CN108728742B - Shock-resistant, fire-resistant and corrosion-resistant steel and manufacturing method of medium-thickness steel plate and thin steel plate - Google Patents
Shock-resistant, fire-resistant and corrosion-resistant steel and manufacturing method of medium-thickness steel plate and thin steel plate Download PDFInfo
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Abstract
The invention discloses a manufacturing method of shock-resistant, fire-resistant and corrosion-resistant steel, a medium-thickness steel plate and a thin steel plate, belongs to the technical field of steel for steel structures, and solves the problem that the existing steel for steel structure buildings has poor comprehensive performances such as shock resistance, fire resistance, corrosion resistance and the like. The composition is as follows: c: 0.05-0.11 wt.%, Si: 0.10-0.30 wt.%, Mn: 1.00-2.00 wt.%, Ni: 1.00-1.50 wt.%, Cu: 1.00-1.50 wt.%, Mo: 0.50-0.60 wt.%, Nb: 0.05-0.10 wt.%, V: 0.05-0.10 wt.%, Ti: 0.010-0.030 wt.%, Al: 0.015-0.035 wt.%, B: 0-0.0018 wt.%, P: <0.015 wt.%, S: <0.010 wt.%, the balance being Fe and unavoidable impurities. The manufacturing method adopts converter or electric furnace smelting, and the casting adopts continuous casting or die casting. The anti-seismic fire-resistant corrosion-resistant steel can be used for steel structure buildings.
Description
Technical Field
The invention belongs to the technical field of steel for steel structures, and relates to a method for manufacturing shock-resistant, fire-resistant and corrosion-resistant steel, medium-thickness steel plates and thin steel plates.
Background
The steel structure building has the advantages of large space utilization rate, flexible and attractive design, cyclic utilization and the like, and the demand is increasing day by day. However, steel for common steel structures has poor fire resistance and corrosion resistance, and is often coated with multiple layers of thick anticorrosive coatings and fireproof coatings to solve the problems of fire safety and corrosion prevention, so that the construction cost of steel structure buildings is greatly increased, and the construction period is prolonged. Therefore, the development trend of steel for steel structures is toward the realization of the combination of functions such as shock resistance, fire resistance, corrosion resistance and the like.
The corrosion resistance is different according to the application environment and is mainly limited by the alloy cost technically, the anti-seismic performance requires that the yield ratio of the steel is below 0.85 at normal temperature and the elongation is above 17% -20%, the fire resistance requires that the yield strength of the steel at 600 ℃ is not lower than 2/3 required by the room-temperature yield strength standard, and the requirements of the two are very technical challenges for steel with the yield strength of 600MPa and above steel structure.
Disclosure of Invention
In view of the above analysis, the present invention aims to provide a steel for earthquake resistance, fire resistance and corrosion resistance and a method for manufacturing the same, which solve the problem of poor comprehensive properties such as earthquake resistance, fire resistance and corrosion resistance of the conventional steel structural construction steel.
The purpose of the invention is mainly realized by the following technical scheme:
on one hand, the invention provides anti-seismic fire-resistant corrosion-resistant steel which comprises the following components: c: 0.05-0.11 wt.%, Si: 0.10-0.30 wt.%, Mn: 1.00-2.00 wt.%, Ni: 1.00-1.50 wt.%, Cu: 1.00-1.50 wt.%, Mo: 0.50-0.60 wt.%, Nb: 0.05-0.10 wt.%, V: 0.05-0.10 wt.%, Ti: 0.010-0.030 wt.%, Al: 0.015-0.035 wt.%, B: 0-0.0018 wt.%, P: <0.015 wt.%, S: <0.010 wt.%, the balance being Fe and unavoidable impurities.
Further, the composition is: c: 0.05-0.09 wt.%, Si: 0.25-0.28 wt.%, Mn: 1.10-1.80 wt.%, Ni: 1.15-1.45 wt.%, Cu: 1.05-1.45 wt.%, Mo: 0.55-0.58 wt.%, Nb: 0.06-0.09 wt.%, V: 0.058-0.092 wt.%, Ti: 0.015-0.028 wt.%, Al: 0.025-0.030 wt.%, B: 0.0002-0.0012 wt.%, P: <0.015 wt.%, S: <0.010 wt.%, the balance being Fe and unavoidable impurities.
Furthermore, the anti-seismic, fireproof and corrosion-resistant steel is a steel plate with the thickness of more than 40mm, and the content of B is 0.0008-0.0018 wt.%.
On the other hand, the invention also provides a manufacturing method of the shock-resistant, fire-resistant and corrosion-resistant medium steel plate, which adopts the shock-resistant, fire-resistant and corrosion-resistant steel, wherein the medium steel plate is a steel plate with the thickness of more than 20 mm;
the manufacturing method comprises the following steps:
step 1: heating the continuous casting billet or the cast ingot, and soaking to obtain a soaked billet;
step 2: carrying out hot rolling rough rolling and hot rolling finish rolling on the soaked steel billet to obtain a hot rolled steel plate;
and step 3: carrying out primary laminar cooling on the hot-rolled steel billet, wherein the re-reddening temperature of the primary laminar cooling is below 400 ℃, and then carrying out primary air cooling to obtain a martensite structure so as to obtain the steel billet after the primary air cooling;
and 4, step 4: heating the steel billet subjected to the first air cooling to 650-700 ℃ to perform two-phase isothermal heat treatment to obtain a heat-treated steel billet;
and 5: and carrying out secondary laminar flow cooling on the steel billet after the heat treatment, wherein the temperature of the secondary laminar flow cooling is 400-500 ℃, and the solid solution of copper is more than 60 wt%, and then carrying out secondary air cooling to obtain the shock-resistant, fire-resistant and corrosion-resistant medium plate.
Further, the method comprises the following steps:
step 1: heating the cogging continuous casting billet or the cogging cast ingot, and soaking to obtain a soaked steel billet, wherein the heating temperature is 1180-1250 ℃, and the soaking time is 0.5-3 h;
step 2: carrying out hot rolling rough rolling and hot rolling finish rolling on the soaked steel billet to obtain a hot rolled steel plate, carrying out hot rolling rough rolling for 3-6 times, and carrying out hot rolling finish rolling for 5-10 times, wherein the starting temperature of the hot rolling rough rolling is 1180-1220 ℃, the finishing temperature of the hot rolling rough rolling is 1135-1170 ℃, the starting temperature of the hot rolling finish rolling is 995-1010 ℃, and the finishing temperature of the hot rolling finish rolling is 850-950 ℃;
and step 3: carrying out first laminar cooling on the hot-rolled steel billet, wherein the temperature of red return of the first laminar cooling is below 400 ℃, the speed of the first laminar cooling is more than 10 ℃/s, and then carrying out first air cooling to below 200 ℃ to obtain a martensite structure to obtain the steel billet after the first air cooling;
and 4, step 4: heating the steel billet subjected to the first air cooling to 650-;
and 5: carrying out secondary laminar flow cooling on the heat-treated steel billet, wherein the temperature of the second laminar flow cooling is 400-
On the other hand, the invention also provides a manufacturing method of the shock-resistant, fire-resistant and corrosion-resistant thin steel plate, which adopts the shock-resistant, fire-resistant and corrosion-resistant steel, wherein the medium steel plate is a hot continuous rolling steel plate with the thickness of less than or equal to 20 mm; the manufacturing method comprises the following steps:
step 1: heating the continuous casting billet or the cast ingot, and soaking to obtain a soaked billet;
step 2: carrying out hot rolling rough rolling and hot rolling finish rolling on the soaked steel billet to obtain a hot rolled steel plate;
and step 3: carrying out sectional laminar cooling on the hot-rolled steel plate, and coiling at the coiling temperature of 600-700 ℃ to obtain ferrite and bainite tissues so as to obtain a hot continuous rolling coil;
and 4, step 4: carrying out heat treatment on the hot continuous rolling coiled plate for two times to obtain a heat-treated steel plate;
and 5: and carrying out secondary laminar flow cooling on the heat-treated steel plate, wherein the red return temperature of the secondary laminar flow cooling is 400-.
Further, the method comprises the following steps:
step 1: heating the cogging continuous casting billet or the cogging cast ingot, and soaking to obtain a soaked steel billet, wherein the heating temperature is 1180-1250 ℃, and the soaking time is 0.5-3 h;
step 2: carrying out hot rolling rough rolling and hot rolling finish rolling on the soaked steel billet to obtain a hot rolled steel plate, wherein the hot rolling rough rolling is carried out for 3-6 times, the hot rolling finish rolling is carried out for 5-10 times, the initial rolling temperature of the hot rolling rough rolling is 1180-1220 ℃, and the final rolling temperature of the hot rolling finish rolling is 850-950 ℃;
and step 3: carrying out sectional laminar cooling on the hot-rolled steel plate, and coiling at the coiling temperature of 600-700 ℃ to obtain ferrite and bainite tissues so as to obtain a hot continuous rolling coil;
and 4, step 4: and (3) after the hot continuous rolling coiled plate is cut and roughly corrected by a transverse cutting machine set, carrying out twice heat treatment by adopting a pressure quenching heat treatment production line to obtain the heat-treated coiled plate.
And 5: and (3) carrying out secondary laminar flow cooling on the heat-treated coiled plate, wherein the red return temperature of the secondary laminar flow cooling is 400-500 ℃, the speed of the secondary laminar flow cooling is more than 10 ℃/s, and more than 60 wt.% of copper is dissolved in the solution, then carrying out secondary air cooling, and utilizing the residual heat for self-tempering to eliminate stress and carrying out carbon distribution to obtain the anti-seismic, fire-resistant and corrosion-resistant thin steel plate.
Further, the sectional cooling method comprises the following steps: the first section is water-cooled, and the cooling speed of the first section is more than 20 ℃/s; the second section is air cooling, the third section is compensation laminar cooling, and the cooling speed of the third section is 3-10 ℃/s.
Further, in the two heat treatments, the first heat treatment is austenitizing-quenching heat treatment, and the method comprises the following steps: heating to 850-950 ℃ for isothermal treatment, keeping the temperature for 20-60 min, then performing pressure quenching, wherein the temperature of the pressure quenching is below 400 ℃, the laminar cooling speed of the pressure quenching is more than 10 ℃/s, and then air cooling to below 200 ℃ to obtain a martensite structure.
Further, in the two heat treatments, the second heat treatment is two-phase isothermal heat treatment, a pressure quenching heat treatment production line is still adopted, the temperature is heated to 650-700 ℃ for isothermal temperature, and the isothermal time is 0.5-3 h.
Compared with the prior art, the invention has the following beneficial effects:
1) the anti-seismic, fire-resistant and corrosion-resistant steel provided by the invention mainly utilizes the modes of high-temperature solid solution strengthening of Mo, solid solution segregation of Mo, Nb and the like, stable high-temperature tissue precipitation of MC phase and Cu phase nano particles, precipitation strengthening of MC phase and Cu phase nano particles and the like to improve the high-temperature tensile strength, namely the fire resistance; the total amount of austenite stabilizing elements such as Mn, Cu, Ni and the like is controlled, the content of residual austenite at room temperature is controlled by combining heat treatment of a two-phase region, the room temperature plasticity is improved, and the low yield ratio is obtained, namely the anti-seismic performance is ensured; the control of corrosion-resistant alloy elements such as Mo, Ni and Cu and a multiphase structure ensures that the anti-seismic, fire-resistant and corrosion-resistant steel has excellent marine atmospheric corrosion resistance. Particularly, more than 60 wt.% of Cu phase forming elements are in a solid solution state during heat treatment in a two-phase region, are kept to room temperature, and are gradually and rapidly precipitated when the temperature is raised in fire, particularly when the temperature is over 500 ℃, so that the high-temperature strength is enhanced, and the fire resistance is improved.
2) The invention provides a manufacturing method of an anti-seismic, fire-resistant and corrosion-resistant medium plate, which adopts low-C alloy design mainly containing Mn + Ni + Cu and Mo-Nb-V-Ti and other composite micro-alloying to carry out hot rolling, on-line direct quenching and off-line two-phase isothermal heat treatment on a billet obtained by smelting, continuous casting or die casting cogging, and finally obtains a multi-phase structure with precipitation of tempered martensite, residual austenite, MC and Cu, and has comprehensive mechanical properties of high yield strength (600 plus 690MPa grade), anti-seismic performance (low yield ratio of 0.85 and below) and high elongation (18% and above), and meanwhile, the anti-seismic, fire-resistant and corrosion-resistant functions are realized, and the welding performance is good. The key to obtain the multi-phase structure is the alloy design mainly containing low C and Mn + Ni + Cu, the component design of Mo-Nb-V-Ti and other composite micro-alloying and the isothermal heat treatment in a two-phase region, and particularly the Mn + Ni + Cu composite alloying of 3.50-4.50 wt.% synergistically improves the marine atmospheric corrosion resistance; after the two-phase zone isothermal heat treatment, the method of rapid laminar cooling and medium-high temperature interrupted cooling and red return self-tempering is adopted, and the method is combined with Mn + Ni + Cu composite alloying, so that austenite is synergistically stabilized, plasticity is improved, copper is dissolved at room temperature by more than 60 wt%, high-temperature precipitation is performed when the copper is exposed to fire, nano particle precipitation is strengthened, and the fireproof performance is enhanced.
3) The method for manufacturing the shock-resistant, fire-resistant and corrosion-resistant thin steel plate provided by the invention adopts low-C alloy design mainly containing Mn + Ni + Cu and Mo-Nb-V-Ti and other composite micro-alloying, and performs hot continuous rolling, high-temperature coiling, offline quenching and two-phase zone isothermal heat treatment on a billet obtained by smelting, continuous casting or die casting cogging to finally obtain a multi-phase structure with tempered martensite, residual austenite, MC and Cu precipitation, and the multi-phase structure has high yield strength (600 plus 690MPa grade), shock resistance (low yield ratio of 0.85 and below) and high elongation (18% and above) comprehensive mechanical properties, and has the functions of fire resistance and corrosion resistance and good welding performance. The key to obtain the multi-phase structure is the alloy design mainly containing low C and Mn + Ni + Cu, the component design of Mo-Nb-V-Ti and other composite micro-alloying and the isothermal heat treatment in a two-phase region, and particularly the Mn + Ni + Cu composite alloying of 3.50-4.50 wt.% synergistically improves the marine atmospheric corrosion resistance; after the two-phase zone isothermal heat treatment, the method of rapid laminar cooling and medium-high temperature interrupted cooling and red return self-tempering is adopted, and the method is combined with Mn + Ni + Cu composite alloying, so that austenite is synergistically stabilized, plasticity is improved, copper is dissolved at room temperature by more than 60 wt%, high-temperature precipitation is performed when the copper is exposed to fire, nano particle precipitation is strengthened, and the fireproof performance is enhanced.
Additional features and advantages of the invention will be set forth in the description which follows, and in part will be obvious from the description, or may be learned by the practice of the invention. The objectives and other advantages of the invention will be realized and attained by the structure particularly pointed out in the written description and claims thereof.
Detailed Description
The preferred embodiments of the present invention are described in detail below.
The invention provides anti-seismic fireproof corrosion-resistant steel which comprises the following components in percentage by mass: c: 0.05-0.11 wt.%, Si: 0.10-0.30 wt.%, Mn: 1.00-2.00 wt.%, Ni: 1.00-1.50 wt.%, Cu: 1.00-1.50 wt.%, Mo: 0.50-0.60 wt.%, Nb: 0.05-0.10 wt.%, V: 0.05-0.10 wt.%, Ti: 0.010-0.030 wt.%, Al: 0.015-0.035 wt.%, B: 0-0.0018 wt.%, P: <0.015 wt.%, S: <0.010 wt.%, the balance being Fe and unavoidable impurities.
Compared with the prior art, the anti-seismic, fire-resistant and corrosion-resistant steel provided by the invention has the advantages that the high-temperature tensile strength, namely the fire resistance, is improved mainly by using the modes of high-temperature solid solution strengthening of Mo, solid solution segregation of Mo, Nb and the like, stable high-temperature tissue precipitation of MC phase and Cu phase nano particles, precipitation strengthening of MC phase and Cu phase nano particles and the like; the total amount of austenite stabilizing elements such as Mn, Cu, Ni and the like is controlled, the content of residual austenite at room temperature is controlled by combining heat treatment of a two-phase region, the room temperature plasticity is improved, and the low yield ratio is obtained, namely the anti-seismic performance is ensured; the control of corrosion-resistant alloy elements such as Mo, Ni and Cu and a multiphase structure ensures that the anti-seismic, fire-resistant and corrosion-resistant steel has excellent marine atmospheric corrosion resistance. Particularly, more than 60 wt.% of Cu phase forming elements are in a solid solution state during heat treatment in a two-phase region, are kept to room temperature, and are gradually and rapidly precipitated when the temperature is raised in fire, particularly when the temperature is over 500 ℃, so that the high-temperature strength is enhanced, and the fire resistance is improved.
Specifically, in the anti-seismic, fire-resistant and corrosion-resistant steel, the action and the proportion of each element are as follows:
carbon (C): the steel has obvious gap replacement solid solution strengthening effect and improves the hardenability of the steel; is also an element forming the MC phase. The carbon content in the steel is 0.05-0.11 wt.%. Below 0.05 wt.%, high strength is difficult to obtain; above 0.11 wt.%, the tendency to cold crack is exacerbated at higher levels of the steel alloy of the present invention, which is detrimental to weld performance.
Silicon (Si): one of the deoxidizing elements in the steel has strong solid solution strengthening effect, but excessive Si deteriorates the toughness and welding performance of the steel. In combination with the above considerations, the silicon content in the steel of the present invention ranges from 0.10 to 0.30 wt.%.
Manganese (Mn): alloy elements in an open austenite phase region are enriched in an austenite phase during heat treatment and heat preservation in an austenite-ferrite two-phase region, so that the stability of the austenite is improved, and the austenite is favorably kept at room temperature; has certain solid solution strengthening effect and improves the hardenability of the steel. Manganese is the most common alloy element, has high cost performance, and in order to fully exert the effects of solid solution strengthening and hardenability improvement, the content is not less than 1.00 wt.%, but is more than 2.00 wt.% to be unfavorable for controlling the segregation quality of the casting blank and simultaneously reduce the welding performance. The content range of manganese in the steel is 1.00-2.00 wt.%.
Nickel (Ni): the manganese-manganese alloy is also an alloy element of an open austenite phase region, and is enriched in an austenite phase during heat treatment and heat preservation of an austenite-ferrite two-phase region, so that the stability of austenite is improved, and the austenite is favorably kept at room temperature; has certain solid solution strengthening effect, improves the hardenability of the steel, can also promote the proceeding of the cross slip, reduces the resistance of dislocation movement, relaxes the stress and improves the plasticity and toughness of the steel. In addition, the carbon equivalent coefficient of the nickel element is only 1/15, which is beneficial to the welding performance. The nickel is not easy to oxidize and corrode, and has higher atmospheric corrosion resistance when the content of the nickel in the steel is not less than 1.00 wt.%. The content range of nickel in the steel is 1.00-1.50 wt.%.
Copper (Cu): the alloy elements which expand the austenite phase region have larger solid solubility in austenite, relatively smaller solid solubility in ferrite and sensitive change of the solid solubility of copper in the ferrite along with temperature. Therefore, when the heat treatment and heat preservation are carried out in an austenite-ferrite two-phase region, part of copper is enriched in an austenite phase, the stability of austenite is improved, and the improvement of hardenability and the retention of austenite at room temperature are facilitated; a part of copper is in solid solution in ferrite; a part of copper is precipitated in the ferrite as nano-copper particles, and the copper content of the part is sharply reduced along with the increase of the heat treatment temperature of the two-phase zone. The invention adopts the heat treatment of a two-phase region with higher temperature, the rapid cooling is carried out after the heat preservation is finished, and the copper which is dissolved in the martensite (ferrite) and the austenite is heated up in case of fireThe steel is quickly separated out in the process, and the high-temperature strength and the fire resistance of the steel are improved. Copper in steel can promote gamma-Fe2O3The transformation from/gamma-FeOOH to a stable rust layer phase α -FeOOH can be enriched at the cracks of an oxidation or corrosion rust layer, and prevents a corrosion medium from further contacting with a matrix, so the addition of copper can improve the corrosion resistance of steel, in addition, the carbon equivalent coefficient of copper element is only 1/15, which is beneficial to the welding performance, but due to the problem of copper brittleness, the increase of copper needs to correspondingly increase nickel, so the comprehensive cost performance is considered, the copper content range in the steel is 1.00-1.50 wt.%.
Molybdenum (Mo): obviously improves the hardenability, the fire resistance and the marine atmosphere corrosion resistance of the steel and reduces the tempering brittleness. Molybdenum directly strengthens a matrix through solid solution strengthening so as to improve high-temperature strength, also is partially gathered at defects such as an interface of the matrix so as to improve the thermal stability of a structure so as to improve the high-temperature strength, and is cooperated with Nb, V and the like to separate out and refine MC phase nano particles, pin the defects such as the interface, dislocation and the like, and the high-temperature strength is improved through precipitation strengthening and structural thermal stability enhancement. The content of molybdenum in the steel is not less than 0.50 wt.%, and the effects of stabilizing the high-temperature structure and not coarsening the MC phase nano particles are obviously embodied in the two-phase zone heat treatment and the high-temperature stretching at 600 ℃, so that the steel is an important guarantee for obtaining the yield strength of 600-plus 690MPa grade and the high-temperature tensile strength matched with the yield strength, and the marine atmospheric corrosion resistance is excellent. In consideration of comprehensive cost performance, the content of molybdenum in the steel is 0.50-0.60 wt.%.
Niobium (Nb): in controlled rolling, niobium dissolved in austenite and niobium-containing MC phase particles precipitated by deformation induction both have strong effects of inhibiting austenite grain recrystallization and refining grains; the interphase precipitation and the ferrite supersaturation precipitation of niobium-containing MC phase particles have stronger precipitation strengthening effect. The MC phase particles in the steel of the present invention further contain V, Mo and other elements. During heat treatment in a two-phase region and high-temperature stretching at 600 ℃, a small amount of niobium is dissolved in austenite and ferrite, and the niobium is easy to segregate at defects such as interfaces, dislocation and the like, so that the high-temperature structure is stabilized, and the room-temperature and high-temperature yield strength, namely the room-temperature high strength and the fire resistance, can be guaranteed. When the content of niobium is less than 0.05 wt.%, the refractory performance is not guaranteed, and when the content of niobium is more than 0.10 wt.%, the difficulty of smelting and continuous casting is increased and the cost is increased. The niobium content in the steel according to the invention is between 0.05 and 0.10 wt.%.
Vanadium (V): the MC phase is precipitated in cooperation with niobium, molybdenum and the like, and has remarkable precipitation strengthening effect because vanadium carbonitride has relatively large solid solubility product in austenite and large supersaturation degree in a bainite, martensite or ferrite matrix for precipitation in a large amount. And a small amount of vanadium is added, so that the precipitation effect is not obvious. The vanadium content in the steel of the invention is controlled between 0.05 and 0.10 wt.%.
Titanium (Ti): the steel is mainly subjected to micro-titanium treatment, titanium is mainly combined with nitrogen to form nano-sized titanium nitride particles, and austenite grains in the heating process of a casting blank are refined. The nitrogen content in the steel of the invention does not exceed 80 ppm. According to the ideal chemical proportion of the titanium nitride, the content of the titanium is generally not more than 0.030 wt%, and overhigh titanium is easy to form thicker titanium nitride, is not beneficial to refining austenite grains and is harmful to the toughness and the plasticity of the steel. Too low a titanium does not fix nitrogen sufficiently to form an effective amount of titanium nitride. The titanium content in the steel according to the invention ranges from 0.010 to 0.030 wt.%.
Aluminum (Al): aluminum is a strong deoxidizing element and can be combined with nitrogen to form aluminum nitride, so that the function of refining austenite grains can be achieved. The content of aluminum in the steel is 0.015-0.035 wt.%.
Boron (B): the strong segregation is in austenite crystal boundary and other crystal defects, the hardenability is obviously improved, the segregation of the copper-rich liquid phase and the permeation of the copper-rich liquid phase to the inside of the matrix along the crystal boundary can be reduced, and the surface quality of the hot rolled plate is improved. However, excess boron may form boron phases that are detrimental to hot workability and toughness. The inventive steel may be added with boron of not more than 0.0018 wt.%.
Phosphorus (P) and sulfur (S): the content of impurity elements in the steel, which obviously reduces the ductility and the welding performance, is as low as possible without obviously increasing the cost, so that the content is controlled within 0.015 wt.% and 0.010 wt.% respectively.
In order to further improve the comprehensive performance of the shock-resistant, fire-resistant and corrosion-resistant steel, the composition of the shock-resistant, fire-resistant and corrosion-resistant steel can be further adjusted. Illustratively, the composition of the material can be as follows by mass percent: c: 0.05-0.09 wt.%, Si: 0.25-0.28 wt.%, Mn: 1.10-1.80 wt.%, Ni: 1.15-1.45 wt.%, Cu: 1.05-1.45 wt.%, Mo: 0.55-0.58 wt.%, Nb: 0.06-0.09 wt.%, V: 0.058-0.092 wt.%, Ti: 0.015-0.028 wt.%, Al: 0.025-0.030 wt.%, B: 0.0002-0.0012 wt.%, P: <0.015 wt.%, S: <0.010 wt.%, the balance being Fe and unavoidable impurities.
The boron content of the steel sheet having a thickness of 40mm or more is 0.0008 to 0.0018 wt.%. This is because the cooling rate of the central portion of the steel sheet having a thickness of 40mm or more is slow, and boron needs to be added to improve the hardenability of the steel sheet, so that the martensite structure is obtained also at the central portion of the steel sheet having a thickness of 40mm or more.
On the other hand, the invention also provides a manufacturing method of the shock-resistant, fire-resistant and corrosion-resistant medium steel plate, the medium steel plate is a steel plate with the thickness of more than 20mm, the manufacturing method adopts converter or electric furnace smelting, casting adopts continuous casting or die casting, and the medium steel plate can be produced by adopting a medium plate mill and a common quenching heat treatment or pressure quenching heat treatment production line, and the method comprises the following steps:
step 1: placing the cogging continuous casting billet or the cogging cast ingot into a heating furnace for heating and soaking to obtain a soaked billet, wherein the heating temperature is 1180-1250 ℃, and the soaking time is 0.5-3 h;
step 2: carrying out hot rolling rough rolling and hot rolling finish rolling on the soaked steel billet by adopting a medium plate rolling mill to obtain a hot rolled steel plate, wherein the hot rolling rough rolling is carried out for 3-6 times, the hot rolling finish rolling is carried out for 5-10 times, the initial rolling temperature of the hot rolling rough rolling is 1180-1220 ℃, the final rolling temperature of the hot rolling rough rolling is 1135-1170 ℃, the initial rolling temperature of the hot rolling finish rolling is 995-1010 ℃, and the final rolling temperature of the hot rolling finish rolling is 850-950 ℃;
and step 3: carrying out first laminar cooling on the hot-rolled steel billet, wherein the temperature of red return of the first laminar cooling is below 400 ℃, the speed of the first laminar cooling is more than 10 ℃/s, and then carrying out first air cooling to below 200 ℃ to obtain a martensite structure to obtain the steel billet after the first air cooling;
and 4, step 4: carrying out heat treatment on the billet subjected to the first air cooling to obtain a billet subjected to heat treatment, heating to 650-700 ℃ to carry out two-phase zone isothermal heat treatment, wherein the heat preservation time is 0.5-3 h;
and 5: and carrying out secondary laminar flow cooling on the heat-treated steel billet, wherein the temperature of the second laminar flow cooling is 400-500 ℃, the speed of the second laminar flow cooling is more than 10 ℃/s, and more than 60 wt.% of copper is dissolved in the steel billet, and then carrying out secondary air cooling.
Compared with the prior art, the manufacturing method of the anti-seismic, fire-resistant and corrosion-resistant medium plate provided by the invention adopts low-C alloy design mainly containing Mn + Ni + Cu and Mo-Nb-V-Ti and other composite micro-alloying, and carries out hot rolling, on-line direct quenching and off-line two-phase isothermal heat treatment on the billet obtained by smelting, continuous casting or die casting cogging, and finally obtains the multi-phase structure with tempered martensite, residual austenite, MC and Cu precipitation, and the multi-phase structure has high yield strength (600-690MPa grade), anti-seismic performance (low yield ratio of 0.85 and below) and high elongation (18% and above), and simultaneously has the functions of fire resistance and corrosion resistance and good welding performance. The key to obtain the multi-phase structure is the alloy design mainly containing low C and Mn + Ni + Cu, the component design of Mo-Nb-V-Ti and other composite micro-alloying and the isothermal heat treatment in a two-phase region, and particularly the Mn + Ni + Cu composite alloying of 3.50-4.50 wt.% synergistically improves the marine atmospheric corrosion resistance; after the two-phase zone isothermal heat treatment, the method of rapid laminar cooling and medium-high temperature interrupted cooling and red return self-tempering is adopted, and the method is combined with Mn + Ni + Cu composite alloying, so that austenite is synergistically stabilized, plasticity is improved, more than 60 wt% of copper (mass percentage of the dissolved copper in the total copper content) is dissolved at room temperature, high-temperature precipitation is carried out when the copper meets fire, nano particle precipitation is strengthened, the fire resistance is enhanced, and the effect is remarkable.
It should be noted that the second laminar flow is cooled to 400-500 ℃ and then air-cooled, the residual heat is fully utilized to eliminate the martensite phase transformation stress and carry out carbon distribution, and the self-tempering effect is generated, so that the steel plate obtains better toughness, plasticity and processing performance.
Particularly, after two-phase isothermal heat treatment in a steel sheet with the thickness of less than 16mm produced in a medium and heavy plate production line, a pressure quenching machine is adopted for pressure laminar cooling to improve the plate shape, and stacking air cooling is carried out after laminar cooling.
In another aspect, the present invention provides a method for manufacturing a shock-resistant, fire-resistant and corrosion-resistant thin steel sheet, wherein the thin steel sheet is a hot continuous rolled steel sheet with a thickness of 20mm or less, the manufacturing method comprises the following steps:
step 1: placing the cogging continuous casting billet or the cogging cast ingot into a heating furnace for heating and soaking to obtain a soaked billet, wherein the heating temperature is 1180-1250 ℃, and the soaking time is 0.5-3 h;
step 2: carrying out hot rolling rough rolling and hot rolling finish rolling on the soaked steel billet by adopting a medium plate rolling mill to obtain a hot rolled steel plate, wherein the hot rolling rough rolling is carried out for 3-6 times, the hot rolling finish rolling is carried out for 5-10 times, the initial rolling temperature of the hot rolling rough rolling is 1180-1220 ℃, and the final rolling temperature of the hot rolling finish rolling is 850-950 ℃;
and step 3: carrying out sectional laminar cooling and coiling on the hot rolled steel plate, carrying out large-water-volume laminar rapid cooling on a first section, wherein the cooling speed of the first section is more than 20 ℃/s, the cooling speed of a second section is air cooling, the cooling speed of a third section is 3-10 ℃/s, the coiling temperature is 600-700 ℃, obtaining a ferrite and bainite tissue, and obtaining a hot continuous rolling coiled plate;
and 4, step 4: and (3) after the hot continuous rolling coiled plate is cut and roughly corrected by a transverse cutting machine set, carrying out twice heat treatment by adopting a pressure quenching heat treatment production line to obtain the heat-treated coiled plate.
Wherein the first heat treatment is austenitizing-quenching heat treatment, heating to 850-950 ℃ for isothermal temperature preservation for 20-60 min, then performing pressure quenching, the temperature of the pressure quenching is below 400 ℃, the laminar cooling speed of the pressure quenching is more than 10 ℃/s, and then air cooling is performed to below 200 ℃ to obtain the martensite structure.
The second heat treatment is isothermal heat treatment in two phase regions, a pressure quenching heat treatment production line is still adopted, the temperature is increased to 650-700 ℃ for isothermal treatment, and the isothermal time is 0.5-3 h.
And 5: and carrying out secondary laminar flow cooling on the steel plate after heat treatment, wherein the red return temperature of the secondary laminar flow cooling is 400-500 ℃, the speed of the secondary laminar flow cooling is more than 10 ℃/s, and more than 60 wt.% of copper is dissolved in the solution, and then carrying out secondary air cooling.
Compared with the prior art, the method for manufacturing the shock-resistant, fire-resistant and corrosion-resistant thin steel plate provided by the invention adopts low-C alloy design mainly containing Mn + Ni + Cu and Mo-Nb-V-Ti and other composite micro-alloying, and performs hot continuous rolling-high-temperature coiling-off-line quenching + two-phase zone isothermal heat treatment on a billet obtained by smelting, continuous casting or die casting cogging to finally obtain a multi-phase structure with tempered martensite + residual austenite + MC and Cu precipitation, and has the comprehensive mechanical properties of high yield strength (600 plus 690MPa grade) and shock resistance (low yield ratio (0.85 and below) and high elongation (18% and above)), and meanwhile, the shock-resistant, fire-resistant and corrosion-resistant thin steel plate has good welding performance. The key to obtain the multi-phase structure is the alloy design mainly containing low C and Mn + Ni + Cu, the component design of Mo-Nb-V-Ti and other composite micro-alloying and the isothermal heat treatment in a two-phase region, and particularly the Mn + Ni + Cu composite alloying of 3.50-4.50 wt.% synergistically improves the marine atmospheric corrosion resistance; after the two-phase zone isothermal heat treatment, the method of rapid laminar cooling and medium-high temperature interrupted cooling and red return self-tempering is adopted, and the method is combined with Mn + Ni + Cu composite alloying, so that austenite is synergistically stabilized, plasticity is improved, copper is dissolved at room temperature by more than 60 wt%, high-temperature precipitation is performed when the copper is exposed to fire, nano particle precipitation is strengthened, and the fireproof performance is enhanced.
Particularly, the thin plates with the thickness of 16mm or less are stacked and air-cooled after the second pressure quenching laminar cooling, the thin plates are stacked and cooled slowly, the martensite phase transformation stress is eliminated and carbon distribution is carried out by fully utilizing waste heat, and the self-tempering effect is generated, so that the steel plate has better toughness and plasticity and processing performance.
Example 1: heating the casting blank to 1180 ℃, keeping the temperature for 2h, keeping the initial rolling temperature of rough rolling at 1200 ℃, carrying out 3-pass rough rolling, keeping the final rolling temperature of rough rolling at 1035 ℃, keeping the initial rolling temperature of finish rolling at 1000 ℃, keeping the final rolling temperature of finish rolling at 885 ℃, and carrying out 5-pass finish rolling to roll the thickness of the steel plate to 40 mm; carrying out laminar flow cooling on the steel plate at a cooling speed of 18 ℃/s to 390 ℃, and then air-cooling to room temperature; keeping the temperature of the steel plate in a heating furnace at 700 ℃ for 0.5h, carrying out laminar flow cooling on the steel plate to 405 ℃ at a cooling speed of 18 ℃/s, and then carrying out air cooling to room temperature.
Example 2: heating the casting blank to 1200 ℃, preserving heat for 2h, wherein the initial rolling temperature of rough rolling is 1200 ℃, carrying out 3-pass rough rolling, the final rolling temperature of rough rolling is 1055 ℃, the initial rolling temperature of finish rolling is 995 ℃, the final rolling temperature of finish rolling is 860 ℃, and carrying out 6-pass finish rolling to roll the thickness of the steel plate to 25 mm; carrying out laminar flow cooling on the steel plate at a cooling speed of 15 ℃/s to 364 ℃, and then air-cooling to room temperature; keeping the temperature of 680 ℃ in a heating furnace for 1.5h, carrying out laminar flow cooling on the steel plate to 420 ℃ at the cooling speed of 18 ℃/s, and then air-cooling to room temperature.
Example 3: heating the casting blank to 1200 ℃, preserving heat for 2h, wherein the initial rolling temperature of rough rolling is 1200 ℃, performing 4-pass rough rolling, the final rolling temperature of rough rolling is 1070 ℃, the initial rolling temperature of finish rolling is 1010 ℃, the final rolling temperature of finish rolling is 901 ℃, performing 6-pass finish rolling, and rolling the thickness of the steel plate to 12 mm; carrying out laminar flow cooling on the steel plate to 395 ℃ at a cooling speed of 20 ℃/s, and then air-cooling to room temperature; keeping the temperature of 660 ℃ in a heating furnace for 3h, carrying out laminar flow cooling on the steel plate to 435 ℃ at the cooling speed of 15 ℃/s, and then air-cooling to room temperature.
Example 4: heating the casting blank to 1200 ℃, preserving heat for 2h, wherein the initial rolling temperature of rough rolling is 1200 ℃, carrying out 3-pass rough rolling and 6-pass finish rolling, and the finish rolling temperature is 893 ℃, and rolling the thickness of the steel plate to 20 mm; carrying out laminar cooling on the steel plate to 663 ℃ at a front section cooling speed of 22 ℃/s and a rear section cooling speed of 5 ℃/s, and then air-cooling to room temperature; keeping the temperature of the steel plate in a heating furnace at 900 ℃ for 45min, carrying out laminar flow cooling on the steel plate to 382 ℃ at a cooling speed of 17 ℃/s, then keeping the temperature in the heating furnace at 700 ℃ for 0.5h, carrying out laminar flow cooling on the steel plate to 466 ℃ at a cooling speed of 18 ℃/s, and then carrying out air cooling to room temperature.
Example 5: heating the casting blank to 1200 ℃, preserving heat for 2h, wherein the initial rolling temperature of rough rolling is 1200 ℃, carrying out rough rolling for 4 times, carrying out finish rolling for 6 times, and the finish rolling temperature is 872 ℃, and rolling the thickness of the steel plate to 12 mm; carrying out laminar cooling on the steel plate to 628 ℃ at a front section cooling speed of 23 ℃/s and a rear section cooling speed of 7 ℃/s, and then air-cooling to room temperature; keeping the temperature in a heating furnace at 880 ℃ for 45min, carrying out laminar flow cooling on the steel plate to 375 ℃ at a cooling speed of 15 ℃/s, then keeping the temperature in the heating furnace at 680 ℃ for 1.5h, carrying out laminar flow cooling on the steel plate to 437 ℃ at a cooling speed of 17 ℃/s, and then air-cooling to room temperature.
Example 6: heating the casting blank to 1200 ℃, preserving heat for 2h, wherein the initial rolling temperature of rough rolling is 1200 ℃, carrying out 4-pass rough rolling and 7-pass finish rolling, and the finish rolling temperature is 905 ℃, and rolling the thickness of the steel plate to 6 mm; carrying out laminar cooling on the steel plate to 694 ℃ at a front section cooling speed of 21 ℃/s and a rear section cooling speed of 5 ℃/s, and then air-cooling to room temperature; keeping the temperature in a heating furnace at 880 ℃ for 45min, carrying out laminar flow cooling on the steel plate to 393 ℃ at a cooling speed of 18 ℃/s, then keeping the temperature in the heating furnace at 660 ℃ for 13h, carrying out laminar flow cooling on the steel plate to 465 ℃ at a cooling speed of 15 ℃/s, and then air-cooling to room temperature.
The mechanical property test of each steel plate is carried out, and the results are shown in table 4, and it can be seen from the table that the room temperature yield strength of examples 1, 3, 4 and 5 reaches 690MPa level, the room temperature yield strength of examples 2 and 6 reaches 600MPa level, and the yield ratio of each steel plate is not higher than 0.85. The elongation is not lower than 18 percent; the yield strength at 620 ℃ is greater than 2/3 of the yield strength standard at room temperature, which indicates good fire resistance.
And then, carrying out corrosion resistance tests on the six steel plates, wherein the experimental conditions are as follows: the steel plates are soaked in an artificial seawater solution at room temperature (the components are shown in table 5), the common Q345GJ steel is taken as a comparison steel plate, the corrosion result is shown in table 6, the corrosion result of the common Q345GJ steel plate is 1, and the corrosion result of the six steel plates is not higher than 30% of the corrosion result of the Q345 steel plate, which shows that the six steel plates have good corrosion resistance.
Table 1 chemical composition (wt.%) of ultra-high strength shock-resistant, fire-resistant, corrosion-resistant steel
| C | Si | Mn | Mo | Ni | Cu | Ti | B | Nb | V | Al | P | S | |
| Example 1 | 0.09 | 0.25 | 1.50 | 0.58 | 1.25 | 1.25 | 0.015 | 0.0002 | 0.085 | 0.085 | 0.025 | 0.008 | 0.002 |
| Example 2 | 0.05 | 0.28 | 1.80 | 0.55 | 1.35 | 1.35 | 0.028 | 0.0004 | 0.060 | 0.063 | 0.027 | 0.008 | 0.003 |
| Example 3 | 0.08 | 0.21 | 1.35 | 0.57 | 1.45 | 1.45 | 0.018 | 0.0012 | 0.090 | 0.087 | 0.030 | 0.005 | 0.003 |
| Example 4 | 0.09 | 0.28 | 1.10 | 0.58 | 1.25 | 1.45 | 0.025 | 0.0003 | 0.090 | 0.092 | 0.030 | 0.006 | 0.002 |
| Example 5 | 0.08 | 0.25 | 1.50 | 0.58 | 1.15 | 1.05 | 0.016 | 0.0005 | 0.090 | 0.088 | 0.028 | 0.006 | 0.003 |
| Example 6 | 0.07 | 0.25 | 1.13 | 0.57 | 1.25 | 1.25 | 0.015 | 0.0002 | 0.060 | 0.058 | 0.028 | 0.009 | 0.003 |
TABLE 2 Rolling and Heat treatment Process for ultra-high strength shock-resistant, fire-resistant and corrosion-resistant medium plate
TABLE 3 Rolling and Heat treatment Process for ultrahigh strength shock-resistant, fire-resistant, corrosion-resistant Hot-rolled thin Steel sheet
TABLE 4 mechanical Properties of the ultra-high-strength shock-resistant, fire-resistant, and corrosion-resistant steels
TABLE 5 chemical composition in Artificial seawater
| Compound (I) | Concentration g/L | Compound (I) | Concentration g/L |
| NaCl | 24.53 | NaHCO3 | 0.201 |
| MgCl2 | 5.20 | KBr | 0.101 |
| Na2SO4 | 4.09 | H3BO3 | 0.027 |
| CaCl2 | 1.16 | SrCl2 | 0.025 |
| KCl | 0.695 | NaF | 0.003 |
TABLE 6 Corrosion resistance of ultra-high strength shock-resistant, fire-resistant and corrosion-resistant steel in artificial seawater
The above description is only for the preferred embodiment of the present invention, but the scope of the present invention is not limited thereto, and any changes or substitutions that can be easily conceived by those skilled in the art within the technical scope of the present invention are included in the scope of the present invention.
Claims (5)
1. The manufacturing method of the shock-resistant, fire-resistant and corrosion-resistant thin steel plate is characterized in that the thin steel plate is a hot continuous rolling steel plate with the thickness less than or equal to 20 mm;
the manufacturing method comprises the following steps:
step 1: heating and soaking the continuous casting blank or the cast ingot to obtain a soaked steel blank, specifically heating and soaking the cogging continuous casting blank or the cogging cast ingot to obtain a soaked steel blank, wherein the heating temperature is 1180-;
step 2: carrying out hot rolling rough rolling and hot rolling finish rolling on the soaked steel billet to obtain a hot rolled steel plate, wherein the hot rolling rough rolling is carried out for 3-6 times, the hot rolling finish rolling is carried out for 5-10 times, the initial rolling temperature of the hot rolling rough rolling is 1180-1220 ℃, and the final rolling temperature of the hot rolling finish rolling is 850-950 ℃;
and step 3: carrying out sectional laminar cooling on the hot-rolled steel plate, and coiling at the coiling temperature of 600-700 ℃ to obtain ferrite and bainite tissues so as to obtain a hot continuous rolling coil; and 4, step 4: performing heat treatment on the hot continuous rolling coiled plate twice to obtain a heat-treated steel plate, specifically, performing heat treatment twice by adopting a pressure quenching heat treatment production line after the hot continuous rolling coiled plate is cut and roughly corrected by a transverse cutting unit to obtain a heat-treated coiled plate;
and 5: carrying out secondary laminar flow cooling on the steel plate after heat treatment, wherein the temperature of the red return of the secondary laminar flow cooling is 400-;
the manufacturing method of the shock-resistant, fire-resistant and corrosion-resistant thin steel plate adopts the following components: c: 0.05-0.11 wt.%, Si: 0.10-0.30 wt.%, Mn: 1.00-2.00 wt.%, Ni: 1.00-1.50 wt.%, Cu: 1.00-1.50 wt.%, Mo: 0.50-0.60 wt.%, Nb: 0.05-0.10 wt.%, V: 0.05-0.10 wt.%, Ti: 0.010-0.030 wt.%, Al: 0.015-0.035 wt.%, B: 0-0.0018 wt.%, P: <0.015 wt.%, S: <0.010 wt.%, the balance being Fe and unavoidable impurities.
2. A method for manufacturing a steel sheet according to claim 1, wherein the sectional cooling method comprises: the first section is water-cooled, and the cooling speed of the first section is more than 20 ℃/s; the second section is air cooling, the third section is compensation laminar cooling, and the cooling speed of the third section is 3-10 ℃/s.
3. The method for manufacturing a steel sheet according to claim 1 or 2, wherein the first heat treatment of the two heat treatments is an austenitizing-quenching heat treatment, comprising the steps of: heating to 850-950 ℃ for isothermal treatment, keeping the temperature for 20-60 min, then performing pressure quenching, wherein the temperature of the pressure quenching is below 400 ℃, the laminar cooling speed of the pressure quenching is more than 10 ℃/s, and then air cooling to below 200 ℃ to obtain a martensite structure.
4. The method for manufacturing a steel sheet as claimed in claim 3, wherein the second heat treatment is isothermal heat treatment in two phases, and the isothermal time is 0.5-3h when the steel sheet is heated to 650-.
5. A method for manufacturing a steel sheet according to claim 4, wherein the steel sheet comprises the following components: c: 0.05-0.09 wt.%, Si: 0.25-0.28 wt.%, Mn: 1.10-1.80 wt.%, Ni: 1.15-1.45 wt.%, Cu: 1.05-1.45 wt.%, Mo: 0.55-0.58 wt.%, Nb: 0.06-0.09 wt.%, V: 0.058-0.092 wt.%, Ti: 0.015-0.028 wt.%, Al: 0.025-0.030 wt.%, B: 0.0002-0.0012 wt.%, P: <0.015 wt.%, S: <0.010 wt.%, the balance being Fe and unavoidable impurities.
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