed cracking is an important problem corresponding to high-strength steel application, and because delayed cracking is not easy to find, the delayed cracking gradually occurs in the use process of parts, and a series of safety problems can be caused.
Disclosure of Invention
The invention aims to overcome the defects of the prior art and provides high-strength high-plasticity cold-rolled steel and a preparation method thereof. The yield strength of the cold-rolled steel plate is 800-900MPa, the tensile strength is 1000-1150MPa, and the elongation is 20-25%.
The technical scheme is as follows:
a cold-rolled steel plate for a high-strength high-plasticity reinforced guard plate comprises the following components in percentage by weight: c: 0.05-0.15%, Si: 0.5-0.6%, Mn: 2.50-2.80%, Cr: 0.5-4%, Ni: 0.2-1.2%, Al: 0.05-1.0%, P: less than or equal to 0.010 percent, S: less than or equal to 0.002%, N: 0.002-0.0035%, B: 0.001-0.003% of Fe and the balance of inevitable impurities.
A cold-rolled steel plate for a high-strength high-plasticity reinforced guard plate comprises the following components in percentage by weight: c: 0.12-0.15%, Si: 0.5-0.6%, Mn: 2.50-2.80%, Cr: 2-3%, Ni: 1.0-1.2%, Al: 0.5-1.0%, Cu: 0.2-0.3%, Mo: 0.3-0.4%, Co: 0.15-0.25%, W: 0.15-0.25%, Nb: 0.15-0.2%, Ti: 0.1-0.15%, Ta: 0.05-0.1%, P: less than or equal to 0.010 percent, S: less than or equal to 0.002%, N: 0.002-0.0035%, B: 0.001-0.003 percent of Fe and inevitable impurities in balance, smelting, refining, continuous casting, rough rolling, finish rolling, coiling, pickling, cold rolling, annealing, flattening, performance detection, packaging and a final product, wherein the microstructure grain size of the cold-rolled steel plate for the reinforced guard plate of the final product is 30-40 mu m, the average grain size of carbide is 20-50nm, a Cu-rich phase is precipitated, and the volume percentage of ferrite in the structure accounts for 70-75 percent, the volume percentage of martensite in the structure accounts for 20-25 percent, and the volume percentage of residual austenite and bainite in the structure accounts for less than or equal to 5 percent; the yield strength is 800-900MPa, the tensile strength is 1000-1150MPa, and the elongation is 20-25%.
Further: a cold-rolled steel plate for a high-strength high-plasticity reinforced guard plate comprises the following components in percentage by weight: c: 0.12%, Si: 0.5%, Mn: 2.5%, Cr: 2%, Ni: 1.0%, Al: 0.5%, Cu: 0.2%, Mo: 0.3%, Co: 0.15%, W: 0.15%, Nb: 0.15%, Ti: 0.1%, Ta: 0.05%, P: less than or equal to 0.010 percent, S: less than or equal to 0.002%, N: 0.002%, B: 0.001%, and the balance of Fe and inevitable impurities.
Further: a cold-rolled steel plate for a high-strength high-plasticity reinforced guard plate comprises the following components in percentage by weight: c: 0.15%, Si: 0.6%, Mn: 2.80%, Cr: 3%, Ni: 1.2%, Al: 1.0%, Cu: 0.3%, Mo: 0.4%, Co: 0.25%, W: 0.25%, Nb: 0.2%, Ti: 0.15%, Ta: 0.1%, P: less than or equal to 0.010 percent, S: less than or equal to 0.002%, N: 0.0035%, B: 0.003% and the balance of Fe and inevitable impurities.
The production process of the cold-rolled steel plate for the high-strength and high-plasticity reinforced guard plate comprises the following core steps: (1) smelting: KR molten iron is pretreated to remove S, the S in the molten iron is controlled to be less than or equal to 0.005 percent, then smelting is carried out in a top-bottom combined blown converter, the mass ratio of the molten iron to the scrap steel is 7-9: 1, the scrap steel is added firstly, then the molten iron is added, and the end point alkalinity of the converter is 3.5-3.8; the tapping temperature is 1580-1620 ℃; carrying out double slag-blocking tapping by adopting a slag-blocking plug and a slag-blocking rod; (2) refining: firstly, adding aluminum wires, fluorite and lime, and controlling the flow of bottom blowing argon to stop electrifying after the slag is completely white; stirring vigorously for desulfurization, controlling the flow of bottom blowing argon at 600-700L/min, stirring for 10-15min under the condition, then controlling the flow of bottom blowing argon at 80-100L/min, stirring for 8-10min under the condition, electrifying again to adjust the temperature of the molten pool so as to facilitate steel tapping, stopping argon blowing by soft blowing, and finishing LF refining; then VD refining is carried out: in the VD refining process, the molten steel vacuum treatment is required to be kept for 10-15 minutes under the condition that the vacuum degree is less than or equal to 67Pa, soft argon blowing stirring is adopted, after the vacuum treatment is finished, the CaSi wire feeding quantity is properly adjusted according to the molten steel condition, after the CaSi wire feeding is finished, the soft blowing operation is continuously carried out, the soft blowing time is ensured to be 5-8 minutes, the hydrogen content of the molten steel discharged from the station is 0-2ppm, and the temperature of the molten steel reaching a continuous casting table is strictly controlled;
(3) the continuous casting process comprises the following steps: argon blowing protection is carried out in the whole process, molten steel oxidation is avoided, and nitrogen increase in the continuous casting process is controlled; the tundish covering agent is adopted to avoid the exposure of the molten steel, and the secondary cooling water selects the low-carbon alloy covering slag according to the low-carbon alloy steel water distribution mode; the continuous casting secondary cooling area adopts the functions of electromagnetic stirring and heavy reduction, the electromagnetic stirring current is 300-320A, the frequency is 8-15Hz, and the heavy reduction amount is 30-35 mm; the superheat degree of the tundish is 15-25 ℃, and the thickness of a casting blank discharged from the crystallizer is 70-150 mm; the casting powder is used in the continuous casting process, and comprises the following components in percentage by mass: 40-45% of (CaO + BaO), 240-45% of SiO, 0.9-1.0% of alkalinity (Fe)2O3+MnO)1～3％，(B2O3+Na2O) 5-15%, C1-2%, and the balance of inevitable impurities 0-5%; the addition amount of the covering slag is 0.3-0.5 kg/t steel, and the thickness of the liquid slag layer is 10-15 mm;
(4) heating and rolling; feeding the steel billet into a heating furnace, heating at 1180-1185 ℃ for 70-90min, removing scale from the heating furnace by high-pressure water at 20-25MPa, rolling at 1050-1060 ℃ during rough rolling, wherein the reduction rate of a single pass is more than 18%, the reduction rate of a last pass is more than or equal to 25%, and carrying out 5 passes during rough rolling for recrystallization and refining austenite grains; the rolling start temperature of finish rolling is 920-930 ℃, the finishing temperature is 830-850 ℃, the accumulated reduction rate is 70-80%, and the finish rolling is carried out for 6 passes to form high-density dislocation in the rolling process; the coiling temperature is 680-700 ℃, and then acid cleaning is carried out;
(5) cold rolling; firstly heating the acid-washed steel plate to 740-.
Further: the production process of the cold-rolled steel plate for the high-strength and high-plasticity reinforced guard plate is characterized by comprising the following steps of: step (4), heating and rolling; feeding the steel billet into a heating furnace, heating at 1180 ℃ for 80min, removing scale from the steel billet by high-pressure water after the steel billet is taken out of the heating furnace, wherein the pressure is 20MPa, the initial rolling temperature of rough rolling is 1060 ℃, the single-pass reduction rate is 20%, the final-pass reduction rate is 30%, the rough rolling is carried out for 5 passes, the rolling speed distribution of each pass is 2m/s, 1.7m/s, 1.5m/s and 1.5m/s, and recrystallization and austenite grain refinement are carried out; the initial rolling temperature of the finish rolling is 920 ℃, the final rolling temperature is 840 ℃, the cumulative reduction rate is 75%, the finish rolling is carried out for 6 passes, the rolling speed distribution of each pass is 1.7m/s, 1.6m/s, 1.5m/s and 1.5m/s, high-density dislocation is formed in the rolling process, the coiling temperature is 690 ℃, and then the acid cleaning is carried out. The rolling speed in the high-reduction rolling process has an important influence on the structure and the performance of the core of the steel plate, and the lower the rolling speed in the rough rolling process, the more complete the recovery and recrystallization, and the finer the grains of the core of the steel plate. The structural uniformity in the thickness direction of a test steel plate with a high rolling speed (2.0m/s) is poor, while the structural uniformity of a steel plate with a low rolling speed (1.5m/s) is good because the rolling force permeates into the core part in the deformation process, and if the speed is too low, the continuous rolling production process cannot be ensured, and at the moment, the corresponding technical effect is also saturated. Therefore, the invention adopts the process that the rolling speed is gradually reduced.
Further: the production process of the cold-rolled steel plate for the high-strength and high-plasticity reinforced guard plate is characterized by comprising the following steps of: step (5), cold rolling; firstly heating the acid-washed steel plate to 740 ℃, preserving heat for 10min, then cooling to 615 ℃ at the speed of 3 ℃/min, preserving heat for 5min, then cooling to 305 ℃ at the speed of 25 ℃/s, then air-cooling to room temperature, and then flattening, detecting performance, packaging and obtaining the final product.
The casting process of the invention recommends a continuous casting process, and the continuous casting process focuses on controlling the casting temperature so as to refine the original cast structure. In order to control the Mn segregation at the center of the continuous casting billet, an electromagnetic stirring process is adopted, specifically, the continuous casting secondary cooling zone adopts the functions of electromagnetic stirring and heavy reduction, the electromagnetic stirring current is 300-320A, the frequency is 8-15Hz, and the heavy reduction is 30-35 mm; the superheat degree of the tundish is 15-25 ℃, and the thickness of a casting blank discharged from the crystallizer is 70-150 mm.
Next, the reason for limiting the chemical components of the present invention will be described. Here, the% of the component means mass%.
C is an important solid solution strengthening element and is used for ensuring high strength, when the content of C is too low, the amount of austenite in a ferrite and austenite two-phase region is reduced during the same critical annealing heating, the amount of the obtained martensite is correspondingly reduced, the strength is difficult to ensure, and when the content of C is too high, the toughness is reduced and the weldability is influenced. In the present invention, C: 0.05-0.15%, preferably C: 0.12 to 0.15 percent.
Si is a ferrite solid solution strengthening element and strongly improves the strength, Si is a main deoxidizing element in steel and has strong solid solution strengthening effect, but the plasticity and the toughness of the steel are reduced due to the excessively high content of Si, smelting is difficult, inclusions are easily formed, and the fatigue resistance of the steel is deteriorated. In the present invention, Si: 0.5 to 0.6 percent.
Mn strongly improves hardenability and work hardening properties, and when the Mn content is too low, it is difficult to form a sufficient amount of martensite in the structure, and the strengthening effect is poor, and when too high, it also affects the weldability of the substrate. In the present invention, Mn: 2.50-2.80%.
Cr and Mo: cr improves hardenability of austenite at critical annealing, further increases the amount of martensite when the C content of steel grades is increased, and in addition, Cr promotes diffusion of C into austenite, reducing the yield strength of ferrite. However, when the content is too high, ductility is deteriorated. Mo is a carbide forming element, is mostly dissolved in a critical heating area, effectively improves the hardenability of austenite, and is beneficial to obtaining the toughness matching. Preferably, Cr: 2-3%, Mo: 0.3 to 0.4 percent.
Co and W replace elements in crystal lattices to inhibit the oxidation of steel; w is a strong carbide forming element, improves the high-temperature strength and the heat resistance of steel, and comprehensively considers the cost factor, namely, Co: 0.15-0.25%, W: 0.15-0.25%.
Ti and Nb: ti is a strong carbide element, and precipitation strengthening and grain refinement are realized. Nb functions similarly to, but more strongly than, Ti, with Nb: 0.15-0.2%, Ti: 0.1 to 0.15 percent.
Ni can improve the hardenability and corrosion resistance of the steel and ensure the toughness of the steel. Since Ni delays the precipitation of Cr carbonitride at high temperature and maintains the hardness of the martensite structure supersaturated with solid-solution C, the Ni content is 0.2 to 1.2%, preferably 1.0 to 1.2%.
Al is an element added to steel for deoxidation. After the deoxidation is completed, Al reduces the O content in the steel sheet to improve the aging properties of the steel sheet. In addition, the addition of a proper amount of Al is beneficial to refining grains, so that the toughness of the steel is improved. The invention adjusts the Al content which is far higher than the Al content (usually less than or equal to 0.1%) of the common steel plate, and mainly considers that the Al is used for increasing the high-temperature strength of the steel through solid solution strengthening, improving the friction of the guard plate and the high-temperature fatigue property. Therefore, Al: 0.5 to 1.0 percent.
Cu enhances the strength of steel by precipitation of Cu-rich phase, and also increases the atmospheric corrosion resistance of steel by adding a proper amount of Cu element, but Cu is an element that expands the γ phase region and reduces fatigue properties, so Cu: 0.2 to 0.3 percent.
Ta can increase strength, cause carbonitride and the like to harden significantly, and therefore Ta: 0.05-0.1 percent.
P is used as harmful impurities in steel and has mechanical performance on steel, and the content of P is controlled to be less than or equal to 0.010%.
S has great damage effect on the performance of steel as harmful impurities in the steel, and the content of S needs to be controlled to be less than or equal to 0.002 percent.
The control range of N corresponds to that of Ti, the content of N is too low, the quantity of generated TiN particles is small, the size is large, and the grain refinement of steel cannot be improved; however, if the N content is too high, the free [ N ] in the steel increases, and the toughness is impaired. Thus N: 0.002-0.0035%.
B strongly suppresses the formation of pro-eutectoid ferrite and promotes the formation of low-temperature transformation structures such as bainite, so solid solution B is important for obtaining low-temperature transformation structures such as bainite to improve the strength of the steel sheet. B can also improve toughness, so B: 0.001-0.003%.
The casting powder of the invention can not be reduced or Al2O3 can not be reduced when contacting molten steel because the casting powder can be combined with CaO, BaO and the like into stable compounds even if Al2O3 exists in the casting powder, and the reduction of Al2O3 can not occur when oxides with high activity such as Fe2O3, MnO and SiO2 exist, so that the lubricating requirement is met, the casting blank surface casting powder layer is uniform, no slag ring exists in a crystallizer, the casting blank has no slag inclusion, no drawing leakage and no aluminum increase phenomenon in steel, and the casting powder of the invention can not increase aluminum in molten steel.
Compared with the prior art, the invention has the technical effects that:
1. the invention ensures the uniformity of the mechanical property of the tissue plate blank by accurately controlling the components and the production process of the product, and lists the rolling pass reduction system and the rolling speed. Has high strength, high toughness and high plasticity, is convenient for stamping and forming, and widens the application occasions.
2. According to the invention, by accurately controlling the alloy elements, the improvement of replacing the alloy with increased amount is avoided, the process cost is saved, and the production efficiency is improved.
3. Through reasonable chemical composition design and the adoption of a controlled rolling and controlled cooling process and an annealing process, the grain size of the microstructure of the cold-rolled steel plate for the reinforced guard plate of the final product is 30-40 mu m, the average grain size of carbide is 20-50nm, a Cu-rich phase is separated out, and the microstructure comprises 70-75% of ferrite, 20-25% of martensite and less than or equal to 5% of residual austenite and bainite in percentage by volume; the yield strength is 800-900MPa, the tensile strength is 1000-1150MPa, and the elongation is 20-25%.
Detailed Description
The technical solution of the present invention will be described in detail with reference to exemplary embodiments. Example embodiments may, however, be embodied in many different forms and should not be construed as limited to the embodiments set forth herein; rather, these embodiments are provided so that this disclosure will be thorough and complete, and will fully convey the concept of example embodiments to those skilled in the art.
Example 1
A cold-rolled steel plate for a high-strength high-plasticity reinforced guard plate comprises the following components in percentage by weight: c: 0.12-0.15%, Si: 0.5-0.6%, Mn: 2.50-2.80%, Cr: 2-3%, Ni: 1.0-1.2%, Al: 0.5-1.0%, Cu: 0.2-0.3%, Mo: 0.3-0.4%, Co: 0.15-0.25%, W: 0.15-0.25%, Nb: 0.15-0.2%, Ti: 0.1-0.15%, Ta: 0.05-0.1%, P: less than or equal to 0.010 percent, S: less than or equal to 0.002%, N: 0.002-0.0035%, B: 0.001-0.003 percent of Fe and inevitable impurities in balance, smelting, refining, continuous casting, rough rolling, finish rolling, coiling, acid washing, cold rolling, annealing, leveling, performance detection, packaging and obtaining a final product,
the core steps are as follows: (1) smelting: KR molten iron is pretreated to remove S, the S in the molten iron is controlled to be less than or equal to 0.005 percent, then smelting is carried out in a top-bottom combined blown converter, the mass ratio of the molten iron to the scrap steel is 7-9: 1, the scrap steel is added firstly, then the molten iron is added, and the end point alkalinity of the converter is 3.5-3.8; the tapping temperature is 1580-1620 ℃; carrying out double slag-blocking tapping by adopting a slag-blocking plug and a slag-blocking rod;
(2) refining: firstly, adding aluminum wires, fluorite and lime, and controlling the flow of bottom blowing argon to stop electrifying after the slag is completely white; stirring vigorously for desulfurization, controlling the flow of bottom blowing argon at 600-700L/min, stirring for 10-15min under the condition, then controlling the flow of bottom blowing argon at 80-100L/min, stirring for 8-10min under the condition, electrifying again to adjust the temperature of the molten pool so as to facilitate steel tapping, stopping argon blowing by soft blowing, and finishing LF refining; then VD refining is carried out: in the VD refining process, the molten steel vacuum treatment is required to be kept for 10-15 minutes under the condition that the vacuum degree is less than or equal to 67Pa, soft argon blowing stirring is adopted, after the vacuum treatment is finished, the CaSi wire feeding quantity is properly adjusted according to the molten steel condition, after the CaSi wire feeding is finished, the soft blowing operation is continuously carried out, the soft blowing time is ensured to be 5-8 minutes, the hydrogen content of the molten steel discharged from the station is 0-2ppm, and the temperature of the molten steel reaching a continuous casting table is strictly controlled;
(3) the continuous casting process comprises the following steps: argon blowing protection is carried out in the whole process, molten steel oxidation is avoided, and nitrogen increase in the continuous casting process is controlled; the tundish covering agent is adopted to avoid the exposure of the molten steel, and the secondary cooling water selects the low-carbon alloy covering slag according to the low-carbon alloy steel water distribution mode; the continuous casting secondary cooling area adopts the functions of electromagnetic stirring and heavy reduction, the electromagnetic stirring current is 300-320A, the frequency is 8-15Hz, and the heavy reduction amount is 30-35 mm; the superheat degree of the tundish is 15-25 ℃, and the thickness of the casting blank discharged out of the crystallizer is 100-200 mm; the casting powder is used in the continuous casting process, and comprises the following components in percentage by mass: 40-45% of (CaO + BaO), 240-45% of SiO, 0.9-1.0% of alkalinity (Fe)2O3+MnO)1～3％，(B2O3+Na2O) 5-15%, C1-2%, and the balance of inevitable impurities 0-5%; the addition amount of the covering slag is 0.3-0.5 kg/t steel, and the thickness of the liquid slag layer is 10-15 mm;
(4) heating and rolling; feeding the steel billet into a heating furnace, heating at 1180-1185 ℃ for 70-90min, removing scale from the heating furnace by high-pressure water at 20-25MPa, rolling at 1050-1060 ℃ during rough rolling, wherein the reduction rate of a single pass is more than 18%, the reduction rate of a last pass is more than or equal to 25%, and carrying out 5 passes during rough rolling for recrystallization and refining austenite grains; the rolling start temperature of finish rolling is 920-930 ℃, the finishing temperature is 830-850 ℃, the accumulated reduction rate is 70-80%, and the finish rolling is carried out for 6 passes to form high-density dislocation in the rolling process; the coiling temperature is 680-700 ℃, and then acid cleaning is carried out;
(5) cold rolling; firstly heating the acid-washed steel plate to 740-. The grain size of the microstructure of the cold-rolled steel plate for the reinforced guard plate of the final product is 30-40 mu m, the average grain diameter of carbide is 20-50nm, and a Cu-rich phase is precipitated, wherein the ferrite accounts for 70-75 percent, the martensite accounts for 20-25 percent, and the residual austenite and bainite account for less than or equal to 5 percent in the structure by volume percentage; the yield strength is 800-900MPa, the tensile strength is 1000-1150MPa, and the elongation is 20-25%.
Comparative example 1
A cold-rolled steel plate for a high-strength high-plasticity reinforced guard plate comprises the following components in percentage by weight: c: 0.08-0.1%, Si: 0.3-0.4%, Mn: 1.50-1.80%, Cr: 1.2-1.5%, Ni: 1.0-1.2%, Al: 0.5-1.0%, Cu: 0.2-0.3%, Mo: 0.3-0.4%, Co: 0.15-0.25%, W: 0.15-0.25%, Nb: 0.15-0.2%, Ti: 0.1-0.15%, Ta: 0.05-0.1%, P: less than or equal to 0.010 percent, S: less than or equal to 0.002%, N: 0.002-0.0035%, B: 0.001-0.003%, and the balance of Fe and inevitable impurities,
the preparation method is consistent with example 1; the final product has yield strength of 500-600MPa, tensile strength of 700-800MPa and elongation of 12.5-14.5%. Ferrite accounts for 70-80%, martensite accounts for 10-15%, and the other structures are residual austenite and bainite.
Comparative example 2
A cold-rolled steel plate for a high-strength high-plasticity reinforced guard plate comprises the following components in percentage by weight: c: 0.12-0.15%, Si: 0.5-0.6%, Mn: 2.50-2.80%, Cr: 2-3%, Ni: 1.0-1.2%, Al: 0.02 to 0.05%, Cu: 0.02 to 0.1%, Mo: 0.1-0.2%, Co: 0.05-0.1%, W: 0.05 to 0.1%, Nb: 0.15-0.2%, Ti: 0.1-0.15%, Ta: 0.05-0.1%, P: less than or equal to 0.010 percent, S: less than or equal to 0.002%, N: 0.002-0.0035%, B: 0.001-0.003%, and the balance of Fe and inevitable impurities,
the preparation process was identical to example 1.
The preparation method is consistent with example 1; the final product has yield strength of 650-700MPa, tensile strength of 750-860MPa and elongation of 13.5-17.5%. 70-75% of ferrite, 20-25% of martensite and the other tissues are residual austenite and bainite.
Comparative example 3
A cold-rolled steel plate for a high-strength high-plasticity reinforced guard plate comprises the following components in percentage by weight: c: 0.12-0.15%, Si: 0.3-0.4%, Mn: 2-2.30%, Cr: 1-1.5%, Ni: 1.0-1.2%, Al: 0.5-1.0%, Cu: 0.2-0.3%, Mo: 0.3-0.4%, Co: 0.15-0.25%, W: 0.15-0.25%, Nb: 0.15-0.2%, P: less than or equal to 0.010 percent, S: less than or equal to 0.002%, N: 0.002-0.0035%, B: 0.001-0.003%, and the balance of Fe and inevitable impurities,
the preparation method is consistent with example 1; the final product has the yield strength of 670-770MPa, the tensile strength of 800-920MPa and the elongation of 15-20 percent. Ferrite accounts for 75-80%, martensite accounts for 15-18%, and the other structures are residual austenite and bainite.
Comparative example 4
A cold-rolled steel plate for a high-strength high-plasticity reinforced guard plate comprises the following components in percentage by weight: c: 0.12-0.15%, Si: 0.5-0.6%, Mn: 2.50-2.80%, Cr: 2-3%, Ni: 1.0-1.2%, Al: 0.5-1.0%, Cu: 0.2-0.3%, Mo: 0.3-0.4%, Co: 0.15-0.25%, W: 0.15-0.25%, Nb: 0.15-0.2%, Ti: 0.1-0.15%, Ta: 0.05-0.1%, P: less than or equal to 0.010 percent, S: less than or equal to 0.002%, N: 0.002-0.0035%, B: 0.001-0.003%, and the balance of Fe and inevitable impurities,
preparation steps (1) - (3), (5) are identical to example 1;
step (4), heating and rolling; the method comprises the following steps of putting a steel billet into a heating furnace, heating at 1180 ℃ for 80min, removing scale from the steel billet after the steel billet is taken out of the heating furnace by high-pressure water, wherein the pressure is 20MPa, the initial rolling temperature of rough rolling is 1040 ℃, the single-pass reduction rate is 15%, the last-pass reduction rate is 20%, the rough rolling is carried out for 5 passes, the rolling speed distribution of each pass is 2.5m/s, 2.2m/s and 2m/s, and recrystallization and refinement of austenite grains are carried out; the initial rolling temperature of the finish rolling is 900 ℃, the final rolling temperature is 830 ℃, the cumulative reduction rate is 60%, the finish rolling is carried out for 6 passes, the rolling speed distribution of each pass is 1.9m/s, 1.7m/s and 1.7m/s, high-density dislocation is formed in the rolling process, the coiling temperature is 670 ℃, and then the acid cleaning is carried out.
The final product has the yield strength of 820-900MPa, the tensile strength of 940-1050MPa and the elongation of 15-18 percent. The ferrite accounts for 77-80%, the martensite accounts for 18-20%, and the other structures are residual austenite and bainite.
Comparative example 5
A cold-rolled steel plate for a high-strength high-plasticity reinforced guard plate comprises the following components in percentage by weight: c: 0.12-0.15%, Si: 0.5-0.6%, Mn: 2.50-2.80%, Cr: 2-3%, Ni: 1.0-1.2%, Al: 0.5-1.0%, Cu: 0.2-0.3%, Mo: 0.3-0.4%, Co: 0.15-0.25%, W: 0.15-0.25%, Nb: 0.15-0.2%, Ti: 0.1-0.15%, Ta: 0.05-0.1%, P: less than or equal to 0.010 percent, S: less than or equal to 0.002%, N: 0.002-0.0035%, B: 0.001-0.003%, and the balance of Fe and inevitable impurities,
preparation steps (1) to (4) correspond to example 1;
step (5), cold rolling; firstly heating the acid-washed steel plate to 730 ℃, preserving heat for 10min, then cooling to 600 ℃ at the speed of 1 ℃/min, preserving heat for 5min, then cooling to 290 ℃ at the speed of 15 ℃/s, then air-cooling to room temperature, and then flattening, detecting performance, packaging and obtaining the final product.
The final product has yield strength of 780-850MPa, tensile strength of 880-1030MPa and elongation of 16-18%. 76-82% of ferrite, 14-18% of martensite and the other structures of residual austenite and bainite.
The terminology used herein is for the purpose of description and illustration, rather than of limitation. As the present invention may be embodied in several forms without departing from the spirit or essential characteristics thereof, it should also be understood that the above-described embodiments are not limited by any of the details of the foregoing description, but rather should be construed broadly within its spirit and scope as defined in the appended claims, and therefore all changes and modifications that fall within the meets and bounds of the claims, or equivalences of such meets and bounds are therefore intended to be embraced by the appended claims.
Claims (5)
1. A cold-rolled steel plate for a high-strength high-plasticity reinforced guard plate comprises the following components in percentage by weight: c: 0.12-0.15%, Si: 0.5-0.6%, Mn: 2.50-2.80%, Cr: 2-3%, Ni: 1.0-1.2%, Al: 0.5-1.0%, Cu: 0.2-0.3%, Mo: 0.3-0.4%, Co: 0.15-0.25%, W: 0.15-0.25%, Nb: 0.15-0.2%, Ti: 0.1-0.15%, Ta: 0.05-0.1%, P: less than or equal to 0.010 percent, S: less than or equal to 0.002%, N: 0.002-0.0035%, B: 0.001-0.003 percent of Fe and inevitable impurities in balance, smelting, refining, continuous casting, rough rolling, finish rolling, coiling, pickling, cold rolling, annealing, flattening, performance detection, packaging and a final product, wherein the microstructure grain size of the cold-rolled steel plate for the reinforced guard plate of the final product is 30-40 mu m, the average grain size of carbide is 20-50nm, a Cu-rich phase is precipitated, and the volume percentage of ferrite in the structure accounts for 70-75 percent, the volume percentage of martensite in the structure accounts for 20-25 percent, and the volume percentage of residual austenite and bainite in the structure accounts for less than or equal to 5 percent; the yield strength is 800-900MPa, the tensile strength is 1000-1150MPa, and the elongation is 20-25%.
2. A cold-rolled steel plate for a high-strength high-plasticity reinforced guard plate comprises the following components in percentage by weight: c: 0.12-0.15%, Si: 0.5-0.6%, Mn: 2.50-2.80%, Cr: 2-3%, Ni: 1.0-1.2%, Al: 0.5-1.0%, Cu: 0.2-0.3%, Mo: 0.3-0.4%, Co: 0.15-0.25%, W: 0.15-0.25%, Nb: 0.15-0.2%, Ti: 0.1-0.15%, Ta: 0.05-0.1%, P: less than or equal to 0.010 percent, S: less than or equal to 0.002%, N: 0.002-0.0035%, B: 0.001-0.003 percent of Fe and inevitable impurities in balance, smelting, refining, continuous casting, rough rolling, finish rolling, coiling, pickling, cold rolling, annealing, flattening, performance detection, packaging and a final product, wherein the microstructure grain size of the cold-rolled steel plate for the reinforced guard plate of the final product is 30-40 mu m, the average grain size of carbide is 20-50nm, a Cu-rich phase is precipitated, and the volume percentage of ferrite in the structure accounts for 70-75 percent, the volume percentage of martensite in the structure accounts for 20-25 percent, and the volume percentage of residual austenite and bainite in the structure accounts for less than or equal to 5 percent; the yield strength is 800-900MPa, the tensile strength is 1000-1150MPa, and the elongation is 20-25%;
the production process of the cold-rolled steel plate for the high-strength and high-plasticity reinforced guard plate comprises the following steps: (1) smelting: KR molten iron is pretreated to remove S, the S in the molten iron is controlled to be less than or equal to 0.005 percent, then smelting is carried out in a top-bottom combined blown converter, the mass ratio of the molten iron to the scrap steel is 7-9: 1, the scrap steel is added firstly, then the molten iron is added, and the end point alkalinity of the converter is 3.5-3.8; the tapping temperature is 1580-1620 ℃; carrying out double slag-blocking tapping by adopting a slag-blocking plug and a slag-blocking rod;
(2) refining: firstly, adding aluminum wires, fluorite and lime, and controlling the flow of bottom blowing argon to stop electrifying after the slag is completely white; stirring vigorously for desulfurization, controlling the flow of bottom blowing argon at 600-700L/min, stirring for 10-15min under the condition, then controlling the flow of bottom blowing argon at 80-100L/min, stirring for 8-10min under the condition, electrifying again to adjust the temperature of the molten pool so as to facilitate steel tapping, stopping argon blowing by soft blowing, and finishing LF refining; then VD refining is carried out: in the VD refining process, the molten steel vacuum treatment is required to be kept for 10-15 minutes under the condition that the vacuum degree is less than or equal to 67Pa, soft argon blowing stirring is adopted, after the vacuum treatment is finished, the CaSi wire feeding quantity is properly adjusted according to the molten steel condition, after the CaSi wire feeding is finished, the soft blowing operation is continuously carried out, the soft blowing time is ensured to be 5-8 minutes, the hydrogen content of the molten steel discharged from the station is 0-2ppm, and the temperature of the molten steel reaching a continuous casting table is strictly controlled;
(3) the continuous casting process comprises the following steps: argon blowing protection is carried out in the whole process, molten steel oxidation is avoided, and nitrogen increase in the continuous casting process is controlled; the tundish covering agent is adopted to avoid the exposure of the molten steel, and the secondary cooling water selects the low-carbon alloy covering slag according to the low-carbon alloy steel water distribution mode; the continuous casting secondary cooling area adopts the functions of electromagnetic stirring and heavy reduction, the electromagnetic stirring current is 300-320A, the frequency is 8-15Hz, and the heavy reduction amount is 30-35 mm; the superheat degree of the tundish is 15-25 ℃, and the thickness of a casting blank discharged from the crystallizer is 70-150 mm; the casting powder is used in the continuous casting process, and comprises the following components in percentage by mass: 40-45% of (CaO + BaO), and SiO240-45%, alkalinity of 0.9-1.0, (Fe)2O3+MnO)1～3％，(B2O3+Na2O) 5-15%, C1-2%, and the balance of inevitable impurities 0-5%; the addition amount of the covering slag is 0.3-0.5 kg/t steel, and the thickness of the liquid slag layer is 10-15 mm;
(4) heating and rolling; feeding the steel billet into a heating furnace, heating at 1180-1185 ℃ for 70-90min, removing scale from the heating furnace by high-pressure water at 20-25MPa, rolling at 1050-1060 ℃ during rough rolling, wherein the reduction rate of a single pass is more than 18%, the reduction rate of a last pass is more than or equal to 25%, and carrying out 5 passes during rough rolling for recrystallization and refining austenite grains; the rolling start temperature of finish rolling is 920-930 ℃, the finishing temperature is 830-850 ℃, the accumulated reduction rate is 70-80%, and the finish rolling is carried out for 6 passes to form high-density dislocation in the rolling process; the coiling temperature is 680-700 ℃, and then the pickling is carried out;
(5) cold rolling and annealing; firstly heating the steel plate subjected to acid cleaning and cold rolling to 740-.
3. A production process of a cold rolled steel sheet for a high-strength high-plasticity reinforced fender according to claim 1 or 2, comprising the steps of: (1) smelting: KR molten iron is pretreated to remove S, the S in the molten iron is controlled to be less than or equal to 0.005 percent, then smelting is carried out in a top-bottom combined blown converter, the mass ratio of the molten iron to the scrap steel is 7-9: 1, the scrap steel is added firstly, then the molten iron is added, and the end point alkalinity of the converter is 3.5-3.8; the tapping temperature is 1580-1620 ℃; carrying out double slag-blocking tapping by adopting a slag-blocking plug and a slag-blocking rod;
(2) refining: firstly, adding aluminum wires, fluorite and lime, and controlling the flow of bottom blowing argon to stop electrifying after the slag is completely white; stirring vigorously for desulfurization, controlling the flow of bottom blowing argon at 600-700L/min, stirring for 10-15min under the condition, then controlling the flow of bottom blowing argon at 80-100L/min, stirring for 8-10min under the condition, electrifying again to adjust the temperature of the molten pool so as to facilitate steel tapping, stopping argon blowing by soft blowing, and finishing LF refining; then VD refining is carried out: in the VD refining process, the molten steel vacuum treatment is required to be kept for 10-15 minutes under the condition that the vacuum degree is less than or equal to 67Pa, soft argon blowing stirring is adopted, after the vacuum treatment is finished, the CaSi wire feeding quantity is properly adjusted according to the molten steel condition, after the CaSi wire feeding is finished, the soft blowing operation is continuously carried out, the soft blowing time is ensured to be 5-8 minutes, the hydrogen content of the molten steel discharged from the station is 0-2ppm, and the temperature of the molten steel reaching a continuous casting table is strictly controlled;
(3) the continuous casting process comprises the following steps: argon blowing protection is carried out in the whole process, molten steel oxidation is avoided, and nitrogen increase in the continuous casting process is controlled; the tundish covering agent is adopted to avoid the exposure of the molten steel, and the secondary cooling water selects the low-carbon alloy covering slag according to the low-carbon alloy steel water distribution mode; the continuous casting secondary cooling area adopts the functions of electromagnetic stirring and heavy reduction, the electromagnetic stirring current is 300-320A, the frequency is 8-15Hz, and the heavy reduction amount is 30-35 mm; the superheat degree of the tundish is 15-25 ℃, and the thickness of a casting blank discharged from the crystallizer is 70-150 mm; the covering slag is used in the continuous casting process, and the components of the covering slag are calculated according to the mass percentage：(CaO+BaO)40～45％，SiO240-45%, alkalinity of 0.9-1.0, (Fe)2O3+MnO)1～3％，(B2O3+Na2O) 5-15%, C1-2%, and the balance of inevitable impurities 0-5%; the addition amount of the covering slag is 0.3-0.5 kg/t steel, and the thickness of the liquid slag layer is 10-15 mm;
(4) heating and rolling; feeding the steel billet into a heating furnace, heating at 1180-1185 ℃ for 70-90min, removing scale from the heating furnace by high-pressure water at 20-25MPa, rolling at 1050-1060 ℃ during rough rolling, wherein the reduction rate of a single pass is more than 18%, the reduction rate of a last pass is more than or equal to 25%, and carrying out 5 passes during rough rolling for recrystallization and refining austenite grains; the rolling start temperature of finish rolling is 920-930 ℃, the finishing temperature is 830-850 ℃, the accumulated reduction rate is 70-80%, and the finish rolling is carried out for 6 passes to form high-density dislocation in the rolling process; the coiling temperature is 680-700 ℃, and then the pickling is carried out;
(5) cold rolling and annealing; firstly heating the steel plate subjected to acid cleaning and cold rolling to 740-.
4. A production process of a cold-rolled steel sheet for a high-strength high-plasticity reinforced fender as claimed in claim 3, wherein: step (4), heating and rolling; feeding the steel billet into a heating furnace, heating at 1180 ℃ for 80min, removing scale from the steel billet by high-pressure water after the steel billet is taken out of the heating furnace, wherein the pressure is 20MPa, the initial rolling temperature of rough rolling is 1060 ℃, the single-pass reduction rate is 20%, the final-pass reduction rate is 30%, the rough rolling is carried out for 5 passes, the rolling speed distribution of each pass is 2m/s, 1.7m/s, 1.5m/s and 1.5m/s, and recrystallization and austenite grain refinement are carried out; the initial rolling temperature of the finish rolling is 920 ℃, the final rolling temperature is 840 ℃, the cumulative reduction rate is 75%, the finish rolling is carried out for 6 passes, the rolling speed distribution of each pass is 1.7m/s, 1.6m/s, 1.5m/s and 1.5m/s, high-density dislocation is formed in the rolling process, the coiling temperature is 690 ℃, and then the acid cleaning is carried out.
5. A production process of a cold rolled steel sheet for a high-strength high-plasticity reinforced fender according to claim 3 or 4, characterized by comprising the following steps: step (5), cold rolling and annealing; firstly heating the steel plate subjected to acid cleaning and cold rolling to 740 ℃, preserving heat for 10min, then cooling to 615 ℃ at the speed of 3 ℃/min, preserving heat for 5min, then cooling to 305 ℃ at the speed of 25 ℃/s, then air-cooling to room temperature, and then flattening, detecting performance, packaging and obtaining the final product.
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