CN115537664B - Hot-rolled pickled enamel steel with yield strength more than or equal to 300MPa after enameling and production method thereof - Google Patents
Hot-rolled pickled enamel steel with yield strength more than or equal to 300MPa after enameling and production method 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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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B37/00—Control devices or methods specially adapted for metal-rolling mills or the work produced thereby
- B21B37/74—Temperature control, e.g. by cooling or heating the rolls or the product
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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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- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
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- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
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- 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
- C21D8/0278—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular surface treatment
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
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- C—CHEMISTRY; METALLURGY
- 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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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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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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23D—ENAMELLING OF, OR APPLYING A VITREOUS LAYER TO, METALS
- C23D3/00—Chemical treatment of the metal surfaces prior to coating
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- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23G—CLEANING OR DE-GREASING OF METALLIC MATERIAL BY CHEMICAL METHODS OTHER THAN ELECTROLYSIS
- C23G1/00—Cleaning or pickling metallic material with solutions or molten salts
- C23G1/02—Cleaning or pickling metallic material with solutions or molten salts with acid solutions
- C23G1/08—Iron or steel
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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
- C21D2211/009—Pearlite
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- Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
- Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
- Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
- Y02P10/00—Technologies related to metal processing
- Y02P10/20—Recycling
Abstract
The invention provides hot-rolled and pickled enamel steel with yield strength more than or equal to 300MPa after enameling and a production method thereof, wherein the steel comprises the following components: c:0.04 to 0.07 percent; si is less than or equal to 0.03%; mn:0.50 to 0.65 percent; p is less than or equal to 0.020%; s:0.010 to 0.025 percent; al:0.010 to 0.060 percent; ti:0.030% -0.060%; cu:0.001% -0.050%, cr:0.001% -0.050%, V:0.001% -0.040%, mo:0.001% -0.030%, ni:0.001% -0.030%, and the balance of Fe and unavoidable impurities. The hot-rolled pickled enamel steel with excellent enameling performance is produced through the design of the production process, and the yield strength reduction value before and after enameling is less than or equal to 50MPa, so that the hot-rolled pickled enamel steel has excellent anti-scaling performance and adhesion performance.
Description
Technical Field
The invention belongs to the field of metal materials, and particularly relates to hot-rolled and pickled enamel steel with yield strength more than or equal to 300MPa after enameling and a production method thereof.
Background
An enamelled steel sheet is a novel composite material in which inorganic vitreous materials are fused and coagulated on a base steel sheet and firmly combined with the steel sheet. Enamel coating is carried out on the surface of the steel plate to prevent the steel plate from rusting, so that an oxide layer is not formed on the surface of the steel plate when the steel plate is heated, and the steel plate can resist corrosion of various liquids. The enamel product is safe and nontoxic, is easy to wash and clean, can be widely used as a food appliance and a washing appliance used in daily life, and has the excellent performances of high hardness, high temperature resistance, wear resistance, insulation effect and the like on a metal blank under specific conditions, so that the enamel product has wider application.
The enamel steel for the pressure-bearing container needs to have certain strength requirement after enameling, and is subjected to enameling at 820-860 ℃ for 5-10min and cooled to room temperature with yield strength not less than 300MPa. The yield strength of the existing steel for hot rolling enamel is greatly reduced before and after enameling, the yield strength is more than or equal to 80MPa before and after enameling, and the yield strength of the steel plate before enameling is higher to meet the service requirement of the product after enameling, so that the processing and forming of users are difficult. The high-strength cold-rolled enamel steel can partially meet the use requirement of high strength, but the thickness of the high-strength cold-rolled enamel steel is not more than 2.5mm, and cannot meet the use requirement of thick specification.
Patent publication number CN 103510011a, "high-strength steel sheet for enamel liner and method for manufacturing same," published in 1 month 15 2014 provides a high-strength steel sheet for enamel liner, C:0.04% -0.10%, si: less than or equal to 0.05 percent, mn:0.60% -1.2%, P: less than or equal to 0.015 percent, S: less than or equal to 0.010 percent, ti:0.04% -0.12%, als:0.005% -0.060%, cr:0.08% -0.30% and the balance of iron and unavoidable impurities. Heating the continuous casting blank to 1180-1250 ℃, and descaling with high-pressure water and rough rolling and cogging after soaking; finish rolling is started at 1100-980 ℃ and rolling is ended at 950-880 ℃; after laminar cooling, coiling is carried out in a temperature range of 570-660 ℃; the steel coil is flattened after natural cooling, the elongation is 0.6% -1.5%, the elongation of the flattened steel plate is 0.8% -1.7% after stretching and straightening, and then the steel plate is pickled. The yield strength of the steel plate is above 450MPa, the steel plate is difficult to process and shape in the using process of a user, the requirement on forming equipment is high, and the yield strength reduction value of the steel plate before and after enameling is large.
The patent publication No. CN 105349884A, published in 24 and 2 in 2016, provides a Ti-containing hot-rolled pickled enamel steel strip and a production method thereof, wherein the Ti-containing hot-rolled pickled enamel steel strip comprises the following chemical components in percentage by weight: 0.05-0.08%, ti:0.030-0.045%, mn:0.65-0.80%, P:0.01% -0.025%, S:0.001% -0.01%, als:0.015-0.050%, si less than or equal to 0.03%, and Fe and unavoidable impurities as the rest. The obtained Ti-containing hot-rolled pickled enamel steel strip has the yield strength of 330-430MPa, the tensile strength of 400-520MPa and the elongation of more than 22 percent, and has high formability and high anti-scaling performance. The yield strength of the steel plate before and after enameling is large in reduction value, and cannot meet the requirement that the yield strength after enameling is more than or equal to 300MPa, so that the service life is influenced.
The steel plate disclosed in patent publication No. CN 107574375A, 1.12.2018, namely the hot-rolled pickled steel plate for double-sided enamel with excellent enameling performance and a manufacturing method thereof comprises the following chemical components in percentage by weight: c:0.010-0.020%, mn:0.5-1.0%, si less than or equal to 0.10%, P less than or equal to 0.02%, S:0.03 to 0.05 percent, als less than or equal to 0.01 percent, cu:0.20 to 0.40 percent of Nb:0.03 to 0.06 percent of O: 0.004-0.010%, and the balance of Fe and other unavoidable impurities; the structure is ferrite and a small amount of cementite, and a large amount of spherical and linear composite inclusions are uniformly distributed in the steel. The invention forms a large number of inclusions uniformly dispersed in steel through component design and smelting control, can be used as traps to avoid enamel scale explosion defects, has higher scale explosion resistance than that of a common acid-washed steel plate, and can be used for double-sided enameling. The inclusions exist in a spherical and linear composite form, and a large number of plastic inclusion particles exist, so that adverse effects of the inclusions on the processing performance of the steel plate are reduced. The yield strength of the steel plate before and after enameling is reduced by a large value, and the yield strength after enameling is not smaller than 300MPa, so that the service life is influenced.
Disclosure of Invention
The invention aims to provide hot-rolled and pickled enamel steel with yield strength more than or equal to 300MPa after enameling and a production method thereof, wherein Ti and Cu are added into carbon-manganese steel to improve the anti-scaling performance and the adhesion performance, a proper amount of Cr, V, mo, ni is added to improve the hot strength of a steel plate, and a reasonable process is matched, so that the influence of enameling on the reduction of the yield strength of the steel plate is reduced, the anti-scaling performance of the steel plate is improved, the hot-rolled and pickled enamel steel plate with surface quality FC grade is produced, the steel plate is subjected to enameling for 5-10min at 820-860 ℃ and cooled to room temperature, the yield strength after enameling is more than or equal to 300MPa, the yield strength reduction value before and after enameling is less than or equal to 50MPa, and the steel plate has excellent anti-scaling performance and adhesion performance.
The specific technical scheme of the invention is as follows:
the hot-rolled pickled enamel steel with the yield strength of more than or equal to 300MPa after enamelling comprises the following components in percentage by mass:
c:0.04 to 0.07 percent; si is less than or equal to 0.03%; mn:0.50 to 0.65 percent; p is less than or equal to 0.020%; s:0.010 to 0.025 percent; al:0.010 to 0.060 percent; ti:0.030% -0.060%; cu:0.001% -0.050%, cr:0.001% -0.050%, V:0.001% -0.040%, mo:0.001% -0.030%, ni:0.001% -0.030%, and the balance of Fe and unavoidable impurities.
The components of the hot-rolled and pickled enamel steel with the yield strength more than or equal to 300MPa after enamelling meet the following conditions: cr+Ni+Mo+V is more than or equal to 0.015 percent.
The invention provides a production process of hot-rolled and pickled enamel steel with yield strength more than or equal to 300MPa after enamelling, which comprises the following process flows:
steelmaking, heating, hot rolling, pickling, rinsing and oiling.
The steelmaking requires front slag skimming and rear slag skimming, secondary ladle top slag modification and RH adopts a light treatment process.
The heating is carried out, when the casting blank is cold packed, namely, the casting blank charging temperature is less than or equal to 400 ℃, the time for heating the casting blank to 1100 ℃ is controlled within 2.5 hours, the time for heating the casting blank to 1100-1200 ℃ is controlled within 0.5-1 hour, and the casting blank discharging temperature is controlled within 1180-1200 ℃;
the heating is carried out, when the casting blank is hot-packed, namely, the casting blank is fed into the furnace at a temperature of more than 400 ℃, the time of the casting blank at 1100-1200 ℃ is controlled to be 0.5-1 h, the total furnace time is controlled to be within 3h, and the casting blank discharging temperature is controlled to be 1180-1215 ℃.
The invention controls the heating process, and aims to reduce the thickness of oxide scales on the surface of a casting blank, improve the uniformity of crystal grains of the casting blank and prevent the excessive growth of the crystal grains; according to the solid solubility product formula of Ti and C, S element, if the tapping temperature is too high, ti is caused 4 C 2 S 2 Or the TiS is dissolved back, and fine TiC is separated out in the subsequent rolling or laminar cooling process, so that the yield strength of the product in a hot rolled state is too high, and the forming processing of the product is not facilitated. The casting blank has long furnace time, coarse austenite grains, more iron scales, and coarse grains at 1100-1200 ℃, and has large temperature difference between the inside and the outside of the casting blank and uneven grains.
The hot rolling: the final rolling temperature is controlled at 840-870 ℃, the coiling temperature is controlled at 550-580 ℃, full-length sparse cooling is adopted, and the cooling speed is 30+/-5 ℃/S. For the tail temperature of a thin intermediate billet, the final rolling temperature is set to be too high to hit, the tail flick is very easy to influence the production stability after finish rolling, meanwhile, the final rolling temperature is high, and at a certain coiling temperature, the cooling rate after rolling is improved, the grain refinement of a hot rolled product is facilitated, and the hot rolled yield strength is high; the method adopts a proper lower coiling temperature and a post-rolling sparse cooling mode, and aims to reduce precipitation and growth of hot-rolled TiC particles, reduce the post-rolling cooling rate, prevent excessive refinement of hot-rolled grains, reduce the yield strength of the hot-rolled product and reduce the difficulty of processing and forming in the use process of a user. Ti, C and other elements dissolved in steel separate out fine dispersed TiC particles as effective hydrogen traps in the subsequent enamel firing and cooling process, so that the anti-scaling performance is improved.
The acid washing: to reasonably control the pickling speed, the following considerations are mainly used: if the pickling speed is too low, overeating may occur; if the pickling speed is too high, underpickling may result, affecting the surface quality. Comprehensively considering that the pickling speed Vs is controlled to be 50-150 m/min, and the thickness H of the oxidized iron scale on the surface of the hot rolled steel plate is 50-90 mu m; preferably, the target value of the pickling speed vs=9000/H-40, and the control range of Vs is target value ±10; the unit of the pickling speed Vs is m/min, the unit of the thickness H of the oxide scale on the surface of the hot rolled steel plate is mu m, and the numerical calculation of the unit is carried out when the formula is calculated. When the iron scale is thick, the pickling speed is reduced, and the iron scale is ensured to be removed cleanly; when the iron scale is thin, the pickling speed is improved, and the steel plate is ensured to be over pickled. The pickling solution is added with inhibitor with the mass concentration of 0.5-3 per mill, and the process can lead the surface quality of the steel plate to reach the FC level. The surface of the steel plate is not undershot or overshot (the surface quality is affected by the residual iron scale on the undershot surface, and small pits are formed on the surface of the overshot steel plate), so that the surface state is optimal.
The rinsing: the desalted water is adopted for rinsing, the pH value is 6.5-7.5, the concentration of Cl ions is less than or equal to 0.5mg/L, the surface of the steel plate is ensured to be cleaned, and the oxidation of the steel plate after rinsing and before squeezing is inhibited.
The oil coating is as follows: and (3) adopting easy-to-clean rust-preventive oil.
The steel structure for hot rolling and pickling enamel with the yield strength more than or equal to 300MPa after enameling is ferrite and a small amount of pearlite; wherein the area proportion of pearlite is 5% -15%, the pearlite is too little, the yield strength before enameling is low, the pearlite is too much, and the difference between the yield strength before enameling and the yield strength after enameling is too large. The grain size grade of the hot-rolled and acid-washed enamel steel with the yield strength more than or equal to 300MPa after enameling is between 9.0 and 11.0, the difference between the grain size grades before and after enameling is less than or equal to 2.0, the enameling can lead crystal grains to grow, if the grain size grade after enameling is too low, the crystal grains are coarse, the forming is not facilitated, and the yield strength before and after enameling cannot meet the requirement.
The yield strength of the hot-rolled and pickled enamel steel after enameling is more than or equal to 300MPa grade, the yield strength of the steel is 330-400MPa, the tensile strength is 390-490MPa, and the elongation of A50 is more than or equal to 32%. The surface quality of the steel plate reaches FC grade and above.
The hot-rolled pickled enamel steel with the yield strength of more than or equal to 300MPa after enameling is subjected to enameling at 820-860 ℃ for 5-10min and cooled to room temperature, the yield strength after enameling is more than or equal to 300MPa, and the yield strength reduction value before and after enameling is less than or equal to 50MPa, so that the hot-rolled pickled enamel steel has excellent anti-fishscaling performance and adhesion performance.
The design idea of the invention is as follows:
c: c is the most economical and effective solid solution strengthening element for improving strength, C content is increased, pearlite formed is increased, strength is increased, but plasticity and formability of steel are reduced, and weldability is unfavorable, and in addition, when C content is too high, a large amount of bubbles are generated in a enameling process, pinhole defects are generated after enameling, so that the control range of C percentage in the invention is 0.04% -0.07% from the viewpoints of economy and comprehensive performance.
Si: the Si content is too high, oxide scales on the surface of the steel plate are not easy to remove, microcracks pressed by oxides are easy to form on the surface, and the steel plate is easy to crack in the cold forming process when the steel plate is used as a crack source, so that the control range of the Si percentage in the invention is less than or equal to 0.03 percent.
Mn: mn can reduce the transformation temperature of austenite to ferrite (just can compensate the transformation temperature rise of austenite to ferrite caused by the reduction of C element content), enlarges the hot working temperature range, is favorable for refining the ferrite grain size, but has overhigh Mn content, the Mn segregation degree of casting blanks is increased in the continuous casting process, the central part of the thickness of the steel plate is easy to form a pearlite or bainite strip-shaped structure, the plasticity, the welding performance and the fatigue performance are all unfavorable, and the Mn percentage control range is 0.50-0.65 percent in the invention comprehensively considered.
P: p has small diffusion speed in gamma-Fe and alpha-Fe, is easy to form segregation, and is unfavorable for the formability, low-temperature impact toughness and welding performance of the steel plate. Therefore, the control range of the P percentage in the invention is less than or equal to 0.020 percent.
S: s can be combined with Mn to form MnS, the MnS is an inclusion with excellent plasticity and is a good hydrogen storage trap, and the method is very beneficial to improving the anti-scaling performance of the steel plate, but the excessively high S content can deteriorate the welding performance of the steel plate and is unfavorable to the adhesion performance of the steel plate after enameling, and the control range of the S percentage in the method is 0.010-0.025 percent by comprehensively considering the content of Mn element in the method.
Al: al is used as a main deoxidizer, and aluminum plays a certain role in refining grains. The disadvantage of aluminum is that it affects the hot workability, weldability and machinability of the steel. The control range of the percentage content of Al in the invention is 0.010-0.060 percent.
Ti: ti has strong affinity with C, N, and can form stable compounds with C and S, such as TiN or Ti (CN), ti 4 C 2 S 2 Or TiS. These phases are far more than Fe 3 C is stable and can not be decomposed at the enameling temperature, thereby preventing CO and CO in the enameling process 2 The generation of the equal gas can improve the anti-scaling property of the steel plate and reduce the defects of pinholes, bubbles and the like of the porcelain surface. The stable compounds formed by Ti and S not only can desulfurize steel, but also promote uniform distribution of sulfur, which avoids various defects caused by sulfur. However, the adhesion of steel sheets with too high Ti content is deteriorated, and the Ti percentage control range in the invention is 0.030% -0.060%.
Cu: copper can improve strength and toughness, can improve the adhesion performance of the steel plate, and the plasticity of the steel plate can be reduced due to the fact that the Cu content is too high. The Cu percentage control range in the invention is 0.001% -0.050%.
Cr: the strength, hardness and wear resistance are significantly improved, but the plasticity and toughness are reduced at the same time. The oxidation resistance and corrosion resistance of the steel are improved. The temperatures of A3 and A1 are raised and the GS line moves to the upper left. Chromium is a medium-strength carbide forming element, and can also improve the anti-scaling performance of the steel plate. The control range of the Cr percentage in the invention is 0.001-0.050%.
V: v is a strong carbide forming element, has extremely strong binding force with carbon, forms stable VC, is typical carbide with high melting point, high hardness and high dispersity, increases the hydrogen storage capacity of the steel plate, improves the anti-scaling performance, and can reduce the strength fluctuation of the steel plate before and after enameling. The V percentage content control range in the invention is 0.001% -0.040%.
Mo: fine grains of steel, improved hardenability and heat strength, and sufficient strength and creep resistance at high temperatures. Red hardness can be improved in tool steels. The alloy steel is inhibited from being brittle due to tempering. The temperatures of A3 and A1 are raised and the GS line moves to the upper left. Molybdenum is a medium-strength carbide forming element, and can also improve the anti-scaling performance of the steel plate. The control range of the percentage content of Mo in the invention is 0.001-0.030%.
Ni: can improve the strength of steel and keep good plasticity and toughness. The ferrite grains are thinned, the hardening performance of the steel is improved, and the heat resistance of the steel can be improved. The Ni percentage content control range in the invention is 0.001% -0.030%.
The Cr+Ni+Mo+V is more than or equal to 0.015 percent, and the achieved effects are that: the four elements can play a role in refining steel grains, improve the high-temperature resistance of the steel, reduce the change of the grains after enameling, reduce the fluctuation of yield strength, have synergistic effect, have better effect than the single element, and can enlarge the fluctuation of the yield strength before and after enameling if the content is low and the effect is not obvious.
Compared with the prior art, the invention improves the scale explosion resistance and the adhesion performance of the steel plate by adding reasonable Ti and Cu on the basis of the carbon manganese steel, refines grains by Cr, ni, mo, V and increases the thermal stability of the steel, so that the change of the grains after the steel is high Wen Tang, reduces the fluctuation of the yield strength before and after the enameling, and simultaneously can further improve the scale explosion resistance of the steel.
Drawings
FIG. 1 is a microstructure of a steel sheet of example 1;
FIG. 2 shows the microstructure after enamelling in example 1;
FIG. 3 is a microstructure of a steel plate of comparative example 1;
FIG. 4 is a microstructure after enamelling of comparative example 1;
FIG. 5 is a macroscopic morphology after enamelling of example 1;
FIG. 6 is the macroscopic morphology after enamelling of comparative example 2.
Detailed Description
Example 1-example 3
The hot-rolled pickled enamel steel with the yield strength of more than or equal to 300MPa after enamelling comprises the following components in percentage by mass: as shown in table 1, the balance not shown in table 1 is Fe and unavoidable impurities.
Comparative example 1-comparative example 4
The steel for hot-rolled and pickled enamel comprises the following components in percentage by mass: as shown in table 1, the balance not shown in table 1 is Fe and unavoidable impurities.
Table 1 chemical compositions of examples and comparative examples, wt%
| Examples | C | Si | Mn | P | S | Al | Ti | Cu | Cr | V | Mo | Ni |
| Example 1 | 0.055 | 0.027 | 0.58 | 0.013 | 0.022 | 0.025 | 0.058 | 0.010 | 0.012 | 0.010 | 0.010 | 0.025 |
| Example 2 | 0.042 | 0.018 | 0.52 | 0.007 | 0.015 | 0.046 | 0.045 | 0.048 | 0.022 | 0.005 | 0.018 | 0.002 |
| Example 3 | 0.067 | 0.009 | 0.65 | 0.015 | 0.010 | 0.053 | 0.038 | 0.028 | 0.003 | 0.020 | 0.024 | 0.011 |
| Comparative example 1 | 0.055 | 0.027 | 0.58 | 0.013 | 0.022 | 0.025 | 0.058 | 0.010 | 0.002 | 0.001 | 0.002 | 0.003 |
| Comparative example 2 | 0.035 | 0.027 | 0.48 | 0.013 | 0.022 | 0.025 | 0.0016 | 0.005 | 0.010 | 0.010 | 0.010 | 0.005 |
| Comparative example 3 | 0.055 | 0.027 | 0.58 | 0.013 | 0.022 | 0.025 | 0.058 | 0.010 | 0.012 | 0.010 | 0.010 | 0.025 |
| Comparative example 4 | 0.055 | 0.027 | 0.58 | 0.013 | 0.022 | 0.025 | 0.058 | 0.010 | 0.012 | 0.010 | 0.010 | 0.025 |
The production method of the hot-rolled and pickled enamel steel comprises the following steps:
1) Steelmaking: and (3) carrying out front skimming and rear skimming, modifying secondary ladle top slag, and adopting a light treatment process for RH.
2) Heating by a heating furnace: when the casting blank is cold-packed (the temperature of the casting blank in a furnace is less than or equal to 400 ℃), the time for heating the casting blank to 1100 ℃ is controlled within 2.5 hours, the time for heating the casting blank to 1100-1200 ℃ is controlled within 0.5-1 hour, and the temperature for discharging the casting blank is controlled within 1180-1200 ℃. When the casting blank is hot-packed (the temperature of the casting blank is more than 400 ℃), the time of the temperature of the casting blank between 1100 ℃ and 1200 ℃ is controlled to be 0.5h to 1h, the total furnace time is controlled to be within 3h, and the furnace outlet temperature of the casting blank is controlled to be 1180 ℃ to 1215 ℃. Aims to reduce the thickness of oxide scale on the surface of a casting blank, improve the uniformity of crystal grains of the casting blank and prevent the excessive growth of the crystal grains (according to a solid solubility product formula of Ti and C, S element, the tapping temperature is too high, so that Ti is caused 4 C 2 S 2 Or the TiS is dissolved back, and fine TiC is separated out in the subsequent rolling or laminar cooling process, so that the yield strength of the product in the hot rolled state is excessiveHigh, which is unfavorable for the product forming process). The casting blank has long furnace time, coarse austenite grains, more iron scales, coarse grains at 1100-1200 ℃, short casting blank, different internal and external temperature differences and uneven internal and external grains.
3) And (3) hot rolling: the final rolling temperature is controlled at 840-870 ℃, the coiling temperature is controlled at 550-580 ℃, full-length sparse cooling is adopted, and the cooling speed is 30+/-5 ℃/S. For the tail temperature of a thin intermediate billet, the final rolling temperature is set to be too high to hit, the tail flick is very easy to influence the production stability after finish rolling, meanwhile, the final rolling temperature is high, and at a certain coiling temperature, the cooling rate after rolling is improved, the grain refinement of a hot rolled product is facilitated, and the hot rolled yield strength is high; the method adopts a proper lower coiling temperature and a post-rolling sparse cooling mode, and aims to reduce precipitation and growth of hot-rolled TiC particles, reduce the post-rolling cooling rate, prevent excessive refinement of hot-rolled grains, reduce the yield strength of the hot-rolled product and reduce the difficulty of processing and forming in the use process of a user. Ti, C and other elements dissolved in steel separate out fine dispersed TiC particles as effective hydrogen traps in the subsequent enamel firing and cooling process, so that the anti-scaling performance is improved.
4) Acid washing: to reasonably control the pickling speed, the following considerations are mainly used: if the pickling speed is too low, overeating may occur; if the pickling speed is too high, underpickling may result, affecting the surface quality. Considering comprehensively that the pickling speed Vs is controlled to be 50-150 m/min, the thickness H of the oxide scale on the surface of the hot rolled steel plate is 50-90 mu m, the target value of the pickling speed Vs=9000/H-40, and the control range of Vs is the target value + -10. The pickling solution is added with inhibitor with the concentration of 0.5 to 3 per mill, and the technology can lead the surface quality of the steel plate to reach the FC grade.
5) Rinsing: the desalted water is adopted for rinsing, the pH value is 6.5-7.5, the concentration of Cl ions is less than or equal to 0.5mg/L, the surface of the steel plate is ensured to be cleaned, and the oxidation of the steel plate after rinsing and before squeezing is inhibited.
6) Oiling: and (3) adopting easy-to-clean rust-preventive oil.
According to the process, after molten steel continuous casting, hot rolling and pickling are carried out to produce hot rolling and pickling enamel steel, and main process parameters and final properties are shown in table 2.
Table 2 production process parameters for each of the examples and comparative examples
The properties of the hot-rolled pickled steel sheet produced in each of the examples and comparative examples are shown in Table 3.
TABLE 3 Properties of hot-rolled pickled Steel sheets produced by the products of examples and comparative examples
The invention discloses a room temperature tensile test method for mechanical property detection according to GB/T228.1 metal materials.
The surface quality grade of the hot-rolled pickled steel plate is that FA is a common surface, FB is a higher-order surface, and FC is a higher-order surface. The steel plate is enamelled after cleaning and post-treatment, the glaze adopts the common wet glaze for the inner container of the water heater, the enameling process is performed for 5-10min for air cooling at 820-860 ℃, and the enamel process and the performance evaluation result are shown in table 4. The adhesion performance of the enamelled steel sheet was rated: the enamel layer was completely adhered to the sample surface after impact and had a shiny appearance (best adhesion strength) grade 1. The enamel layer was almost completely adhered to the sample surface after impact (good adhesion strength) grade 2. And 3, most of enamel layer is attached to the sample after impact, and a small amount of exposed iron is better. 4 stages: a small portion of the enamel layer was attached to the test specimen after impact and a large amount of exposed iron (comparatively poor). 5 stages: the porcelain of the sample after impact is removed, and the separation of the enamel layer and the metal layer is very clear (very poor).
TABLE 4 surface quality and enamel Properties of the examples and comparative examples products
The data in the horizontal direction shown in the above table are data which do not satisfy the requirements of the present invention.
Table 4 shows that the enamel according to the embodiment of the process of the invention has excellent anti-scaling performance and adhesion performance, the yield strength after enameling is more than or equal to 300MPa, and the change value of the yield strength before and after enameling is less than or equal to 50MPa. Fig. 1 shows the microstructure of example 1, which is mainly ferrite+pearlite, the pearlite ratio is 13.2%, the grain size is 11.0, and the fine inclusions are contained in a large amount, and fig. 2 shows the structure of example 1 after enameling, and the crystal grain size is 10. Example 1 the grain size was changed from 11.0 to 10.0 before and after enameling, the grains were still fine after enameling, the yield strength after enameling was high, and the yield strength reduction value after enameling was small and the fluctuation was small.
Fig. 3 shows the microstructure of comparative example 1, mainly ferrite+carbide, with a grain size of 11.0, and the microstructure of comparative example 1 in fig. 4 after enameling, with 8-level grains and coarse grains. Comparative example 1, the yield strength before enameling is higher, the processing difficulty is increased, the grain size before and after enameling is changed from 11.0 to 8.0, the grains after enameling are coarse, and the yield strength after enameling is lower than the use requirement.
Fig. 5 is a macroscopic picture of example 1 after enameling without scale explosion. FIG. 6 is a macroscopic picture of comparative example 2 after enameling, localized scaling.
As can be seen, the chemical components of the comparative example 1 do not meet the requirement that Cr+Ni+Mo+V is more than or equal to 0.015%, the yield strength reduction value after enameling is more than 50MPa, and the yield strength after enameling is less than 300MPa, which does not meet the requirement. The chemical compositions of C, mn and Ti of comparative example 2 do not meet the requirements of the invention, and scale explosion occurs after enameling. Comparative example 3 and comparative example 4 were the same components as in example 1, but in production, the hot rolling process of comparative example 3 did not meet the requirements of the present invention, the yield strength of the product was high, the processing difficulty was high, and the reduction value of the yield strength after enameling greatly affected the adhesion performance. Comparative example 4 the pickling conditions did not meet the requirements of the present invention, resulting in the presence of under-pickling and scale indentation on the surface of comparative example 4 affecting enamel properties and adhesion properties.
As can be seen from the above examples, the hot-rolled pickled steel plate produced by the process of the invention has the surface quality reaching the FC level, mainly comprises ferrite and a small amount of pearlite, has the yield strength of 330-400MPa, the tensile strength of 390-490MPa, the A50 elongation of more than or equal to 32%, is subjected to enameling at the temperature of 820-860 ℃ for 5-10min and is cooled to the room temperature yield strength of more than or equal to 300MPa, the yield strength reduction value before and after enameling is less than or equal to 50MPa, and has excellent anti-fishscale performance and adhesion performance.
The foregoing description is only illustrative of the present invention, and it is to be understood that the specific implementation of the present invention is not limited by the foregoing manner, and it is within the scope of the present invention to apply the technical concept and technical solution of the present invention to other situations without any substantial improvement or any improvement.
Claims (12)
1. The hot-rolled and pickled enamel steel with the yield strength of more than or equal to 300MPa after enamelling is characterized by comprising the following components in percentage by mass:
c:0.04% -0.07%; si is less than or equal to 0.03%; mn:0.50% -0.65%; p is less than or equal to 0.020%; s:0.010% -0.025%; al:0.010% -0.060%; ti:0.030% -0.060%; cu:0.001% -0.050%, cr:0.001% -0.050%, V:0.001% -0.040%, mo:0.001% -0.030%, ni:0.001% -0.030%, and the balance being Fe and unavoidable impurities;
the components of the hot-rolled and pickled enamel steel with the yield strength more than or equal to 300MPa after enamelling meet the following conditions: cr+Ni+Mo+V is more than or equal to 0.015%;
the production method of the hot-rolled and pickled enamel steel with the yield strength more than or equal to 300MPa after enamelling comprises the following process flows: steelmaking, heating, hot rolling, pickling, rinsing and oiling;
the heating is carried out, when the casting blank is cold packed, namely, the casting blank charging temperature is less than or equal to 400 ℃, the time for heating the casting blank to 1100 ℃ is controlled within 2.5 hours, the time for heating the casting blank to 1100-1200 ℃ is controlled within 0.5-1 hour, and the casting blank discharging temperature is controlled within 1180-1200 ℃;
when the casting blank is hot-packed, namely, when the temperature of the casting blank entering a furnace is more than 400 ℃, the time of the temperature of the casting blank between 1100 ℃ and 1200 ℃ is controlled to be 0.5h to 1h, the total time of the casting blank entering the furnace is controlled to be within 3h, and the temperature of the casting blank exiting the furnace is controlled to be 1180 ℃ to 1215 ℃;
the heating is carried out, the final rolling temperature is controlled at 840-870 ℃, the coiling temperature is controlled at 550-580 ℃, full-length sparse cooling is adopted, and the cooling speed is 30+/-5 ℃/S;
the acid washing: the thickness H of the oxide scale on the surface of the hot rolled steel plate is 50-90 mu m, the target value of the pickling speed Vs=9000/H-40, and the control range of the pickling speed Vs is the target value + -10;
the acid washing: adding an inhibitor into the pickling solution, wherein the concentration is 0.5-3 mill;
the rinsing: the rinsing adopts desalted water, the pH value is 6.5-7.5, and the concentration of Cl ions is less than or equal to 0.5mg/L;
the hot-rolled pickled enamel steel with the yield strength of more than or equal to 300MPa after enameling is subjected to enameling at 820-860 ℃ for 5-10min and cooled to room temperature, the yield strength after enameling is more than or equal to 300MPa, and the yield strength reduction value before and after enameling is less than or equal to 50MPa.
2. A method for producing hot-rolled pickled enamel steel with yield strength more than or equal to 300MPa grade after enameling according to claim 1, which is characterized in that the production method comprises the following process flows: steelmaking, heating, hot rolling, pickling, rinsing and oiling.
3. The production method according to claim 2, wherein the heating is performed, when the casting blank is cold-charged, namely, the casting blank charging temperature is less than or equal to 400 ℃, the time for heating the casting blank to 1100 ℃ is controlled within 2.5h, the time for heating the casting blank to 1100-1200 ℃ is controlled within 0.5h-1h, and the casting blank discharging temperature is controlled within 1180-1200 ℃.
4. The method according to claim 2, wherein the heating is performed for a period of time between 1100 and 1200 ℃ for 0.5h to 1h, the total period of time is controlled within 3h, and the casting discharging temperature is controlled between 1180 ℃ and 1215 ℃ when the casting is hot-charged, i.e. the casting charging temperature is more than 400 ℃.
5. The production method according to claim 2, wherein the heating is performed at a finishing temperature of 840-870 ℃, a coiling temperature of 550-580 ℃, and full-length sparse cooling is performed at a cooling rate of 30+ -5 ℃/S.
6. The production method according to claim 2, wherein the acid washing: the thickness H of the oxide scale on the surface of the hot rolled steel plate is 50-90 mu m, the target value of the pickling speed Vs=9000/H-40, and the control range of the pickling speed Vs is the target value + -10.
7. The production method according to claim 2 or 6, characterized in that the acid washing: the pickling solution is added with inhibitor, and the concentration is 0.5-3 per mill.
8. The production method as claimed in any one of claims 2 to 6, wherein the produced hot-rolled pickled enamel steel has a post-enamelling yield strength of not less than 300MPa, a yield strength of 330 to 400MPa, a tensile strength of 390 to 490MPa, A 50 The elongation is more than or equal to 32 percent, and the surface quality of the steel plate reaches the FC grade and above.
9. The production method according to claim 7, wherein the produced steel for hot-rolled pickled enamel has a yield strength of not less than 300MPa, a yield strength of 330-400MPa, a tensile strength of 390-490MPa, A 50 The elongation is more than or equal to 32 percent, and the surface quality of the steel plate reaches the FC grade and above.
10. The production method according to any one of claims 2, 3, 4, 5, 6 and 9, wherein the hot-rolled pickled enamel steel with the post-enameling yield strength of not less than 300MPa is enamelled at 820-860 ℃ for 5-10min and cooled to room temperature, the post-enameling yield strength of not less than 300MPa, and the post-enameling yield strength reduction value of not more than 50MPa.
11. The production method according to claim 7, wherein the post-enameling yield strength is not less than 300MPa, the hot-rolled pickled enamel steel is enamelled at 820-860 ℃ for 5-10min and cooled to room temperature, the post-enamelling yield strength is not less than 300MPa, and the post-enameling yield strength reduction value is not more than 50MPa.
12. The production method according to claim 8, wherein the post-enameling yield strength is not less than 300MPa grade hot-rolled pickled enamel steel, enamelling is carried out at 820-860 ℃ for 5-10min and cooled to room temperature, the post-enameling yield strength is not less than 300MPa, and the post-enameling yield strength reduction value is not more than 50MPa.
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Citations (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS56248A (en) * | 1979-06-14 | 1981-01-06 | Nippon Steel Corp | Hot-rolled high-strength steel sheet for both-side enameling |
| JPH0967647A (en) * | 1995-08-29 | 1997-03-11 | Sumitomo Metal Ind Ltd | Cold rolled steel sheet for enameling and its production |
| JPH10102222A (en) * | 1996-09-30 | 1998-04-21 | Nkk Corp | Cold rolled steel sheet for direct one time porcelain enameling excellent in deep drawability and its production |
| JPH10168522A (en) * | 1996-12-10 | 1998-06-23 | Nkk Corp | Production of cold rolled steel sheet for porcelain enameling, excellent in fishscale resistance |
| JP2002129279A (en) * | 2000-08-16 | 2002-05-09 | Kawasaki Steel Corp | Ultrahigh strength hot rolled steel sheet having excellent strain age hardening characteristics and its production method |
| JP2003096542A (en) * | 2001-09-21 | 2003-04-03 | Sumitomo Metal Ind Ltd | Steel sheet for enamel, and production method therefor |
| CN107574375A (en) * | 2017-08-31 | 2018-01-12 | 武汉钢铁有限公司 | Counterenamel hot rolling acid-cleaning steel plate and its manufacture method with excellent application of slip performance |
| CN110284070A (en) * | 2019-07-30 | 2019-09-27 | 马鞍山钢铁股份有限公司 | A kind of 260MPa rank hot rolling acid-cleaning glassed steel and its production method |
| CN110343964A (en) * | 2019-07-30 | 2019-10-18 | 马鞍山钢铁股份有限公司 | A kind of yield strength is greater than the enamel cold-rolled steel sheet and its production method of 500MPa |
-
2022
- 2022-10-13 CN CN202211254049.0A patent/CN115537664B/en active Active
Patent Citations (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS56248A (en) * | 1979-06-14 | 1981-01-06 | Nippon Steel Corp | Hot-rolled high-strength steel sheet for both-side enameling |
| JPH0967647A (en) * | 1995-08-29 | 1997-03-11 | Sumitomo Metal Ind Ltd | Cold rolled steel sheet for enameling and its production |
| JPH10102222A (en) * | 1996-09-30 | 1998-04-21 | Nkk Corp | Cold rolled steel sheet for direct one time porcelain enameling excellent in deep drawability and its production |
| JPH10168522A (en) * | 1996-12-10 | 1998-06-23 | Nkk Corp | Production of cold rolled steel sheet for porcelain enameling, excellent in fishscale resistance |
| JP2002129279A (en) * | 2000-08-16 | 2002-05-09 | Kawasaki Steel Corp | Ultrahigh strength hot rolled steel sheet having excellent strain age hardening characteristics and its production method |
| JP2003096542A (en) * | 2001-09-21 | 2003-04-03 | Sumitomo Metal Ind Ltd | Steel sheet for enamel, and production method therefor |
| CN107574375A (en) * | 2017-08-31 | 2018-01-12 | 武汉钢铁有限公司 | Counterenamel hot rolling acid-cleaning steel plate and its manufacture method with excellent application of slip performance |
| CN110284070A (en) * | 2019-07-30 | 2019-09-27 | 马鞍山钢铁股份有限公司 | A kind of 260MPa rank hot rolling acid-cleaning glassed steel and its production method |
| CN110343964A (en) * | 2019-07-30 | 2019-10-18 | 马鞍山钢铁股份有限公司 | A kind of yield strength is greater than the enamel cold-rolled steel sheet and its production method of 500MPa |
Non-Patent Citations (1)
| Title |
|---|
| 碳对低碳搪瓷用钢密着性能的影响;张丽琴等;特殊钢;第50-53页 * |
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