CN115505833B - Hot dip aluminized zinc steel plate with yield strength of 450MPa and manufacturing method thereof - Google Patents
Hot dip aluminized zinc steel plate with yield strength of 450MPa and manufacturing method thereof Download PDFInfo
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- CN115505833B CN115505833B CN202110630824.7A CN202110630824A CN115505833B CN 115505833 B CN115505833 B CN 115505833B CN 202110630824 A CN202110630824 A CN 202110630824A CN 115505833 B CN115505833 B CN 115505833B
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 122
- 239000010959 steel Substances 0.000 title claims abstract description 122
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 30
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 title claims description 22
- 239000011701 zinc Substances 0.000 title claims description 22
- 229910052725 zinc Inorganic materials 0.000 title claims description 22
- FJMNNXLGOUYVHO-UHFFFAOYSA-N aluminum zinc Chemical compound [Al].[Zn] FJMNNXLGOUYVHO-UHFFFAOYSA-N 0.000 claims abstract description 38
- 238000000034 method Methods 0.000 claims abstract description 24
- 239000012535 impurity Substances 0.000 claims abstract description 11
- 239000000126 substance Substances 0.000 claims abstract description 11
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 9
- 238000005096 rolling process Methods 0.000 claims description 47
- 238000000137 annealing Methods 0.000 claims description 38
- 229910000859 α-Fe Inorganic materials 0.000 claims description 31
- 239000010936 titanium Substances 0.000 claims description 27
- 238000005097 cold rolling Methods 0.000 claims description 25
- 238000010438 heat treatment Methods 0.000 claims description 21
- 238000005098 hot rolling Methods 0.000 claims description 18
- 238000009749 continuous casting Methods 0.000 claims description 14
- 230000009467 reduction Effects 0.000 claims description 13
- 238000001816 cooling Methods 0.000 claims description 12
- 238000012360 testing method Methods 0.000 claims description 11
- 238000002791 soaking Methods 0.000 claims description 10
- 238000005452 bending Methods 0.000 claims description 9
- UNASZPQZIFZUSI-UHFFFAOYSA-N methylidyneniobium Chemical compound [Nb]#C UNASZPQZIFZUSI-UHFFFAOYSA-N 0.000 claims description 9
- 239000002244 precipitate Substances 0.000 claims description 9
- MTPVUVINMAGMJL-UHFFFAOYSA-N trimethyl(1,1,2,2,2-pentafluoroethyl)silane Chemical compound C[Si](C)(C)C(F)(F)C(F)(F)F MTPVUVINMAGMJL-UHFFFAOYSA-N 0.000 claims description 9
- 229910001567 cementite Inorganic materials 0.000 claims description 8
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 claims description 8
- 229910001562 pearlite Inorganic materials 0.000 claims description 5
- 238000005554 pickling Methods 0.000 claims description 5
- 238000007747 plating Methods 0.000 claims description 4
- 238000005266 casting Methods 0.000 claims description 3
- 239000010955 niobium Substances 0.000 description 17
- 239000000463 material Substances 0.000 description 13
- 239000011572 manganese Substances 0.000 description 11
- 229910052719 titanium Inorganic materials 0.000 description 11
- 229910052799 carbon Inorganic materials 0.000 description 10
- 229910052758 niobium Inorganic materials 0.000 description 10
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 10
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 9
- 230000008569 process Effects 0.000 description 9
- 239000000047 product Substances 0.000 description 9
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 8
- 238000005728 strengthening Methods 0.000 description 8
- 239000000758 substrate Substances 0.000 description 8
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 7
- 238000013461 design Methods 0.000 description 7
- 229910045601 alloy Inorganic materials 0.000 description 6
- 239000000956 alloy Substances 0.000 description 6
- 238000002474 experimental method Methods 0.000 description 5
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 4
- 230000008859 change Effects 0.000 description 4
- 238000005336 cracking Methods 0.000 description 4
- 239000011159 matrix material Substances 0.000 description 4
- 239000000203 mixture Substances 0.000 description 4
- 238000001953 recrystallisation Methods 0.000 description 4
- 229910052710 silicon Inorganic materials 0.000 description 4
- 239000010703 silicon Substances 0.000 description 4
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 3
- 238000005275 alloying Methods 0.000 description 3
- 229910001566 austenite Inorganic materials 0.000 description 3
- 238000005260 corrosion Methods 0.000 description 3
- 230000007797 corrosion Effects 0.000 description 3
- 229910052748 manganese Inorganic materials 0.000 description 3
- 239000002245 particle Substances 0.000 description 3
- 238000001556 precipitation Methods 0.000 description 3
- 238000011160 research Methods 0.000 description 3
- 229910052717 sulfur Inorganic materials 0.000 description 3
- 229910001335 Galvanized steel Inorganic materials 0.000 description 2
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 2
- 238000003723 Smelting Methods 0.000 description 2
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 2
- 229910001069 Ti alloy Inorganic materials 0.000 description 2
- 229910052782 aluminium Inorganic materials 0.000 description 2
- 230000008901 benefit Effects 0.000 description 2
- 230000000694 effects Effects 0.000 description 2
- 239000008397 galvanized steel Substances 0.000 description 2
- 239000007769 metal material Substances 0.000 description 2
- 239000011574 phosphorus Substances 0.000 description 2
- 238000009628 steelmaking Methods 0.000 description 2
- 239000011593 sulfur Substances 0.000 description 2
- 238000009864 tensile test Methods 0.000 description 2
- 238000010998 test method Methods 0.000 description 2
- 230000009466 transformation Effects 0.000 description 2
- 229910000851 Alloy steel Inorganic materials 0.000 description 1
- 229910000914 Mn alloy Inorganic materials 0.000 description 1
- 229910001257 Nb alloy Inorganic materials 0.000 description 1
- 101100184727 Rattus norvegicus Pmpca gene Proteins 0.000 description 1
- 229910000676 Si alloy Inorganic materials 0.000 description 1
- 229910001297 Zn alloy Inorganic materials 0.000 description 1
- 238000004220 aggregation Methods 0.000 description 1
- 230000002776 aggregation Effects 0.000 description 1
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 238000004364 calculation method Methods 0.000 description 1
- 239000003054 catalyst Substances 0.000 description 1
- 239000011248 coating agent Substances 0.000 description 1
- 238000000576 coating method Methods 0.000 description 1
- 230000006835 compression Effects 0.000 description 1
- 238000007906 compression Methods 0.000 description 1
- 230000007423 decrease Effects 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 230000002349 favourable effect Effects 0.000 description 1
- 239000000835 fiber Substances 0.000 description 1
- 239000012467 final product Substances 0.000 description 1
- 238000005246 galvanizing Methods 0.000 description 1
- 230000006872 improvement Effects 0.000 description 1
- 229910052742 iron Inorganic materials 0.000 description 1
- WPBNNNQJVZRUHP-UHFFFAOYSA-L manganese(2+);methyl n-[[2-(methoxycarbonylcarbamothioylamino)phenyl]carbamothioyl]carbamate;n-[2-(sulfidocarbothioylamino)ethyl]carbamodithioate Chemical compound [Mn+2].[S-]C(=S)NCCNC([S-])=S.COC(=O)NC(=S)NC1=CC=CC=C1NC(=S)NC(=O)OC WPBNNNQJVZRUHP-UHFFFAOYSA-L 0.000 description 1
- 229910052757 nitrogen Inorganic materials 0.000 description 1
- 230000001590 oxidative effect Effects 0.000 description 1
- 230000008092 positive effect Effects 0.000 description 1
- 230000001376 precipitating effect Effects 0.000 description 1
- 238000012545 processing Methods 0.000 description 1
- 238000007670 refining Methods 0.000 description 1
- 239000002893 slag Substances 0.000 description 1
- 239000006104 solid solution Substances 0.000 description 1
- 238000006467 substitution reaction Methods 0.000 description 1
Classifications
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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
-
- 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
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
-
- 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
- C21D8/0247—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
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
-
- 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
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
-
- 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
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
- C23C2/06—Zinc or cadmium or alloys based thereon
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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
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/34—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the shape of the material to be treated
- C23C2/36—Elongated material
- C23C2/40—Plates; Strips
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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
- C21D2211/003—Cementite
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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
- C21D2211/004—Dispersions; Precipitations
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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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- 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
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- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Heat Treatment Of Sheet Steel (AREA)
- Coating With Molten Metal (AREA)
Abstract
The invention discloses a hot-dip aluminum-zinc-plated steel plate with the yield strength of 450MPa and a manufacturing method thereof, and solves the technical problems of low elongation after breaking, high manufacturing cost and low production efficiency of the existing hot-dip aluminum-zinc-plated steel plate with the yield strength of 450 MPa. The hot dip aluminum zinc plated steel plate with the yield strength of 450MPa comprises the following chemical components in percentage by weight: c:0.11 to 0.13 percent, si:0 to 0.05 percent, mn:0.60% -0.80%, P:0 to 0.015 percent, S:0 to 0.015 percent, nb:0.005% -0.009%, ti: 0.040-0.055%, al:0.010 to 0.030 percent, and satisfies 0.210 percent less than or equal to (C+Mn/6) less than or equal to 0.255 percent, 0.095 percent less than or equal to (C-Ti/4) less than or equal to 0.120 percent, and the balance of Fe and unavoidable impurities. The method is used for building steel structural components.
Description
Technical Field
The invention relates to a cold-rolled hot-dip aluminum-zinc-plated steel plate, in particular to a hot-dip aluminum-zinc-plated steel plate with the yield strength of 450MPa and a manufacturing method thereof, and specifically relates to a hot-dip aluminum-zinc-plated steel plate with the yield strength of 450-550 MPa and a manufacturing method thereof, belonging to the technical field of iron-based alloys.
Background
The aluminum-zinc plated plate is mainly used in the building industry, the market demand in China is continuously increased in recent years, the competition is more and more vigorous, the mechanical property requirement on hot dip aluminum-zinc plated products is obviously improved, the control requirement on the production cost of steel products is also continuously increased, and the elongation of the existing steel plate is low.
The aluminum zinc alloy coating of the hot dip aluminum zinc plated steel plate ensures that the steel plate has excellent atmospheric corrosion resistance and high temperature corrosion resistance, has good spangle, smooth surface and good appearance, can reduce the consumption of steel, and is mainly applied to the building industry and used as a roof, a wall, a waterproof board, a garage door and the like. The hot dip aluminum zinc plated steel product integrates product performance and corrosion resistance, and meanwhile, the steel material has better plasticity, can meet the forming performance of the product, but needs aluminum zinc plated high-strength steel plate with lower cost for the building industry.
The existing hot dip aluminum zinc plated steel plate with the yield strength of 450MPa has the technical problems of low elongation after breaking, poor bending performance, high alloy content and high manufacturing cost.
The Chinese patent document with the application publication number of CN105039848A discloses a production method of 500-600MPa grade cold-rolled annealed low-alloy steel, the tensile strength of the product produced by the method is between 500 and 600MPa, the yield ratio is changed within the range of 0.55-0.85, the yield strength of the obtained final product is 305-459 MPa, the tensile strength is 500-600MPa, the Nb content in the component is 0.025-0.040%, the Ti content is 0.015-0.025%, the yield strength does not meet the requirement, the alloy quantity is added more, and the cost is high.
The Chinese patent document with the application publication number of CN102199723A discloses a cold-rolled hot dip aluminum zinc precipitation strengthening steel and a manufacturing method thereof, wherein the chemical components of a substrate are as follows: c:0.09 to 0.12 weight percent, si is less than or equal to 0.05 weight percent, mn:0.8 to 1.8 weight percent, less than or equal to 0.02 weight percent of P, less than or equal to 0.01 weight percent of S, less than or equal to 0.008 weight percent of N, and less than or equal to Al:0.02 to 0.06wt percent, nb+Ti:0.05 to 0.08 weight percent, and the balance of Fe and unavoidable impurities. The microstructure is ferrite plus second phase particles, the diameter of the second phase particles is less than 6um, the yield strength is 500-600MPa, the tensile strength is 570-710 MPa, the total elongation is more than 14% (80 gauge length, transverse stretching), more expensive alloying element Nb is added in the composition, the cost is high, and meanwhile, the material has over-high yield strength and low elongation and cannot meet the high forming requirement.
Chinese patent document with publication number CN102094149a discloses a niobium-containing hot dip galvanized steel sheet and a method for producing the same, providing a high-value low- Δγ -value structure-use niobium-containing hot dip galvanized steel sheet and a method for producing the same; the composition of the catalyst is C:0.03 to 0.1 percent, si: less than or equal to 0.05 percent, mn:0.5 to 0.9 percent, P: less than or equal to 0.025 percent, S: less than or equal to 0.015 percent, N: less than or equal to 0.005 percent, ti: less than or equal to 0.005 percent, nb:0.03 to 0.06 percent of Al:0.01 to 0.08 percent, and the balance of Fe and unavoidable impurities. The yield strength is more than or equal to 460MPa, the tensile strength is more than or equal to 570MPa, the elongation at break is more than or equal to 28%, the product strength meets the requirements, but the expensive alloying element Nb is added more, and the cost is high.
Disclosure of Invention
The invention aims to provide a hot-dip aluminum-zinc-plated steel plate with the yield strength of 450MPa and a manufacturing method thereof, which mainly solve the technical problems of low elongation after fracture, high manufacturing cost and low production efficiency of the existing hot-dip aluminum-zinc-plated steel plate with the yield strength of 450 MPa.
The invention adopts the technical thought that the microstructure of recrystallized equiaxed ferrite + partially recrystallized fibrous ferrite + cementite + fine titanium carbide and niobium carbide precipitates is obtained through a quick annealing process by adding less expensive alloying element Nb, adopting a low-cost component design with low-cost element Ti added, obtaining a fine grain structure by hot rolling, and then carrying out short-time annealing through a horizontal continuous annealing furnace, thereby realizing the improvement of the yield strength and the elongation after breaking of the hot dip aluminum zinc plated steel plate and the reduction of the manufacturing cost.
The technical scheme adopted by the invention is that the hot dip aluminum zinc plated steel plate with the yield strength of 450MPa comprises the following chemical components in percentage by weight: c:0.11 to 0.13 percent, si:0 to 0.05 percent, mn:0.60% -0.80%, P:0 to 0.015 percent, S:0 to 0.015 percent, nb:0.005% -0.009%, ti: 0.040-0.055%, al:0.010 to 0.030 percent, and satisfies 0.210 percent less than or equal to (C+Mn/6) less than or equal to 0.255 percent, 0.095 percent less than or equal to (C-Ti/4) less than or equal to 0.120 percent, and the balance of Fe and unavoidable impurities.
The metallographic structure of the hot dip aluminized zinc-plated steel plate is a precipitate of recrystallized equiaxed ferrite, partially recrystallized fibrous ferrite, cementite and fine titanium carbide and niobium carbide, and is ironThe grain size grade of the element is II 10.5-II 11.5 grade; yield strength R of 0.40-0.60 mm thick hot-dip aluminum zinc plated steel plate P0.2 450-550 MPa, tensile strength R m 500-600MPa, elongation after break A 80mm 15% -22%, 180 DEG bending test, d=0a is qualified, and no phenomenon of zinc layer falling and substrate cracking is caused.
The reason why the chemical components of the substrate of the hot dip aluminum zinc plated steel sheet with the yield strength of 450MPa level are limited in the above range is as follows:
carbon: carbon is a cheaper and economical solid solution strengthening element and is also used for strengthening the steel matrix niobium and titanium alloy elements to form carbide. In the general design, as the strength of a steel matrix increases with the increase of the carbon content, the plasticity of the material also decreases rapidly, in the design, the carbon required to be consumed by adding a small amount of niobium and low-cost titanium is fully considered, through a large amount of experiments, when the (C-Ti/4) content is smaller than 0.095%, the tensile strength can not reach 500MPa, when the (C-Ti/4) content is larger than 0.120%, the pearlite aggregation in the tissue can be brought to the elongation rate not reach 15%, and the economic cost and mechanical property can be obtained by summarizing that the (C-Ti/4) content is smaller than or equal to 0.095% and smaller than 0.120%, and the invention limits the C content to 0.11% -0.13% in consideration of the characteristics of low cost and sum.
Silicon: the contribution degree of silicon to the strength is larger, but for the heating process of a horizontal annealing furnace is an oxidizing atmosphere, the silicon element in the steel plate is easy to oxidize, the binding force of the hot dip aluminum zinc plating layer is unfavorable, and according to the test result, no silicon alloy is added in the production and manufacturing process, and the Si content is limited to be 0-0.05%.
Manganese: in order to ensure the comprehensive mechanical strength of steel, the invention considers the relevance of carbon and manganese addition, and through a large number of experiments, when (C+Mn/6) is less than 0.210%, the tensile strength of the material is not easy to reach 500MPa, when (C+Mn/6) is more than 0.255%, excessive Mn alloy is added to bring about the problem of overhigh cost, and through repeated experiments, the invention determines that 0.210 percent less than or equal to (C+Mn/6) less than or equal to 0.255 percent can obtain better mechanical property, and realizes the low cost requirement, and the limit Mn content is 0.60 to 0.80 percent.
Titanium: titanium is an important element in the base body of the hot dip aluminum zinc plated steel plate and is also an economic strengthening element. Titanium is a strong carbide forming element, and adding trace titanium into steel is favorable for fixing N in the steel, can play a role in precipitation strengthening in the steel, and particularly can play a role in refining grains by precipitating fine titanium carbide in the annealing process. Meanwhile, titanium can be added to be combined with S, so that the generation of slab cracks is reduced. Tests prove that the cost and mechanical property which are more economic can be obtained by the method that the C-Ti/4 is less than or equal to 0.095 and less than or equal to 0.120 percent; the invention limits the Ti content to 0.040% -0.055%.
Niobium: niobium is an important element in the base body of the hot dip aluminized zinc steel sheet, but is added as little as possible due to its high cost. The Nb element is added into the steel to improve the recrystallization temperature during hot rolling and rolling, thereby playing a role of grain refinement, and after the Nb element is added, the recrystallization annealing temperature of the steel plate after cold rolling is improved, a large amount of fine niobium carbide precipitates are dispersed in a matrix to strengthen the matrix, and in order to achieve the aim of adding less niobium, the aluminum-zinc plated steel plate with low alloy content is designed, and meanwhile, the yield strength of the product can be ensured to meet the requirement of 450 MPa.
Sulfur: s in the invention is an impurity element, and the S content is limited to be less than or equal to 0.015 percent according to actual steelmaking production capacity.
Phosphorus: p in the invention is an impurity element, and the content of P is limited to be less than or equal to 0.015 percent according to actual steelmaking production capacity.
Aluminum: the main purpose of adding Al into steel is deoxidization, and the invention sets Al:0.010 to 0.030 percent.
A method for manufacturing a hot dip aluminized zinc coated steel sheet having a yield strength of 450MPa, the method comprising:
continuously casting molten steel to obtain a continuous casting plate blank, wherein the molten steel comprises the following chemical components in percentage by weight: c:0.11 to 0.13 percent, si:0 to 0.05 percent, mn:0.60% -0.80%, P:0 to 0.015 percent, S:0 to 0.015 percent, nb:0.005% -0.009%, ti: 0.040-0.055%, al:0.010 to 0.030 percent, and satisfies 0.210 percent (C+Mn/6) to 0.255 percent, 0.095 percent to 0.120 percent (C-Ti/4), and the balance of Fe and unavoidable impurities;
heating a continuous casting plate blank to 1250-1300 ℃ by a heating furnace, and then carrying out hot rolling, wherein the hot rolling is a two-stage rolling process, rough rolling is 6-pass rolling, and the rough rolling finishing temperature is 1050-1090 ℃; the finish rolling is 7-pass continuous rolling, the finish rolling finishing temperature is 800-820 ℃, and the finish rolling reduction rate is 93-94%; the thickness of the steel plate after finish rolling is 1.8-2.0 mm; the laminar cooling adopts front-stage cooling, and the coiling temperature is 450-510 ℃ to coil to obtain a hot rolled steel coil;
the hot rolled steel coil is uncoiled again and then subjected to pickling, cold rolling, annealing by a horizontal continuous annealing furnace, hot dip aluminum zinc plating and leveling, and finished hot dip aluminum zinc plated steel plate with the thickness of 0.40-0.60 mm is obtained by coiling, wherein the cold rolling reduction rate is 66-80%, the heating temperature of the strip steel in a rolled hard state after cold rolling in the horizontal continuous annealing furnace is 600-620 ℃, the soaking section temperature is 730-749 ℃, the annealing time of the strip steel in the soaking section is 21 s-25 s, the temperature of the strip steel entering an aluminum zinc pot is 590-600 ℃, and the leveling elongation rate is 0.7-1.0%.
The reason for the production process adopted by the invention is as follows:
1. setting of heating temperature of continuous casting slab
In order to fully dissolve second-phase particles such as TiC and NbC and the like, so as to fully play the role of grain refinement of Ti and Nb elements, a high heating temperature is required in the heating process of the continuous casting slab. Experiments show that when the heating temperature is lower than 1250 ℃, the strengthening effect of Ti element cannot be well exerted, the yield strength can not reach the requirement of 450MPa, the heating temperature is too high, the energy cost is higher, and the economy is poor. Through repeated experiments, the heating temperature is set to 1250-1300 ℃.
2. Setting of finish finishing temperature
The microalloy elements of carbon, manganese, titanium and niobium are added into the steel to cause a material phase change point A 3 Descending, through material test and calculation, the phase change point A of the material 3 In the range of 770-790 ℃, in order to achieve the purpose of austenite rolling, the method is carried out by trialProved by experimental study, when the finishing temperature of finish rolling is less than 800 ℃, the finish rolling process is carried out in a ferrite-austenite two-phase region, the ferrite structure is easy to be uneven, and the elongation after breaking can not reach the requirement of 15%; if the finish rolling finishing temperature is higher than 820 ℃, austenite grains are overlarge before phase transformation, stable refined grains cannot be achieved, and the yield strength is unstable. Therefore, the finish rolling temperature is set to 800-820 ℃.
3. Laminar cooling method and hot rolling coiling temperature setting
In order to obtain fine grains, quick cooling is needed in the phase change process, meanwhile, the coiling temperature is reduced, ferrite grains can be controlled to grow, the amount of brittle phase pearlite is reduced, the elongation of the material is improved, when the coiling temperature is higher than 510 ℃, the yield strength of the material is easily smaller than 450MPa, the carbide precipitation strengthening effect in the cold rolling annealing process is not easily exerted, when the coiling temperature is lower than 450 ℃, the control capability of the existing rolling temperature is limited, the fluctuation of the yield strength is easily caused, and the comprehensive consideration is that the laminar cooling adopts front-stage cooling, and the coiling temperature is 450-510 ℃ to coil to obtain the hot rolled steel coil.
4. Setting of cold rolling reduction
The invention provides a hot dip aluminized zinc sheet cold rolling process for the rapid heating treatment. The hot rolled steel coil with the components and subjected to hot rolling is uncoiled again and subjected to pickling to remove surface scale, and then is subjected to cold rolling on a cold continuous rolling mill or a reciprocating single-stand rolling mill for a plurality of times, wherein the cold rolling reduction is less than 66%, the recrystallization annealing is insufficient, the elongation rate does not meet 15% requirements, the cold rolling reduction is more than 80%, the cold rolling load is overlarge, the limitation of rolling capacity is imposed, and the cold rolling reduction is determined to be 66% -80% by comprehensive consideration.
5. Setting of annealing temperature and annealing time
Through material annealing process research, the annealing recrystallization temperature under the conditions of the composition and the hot rolling process is 680-700 ℃, and the advantage of rapid annealing is utilized by combining the rapid heating capability of a horizontal continuous annealing furnace, so as to obtain the fiber with recrystallized equiaxed ferrite and partially recrystallized fiberThe steel sheet with ferrite, cementite, fine titanium carbide and niobium carbide precipitate structure has recrystallized ferrite grain size change caused by too high or too low temperature, and the grain size of ferrite is not up to the grade II 10.5-II 11.5, thus the yield strength R of the steel sheet is not up to the grade II 10.5 P0.2 450-550 MPa and tensile strength R m 500-600MPa, elongation after break A 80mm The requirement of 15-22% is met, so that the heating temperature of the strip steel in the horizontal continuous annealing furnace is 600-620 ℃, the soaking section temperature is 730-749 ℃, and the annealing time of the strip steel in the soaking section is 21-25 s.
6. Setting of temperature and leveling elongation of strip steel entering aluminum zinc pot
According to the research on different entering temperatures of the strip steel, the higher the entering temperature is, the higher the elongation of the steel plate is, but the higher the entering temperature is, the surface quality of the steel plate is poor, zinc slag is easy to generate, so that the entering temperature of the strip steel into an aluminum zinc pot is set to 590-600 ℃ according to the actual test result; further, in order to control the performance stability of the material, the flattening elongation is set to be 0.7% -1.0%.
The metallographic structure of the hot rolled steel plate produced by the method is ferrite and pearlite, the ferrite grain size grade is 11.5-12.0 grade, and the yield strength R of the hot rolled steel plate with the thickness of 1.8-2.0 mm P0.2 465-558 MPa, tensile strength R m 547-610 MPa, elongation after break A 80mm 20% -28%.
The metallographic structure of the hot dip aluminum zinc plated steel plate produced by the method is a precipitate of recrystallized equiaxed ferrite, partially recrystallized fibrous ferrite, cementite, fine titanium carbide and niobium carbide, and the ferrite grain size grade is II 10.5-II 11.5; yield strength R of 0.40-0.60 mm thick hot-dip aluminum zinc plated steel plate P0.2 450-550 MPa, tensile strength R m 500-600MPa, elongation after break A 80mm The steel is 15-22 percent, 180-degree bending test is carried out, d=0a is qualified, the phenomena of zinc layer falling and substrate cracking are avoided, and the rolling forming plastic processing requirement of the steel for hot-dip aluminum-zinc-plated building is met.
Compared with the prior art, the invention has the following positive effects: 1. the method is the development of an economic low-alloy element added hot dip aluminum zinc plated steel plate, researches a low-cost steel with the yield strength of 450-550 MPpa, and obtains the structures of recrystallized equiaxed ferrite, partially recrystallized fibrous ferrite, cementite and fine precipitates of titanium carbide and niobium carbide, thereby achieving the purposes of high yield strength and elongation of the material. 2. According to the invention, through the design of economic and cheap alloy components, the advantages and the characteristics of equipment are fully utilized, the characteristics of hot rolling refined grains and quick annealing of an annealing furnace are brought into play, the production efficiency is high, and the method is a production mode which is very energy-saving. 3. According to the invention, the component design is adopted, and a certain titanium alloy element is added in the smelting and continuous casting processes, so that S element easy to crack of the product is solidified, the production manufacturability is greatly improved, and the problem of slab cracking is avoided. 4. The hot rolling process adopted in the method fully combines the characteristics of materials, fully plays the strengthening role of adding carbon, titanium and niobium elements, and realizes more reliable hot rolling process. 5. The invention adopts a design with lower cold rolling deformation rate, can be realized on a rolling mill with limited cold rolling capacity, and simultaneously has low compression ratio, thereby being beneficial to reducing the consumption of energy sources.
Drawings
FIG. 1 is a photograph showing the metallographic structure of a hot rolled steel sheet according to example 4 of the present invention;
fig. 2 is a photograph showing a metallographic structure of a hot-dip aluminized zinc-coated steel sheet according to example 4 of the present invention.
Detailed Description
The invention is further illustrated below in connection with examples 1-6, as shown in tables 1-4.
Table 1 shows chemical components (in weight percent) of the substrate of the hot-dip aluminized zinc sheet according to the embodiment of the present invention, and the balance of Fe and unavoidable impurities.
Table 1 chemical components of the substrate of the hot dip aluminized zinc coated steel sheet according to the embodiment of the present invention, unit: weight percent.
The contents of C, mn and Ti elements of the substrate of the hot dip aluminum zinc plated steel plate simultaneously satisfy the following relations: 0.210 to 0.255 percent of (C+Mn/6) and 0.095 to 0.120 percent of (C-Ti/4) in percentage by weight; in examples 1 to 6, (C+Mn/6) was 0.246%, 0.237%, 0.213%, 0.255%, 0.243%, 0.240%, respectively; (C-Ti/4) was 0.107%, 0.118%, 0.102%, 0.113%, 0.100% and 0.107%, respectively.
Molten steel meeting the chemical composition is obtained through converter smelting, the molten steel is continuously cast to obtain a continuous casting slab, the thickness of the continuous casting slab is 210 mm-230 mm, the width of the continuous casting slab is 800 mm-1300 mm, and the length of the continuous casting slab is 5000 mm-10000 mm.
The continuous casting slab is heated to 1250-1300 ℃ by a heating furnace and then subjected to hot rolling, wherein the hot rolling is a two-stage rolling process, rough rolling is 6-pass rolling, the rough rolling finishing temperature is 1050-1090 ℃, finish rolling is 7-pass continuous rolling, the finish rolling finishing temperature is 800-820 ℃, the finish rolling reduction rate is 93-94%, and the thickness of the finished steel plate is 1.8-2.0 mm; the laminar cooling adopts front-stage cooling, and the coiling temperature is 450-510 ℃ to coil to obtain a hot rolled steel coil; the hot rolling process control parameters are shown in Table 2.
Referring to FIG. 1, the hot rolled steel sheet produced by the method of the present invention has a metallographic structure of ferrite + pearlite, a ferrite grain size grade of 11.5 to 12.0, and a yield strength R of the hot rolled steel sheet P0.2 465-558 MPa, tensile strength R m 547-610 MPa, elongation after break A 80mm 20% -28%; the mechanical properties of the hot rolled steel sheet are shown in Table 3.
TABLE 2 Hot Rolling Process control parameters according to the examples of the invention
TABLE 3 mechanical Properties of the hot rolled Steel sheet according to the example of the invention
The hot rolled steel coil is uncoiled again and then subjected to pickling, cold rolling, annealing by a horizontal continuous annealing furnace, hot galvanizing and leveling, and finished hot dip aluminum zinc plated steel plate with the thickness of 0.40-0.60 mm is obtained by coiling, wherein the cold rolling reduction rate is 66-80%, the annealing heating temperature of the strip steel in a rolled hard state after cold rolling in the horizontal continuous annealing furnace is 600-620 ℃, the soaking section temperature is 730-749 ℃, the annealing time of the strip steel in the soaking section is 21 s-25 s, the temperature of the strip steel entering an aluminum zinc pot is 590-600 ℃, and the leveling elongation rate is 0.7-1.0%. The control parameters of the cold rolling, annealing and leveling processes are shown in Table 4.
TABLE 4 control parameters for the cold rolling, annealing, and temper rolling processes in accordance with embodiments of the present invention
The hot dip aluminized zinc plated steel sheet obtained by the above method has a metallographic structure of recrystallized equiaxed ferrite + partially recrystallized fibrous ferrite + cementite + fine precipitates of titanium carbide and niobium carbide, ferrite grain size grade of II 10.5-II 11.5, and yield strength R of 0.40-0.60 mm thick hot dip aluminized zinc plated steel sheet, see FIG. 2 P0.2 450-550 MPa, tensile strength R m 500-600MPa, elongation after break A 80mm 15% -22%, 180 DEG bending test, d=0a is qualified, and no phenomenon of zinc layer falling and substrate cracking is caused.
The hot dip aluminized zinc steel plate obtained by the invention is subjected to a tensile test according to the section 1 of GB/T228.1-2010 metal materials: room temperature test method tensile test was performed, bending test was performed with reference to GB/T232-2010 metal material bending test method, and the mechanical properties and 180 ° bending test results of the steel sheet are shown in table 5.
Table 5 mechanical properties of the hot dip aluminized zinc coated steel sheet according to the embodiment of the present invention
Examples 1 to 6 of the invention show that the carbon content in the hot dip aluminum zinc plated steel plate is controlled to be 0.11 to 0.13 percent, the manganese content is controlled to be 0.60 to 0.80 percent, the titanium content is controlled to be 0.040 to 0.055 percent, the niobium content is controlled to be 0.005 to 0.009 percent, the silicon content is controlled to be 0 to 0.05 percent, the sulfur content is controlled to be 0 to 0.015 percent, the phosphorus content is controlled to be 0 to 0.015 percent, and the yield strength range can be controlled to be R P0.2 450-550 MPa, tensile strength Rm 500-600MPa, elongation after break A 80mm 15 to 22 percent
Example 4 shows that the low-cost high-elongation hot-dip aluminum zinc plated plate is manufactured by combining hot-rolled refined grains and a rapid annealing process technology through low-cost component design with the yield strength of 482MPa and the tensile strength of 554MPa and the elongation of 22%.
In addition to the embodiments described above, other embodiments of the invention are possible. All technical schemes formed by equivalent substitution or equivalent transformation fall within the protection scope of the invention.
Claims (5)
1. The hot dip aluminum zinc plated steel plate with the yield strength of 450MPa comprises the following chemical components in percentage by weight: c:0.11 to 0.13 percent, si:0 to 0.05 percent, mn:0.60% -0.80%, P:0 to 0.015 percent, S:0 to 0.015 percent, nb:0.005% -0.009%, ti: 0.040-0.055%, al:0.010 to 0.030 percent, and satisfies 0.210 percent (C+Mn/6) to 0.255 percent, 0.095 percent to 0.120 percent (C-Ti/4), and the balance of Fe and unavoidable impurities; the metallographic structure of the hot dip aluminum zinc plated steel plate is a precipitate of recrystallized equiaxed ferrite, partially recrystallized fibrous ferrite, cementite and fine titanium carbide and niobium carbide, and the ferrite grain size grade is II 10.5-II 11.5; yield strength R of 0.40-0.60 mm thick hot-dip aluminum zinc plated steel plate P0.2 450-550 MPa, tensile strength R m 500-600MPa, elongation after break A 80mm 15% -22%; the method for manufacturing the hot dip aluminized zinc steel plate comprises the following steps:
continuously casting molten steel to obtain a continuous casting plate blank, wherein the molten steel comprises the following chemical components in percentage by weight: c:0.11 to 0.13 percent, si:0 to 0.05 percent, mn:0.60% -0.80%, P:0 to 0.015 percent, S:0 to 0.015 percent, nb:0.005% -0.009%, ti: 0.040-0.055%, al:0.010 to 0.030 percent, and satisfies 0.210 percent (C+Mn/6) to 0.255 percent, 0.095 percent to 0.120 percent (C-Ti/4), and the balance of Fe and unavoidable impurities;
heating a continuous casting plate blank to 1250-1300 ℃ by a heating furnace, and then carrying out hot rolling, wherein the hot rolling is a two-stage rolling process, rough rolling is 6-pass rolling, and the rough rolling finishing temperature is 1050-1090 ℃; the finish rolling is 7-pass continuous rolling, the finish rolling finishing temperature is 800-820 ℃, and the finish rolling reduction rate is 93-94%; the laminar cooling adopts front-stage cooling, and the coiling temperature is 450-510 ℃ to coil to obtain a hot rolled steel coil;
the hot rolled steel coil is uncoiled again and then subjected to pickling, cold rolling, annealing by a horizontal continuous annealing furnace, hot dip aluminum zinc plating and leveling, and finished hot dip aluminum zinc plated steel plate with the thickness of 0.40-0.60 mm is obtained by coiling, wherein the cold rolling reduction rate is 66-80%, the heating temperature of the strip steel in a rolled hard state after cold rolling in the horizontal continuous annealing furnace is 600-620 ℃, the soaking section temperature is 730-749 ℃, the annealing time of the strip steel in the soaking section is 21 s-25 s, the temperature of the strip steel entering an aluminum zinc pot is 590-600 ℃, and the leveling elongation rate is 0.7-1.0%.
2. The hot-dip aluminum-zinc-plated steel sheet with a yield strength of 450MPa grade according to claim 1, wherein d=0a is acceptable in 180 ° bending test of 0.40-0.60 mm thick hot-dip aluminum-zinc-plated steel sheet.
3. A method for manufacturing a hot dip aluminized zinc steel plate with a yield strength of 450MPa, which is characterized by comprising the following steps:
continuously casting molten steel to obtain a continuous casting plate blank, wherein the molten steel comprises the following chemical components in percentage by weight: c:0.11 to 0.13 percent, si:0 to 0.05 percent, mn:0.60% -0.80%, P:0 to 0.015 percent, S:0 to 0.015 percent, nb:0.005% -0.009%, ti: 0.040-0.055%, al:0.010 to 0.030 percent, and satisfies 0.210 percent (C+Mn/6) to 0.255 percent, 0.095 percent to 0.120 percent (C-Ti/4), and the balance of Fe and unavoidable impurities;
heating a continuous casting plate blank to 1250-1300 ℃ by a heating furnace, and then carrying out hot rolling, wherein the hot rolling is a two-stage rolling process, rough rolling is 6-pass rolling, and the rough rolling finishing temperature is 1050-1090 ℃; the finish rolling is 7-pass continuous rolling, the finish rolling finishing temperature is 800-820 ℃, and the finish rolling reduction rate is 93-94%; the laminar cooling adopts front-stage cooling, and the coiling temperature is 450-510 ℃ to coil to obtain a hot rolled steel coil;
the hot rolled steel coil is uncoiled again and then subjected to pickling, cold rolling, annealing by a horizontal continuous annealing furnace, hot dip aluminum zinc plating and leveling, and finished hot dip aluminum zinc plated steel plate with the thickness of 0.40-0.60 mm is obtained by coiling, wherein the cold rolling reduction rate is 66-80%, the heating temperature of the strip steel in a rolled hard state after cold rolling in the horizontal continuous annealing furnace is 600-620 ℃, the soaking section temperature is 730-749 ℃, the annealing time of the strip steel in the soaking section is 21 s-25 s, the temperature of the strip steel entering an aluminum zinc pot is 590-600 ℃, and the leveling elongation rate is 0.7-1.0%.
4. The method for producing a hot-dip aluminized zinc coated steel sheet having a yield strength of 450MPa grade according to claim 3, wherein the thickness of the hot-rolled steel sheet is controlled to be 1.8 to 2.0mm after finish rolling; the metallographic structure of the hot rolled steel plate is ferrite and pearlite, and the ferrite grain size grade is 11.5-12.0 grade; yield strength R of hot rolled steel sheet P0.2 465-558 MPa, tensile strength R m 547-610 MPa, elongation after break A 80mm 20% -28%.
5. A method for producing a hot dip aluminized zinc plated steel sheet having a yield strength of 450MPa grade according to claim 3, wherein the hot dip aluminized zinc plated steel sheet has a metallographic structure of recrystallized equiaxed ferrite + partially recrystallized fibrous ferrite + cementite + fine precipitates of titanium carbide and niobium carbide, and has a ferrite grain size grade of from ii 10.5 to ii 11.5; yield strength R of hot dip aluminized zinc steel sheet P0.2 450-550 MPa, tensile strength R m 500-600MPa, elongation after break A 80mm 15% -22%, 180 DEG bending test, d=0a is qualified.
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