CN117327970A - Hot-dip aluminized zinc-plated steel plate with yield strength of 350MPa and manufacturing method thereof - Google Patents
Hot-dip aluminized zinc-plated steel plate with yield strength of 350MPa and manufacturing method thereof Download PDFInfo
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- CN117327970A CN117327970A CN202210722676.6A CN202210722676A CN117327970A CN 117327970 A CN117327970 A CN 117327970A CN 202210722676 A CN202210722676 A CN 202210722676A CN 117327970 A CN117327970 A CN 117327970A
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 144
- 239000010959 steel Substances 0.000 title claims abstract description 144
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 43
- FJMNNXLGOUYVHO-UHFFFAOYSA-N aluminum zinc Chemical compound [Al].[Zn] FJMNNXLGOUYVHO-UHFFFAOYSA-N 0.000 claims abstract description 48
- 238000005097 cold rolling Methods 0.000 claims abstract description 34
- 239000000126 substance Substances 0.000 claims abstract description 12
- 239000012535 impurity Substances 0.000 claims abstract description 10
- 238000005096 rolling process Methods 0.000 claims description 43
- 238000000137 annealing Methods 0.000 claims description 38
- 238000001816 cooling Methods 0.000 claims description 32
- 239000010936 titanium Substances 0.000 claims description 25
- 229910000859 α-Fe Inorganic materials 0.000 claims description 23
- 239000011701 zinc Substances 0.000 claims description 22
- 229910052725 zinc Inorganic materials 0.000 claims description 22
- HCHKCACWOHOZIP-UHFFFAOYSA-N Zinc Chemical compound [Zn] HCHKCACWOHOZIP-UHFFFAOYSA-N 0.000 claims description 21
- 238000010438 heat treatment Methods 0.000 claims description 19
- 238000005098 hot rolling Methods 0.000 claims description 16
- 238000005452 bending Methods 0.000 claims description 12
- 238000009749 continuous casting Methods 0.000 claims description 11
- 238000012360 testing method Methods 0.000 claims description 11
- 229910001563 bainite Inorganic materials 0.000 claims description 10
- 230000009467 reduction Effects 0.000 claims description 10
- 238000002791 soaking Methods 0.000 claims description 9
- 239000002244 precipitate Substances 0.000 claims description 8
- 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 8
- 229910001567 cementite Inorganic materials 0.000 claims description 7
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 claims description 7
- 238000007747 plating Methods 0.000 claims description 5
- 229910001562 pearlite Inorganic materials 0.000 claims description 4
- 239000002253 acid Substances 0.000 claims description 3
- 238000005406 washing Methods 0.000 claims description 3
- 238000005266 casting Methods 0.000 claims description 2
- 238000000034 method Methods 0.000 description 20
- 238000005728 strengthening Methods 0.000 description 18
- 239000000463 material Substances 0.000 description 15
- IJGRMHOSHXDMSA-UHFFFAOYSA-N Atomic nitrogen Chemical compound N#N IJGRMHOSHXDMSA-UHFFFAOYSA-N 0.000 description 14
- 229910052799 carbon Inorganic materials 0.000 description 13
- 238000013461 design Methods 0.000 description 13
- 229910052757 nitrogen Inorganic materials 0.000 description 10
- 230000008569 process Effects 0.000 description 10
- 229910052719 titanium Inorganic materials 0.000 description 10
- 229910045601 alloy Inorganic materials 0.000 description 9
- 239000000956 alloy Substances 0.000 description 9
- 239000011572 manganese Substances 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
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 description 8
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 8
- 229910052796 boron Inorganic materials 0.000 description 7
- 230000000694 effects Effects 0.000 description 7
- 238000011160 research Methods 0.000 description 7
- 239000000758 substrate Substances 0.000 description 7
- 229910052782 aluminium Inorganic materials 0.000 description 6
- 229910052748 manganese Inorganic materials 0.000 description 6
- 229910001566 austenite Inorganic materials 0.000 description 4
- 239000010955 niobium Substances 0.000 description 4
- 238000001556 precipitation Methods 0.000 description 4
- 239000006104 solid solution Substances 0.000 description 4
- 238000009864 tensile test Methods 0.000 description 4
- ZOXJGFHDIHLPTG-UHFFFAOYSA-N Boron Chemical compound [B] ZOXJGFHDIHLPTG-UHFFFAOYSA-N 0.000 description 3
- XAGFODPZIPBFFR-UHFFFAOYSA-N aluminium Chemical compound [Al] XAGFODPZIPBFFR-UHFFFAOYSA-N 0.000 description 3
- 230000008901 benefit Effects 0.000 description 3
- 230000008859 change Effects 0.000 description 3
- 238000002474 experimental method Methods 0.000 description 3
- 239000007769 metal material Substances 0.000 description 3
- 229910052758 niobium Inorganic materials 0.000 description 3
- 239000002245 particle Substances 0.000 description 3
- 238000010998 test method Methods 0.000 description 3
- XUIMIQQOPSSXEZ-UHFFFAOYSA-N Silicon Chemical compound [Si] XUIMIQQOPSSXEZ-UHFFFAOYSA-N 0.000 description 2
- 238000005275 alloying Methods 0.000 description 2
- 230000007797 corrosion Effects 0.000 description 2
- 238000005260 corrosion Methods 0.000 description 2
- 238000005336 cracking Methods 0.000 description 2
- 239000011159 matrix material Substances 0.000 description 2
- 239000000203 mixture Substances 0.000 description 2
- 229910052698 phosphorus Inorganic materials 0.000 description 2
- 238000012545 processing Methods 0.000 description 2
- 238000001953 recrystallisation Methods 0.000 description 2
- 238000007670 refining Methods 0.000 description 2
- 230000003014 reinforcing effect Effects 0.000 description 2
- 229910052710 silicon Inorganic materials 0.000 description 2
- 239000010703 silicon Substances 0.000 description 2
- 238000009628 steelmaking Methods 0.000 description 2
- 229910052717 sulfur Inorganic materials 0.000 description 2
- 230000009466 transformation Effects 0.000 description 2
- 238000012795 verification Methods 0.000 description 2
- 229910000521 B alloy Inorganic materials 0.000 description 1
- 229910001335 Galvanized steel Inorganic materials 0.000 description 1
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 1
- 229910000914 Mn alloy Inorganic materials 0.000 description 1
- OAICVXFJPJFONN-UHFFFAOYSA-N Phosphorus Chemical compound [P] OAICVXFJPJFONN-UHFFFAOYSA-N 0.000 description 1
- 229910000676 Si alloy Inorganic materials 0.000 description 1
- 238000003723 Smelting Methods 0.000 description 1
- NINIDFKCEFEMDL-UHFFFAOYSA-N Sulfur Chemical compound [S] NINIDFKCEFEMDL-UHFFFAOYSA-N 0.000 description 1
- 229910001069 Ti alloy Inorganic materials 0.000 description 1
- 229910001297 Zn alloy Inorganic materials 0.000 description 1
- QFGIVKNKFPCKAW-UHFFFAOYSA-N [Mn].[C] Chemical compound [Mn].[C] QFGIVKNKFPCKAW-UHFFFAOYSA-N 0.000 description 1
- 230000009286 beneficial effect Effects 0.000 description 1
- 238000004364 calculation method Methods 0.000 description 1
- 239000011248 coating agent Substances 0.000 description 1
- 238000000576 coating method Methods 0.000 description 1
- 239000010960 cold rolled steel Substances 0.000 description 1
- 230000007547 defect Effects 0.000 description 1
- 238000011161 development Methods 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 239000012467 final product Substances 0.000 description 1
- 239000008397 galvanized steel Substances 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
- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 1
- 239000011574 phosphorus Substances 0.000 description 1
- 238000005554 pickling Methods 0.000 description 1
- 230000008092 positive effect Effects 0.000 description 1
- 239000002893 slag Substances 0.000 description 1
- 230000000087 stabilizing effect Effects 0.000 description 1
- 238000006467 substitution reaction Methods 0.000 description 1
- 239000011593 sulfur Substances 0.000 description 1
- 230000007704 transition Effects 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
- C21D8/0221—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
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0236—Cold rolling
-
- 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
- C21D8/0273—Final recrystallisation annealing
-
- 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
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
-
- 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
- C22C38/14—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
-
- 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
- C23C2/26—After-treatment
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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
- C21D2211/002—Bainite
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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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- Chemical & Material Sciences (AREA)
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- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
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- 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 a yield strength of 350MPa and a manufacturing method thereof, and mainly solves the technical problems of high cold rolling load, high manufacturing cost and low production efficiency of the existing hot-dip aluminum-zinc-plated steel plate with the yield strength of 350MPa. The technical scheme is that the hot dip aluminum zinc plated steel plate with the yield strength of 350MPa comprises the following chemical components in percentage by weight: c:0.12 to 0.16 percent, si is less than or equal to 0.05 percent, mn:0.35 to 0.45 percent, P is less than or equal to 0.015 percent, S is less than or equal to 0.015 percent, ti:0.025 to 0.035 percent, B:0.0010 to 0.0020 percent, al:0.010 to 0.030 percent, N: 0.0040-0.0080%, and satisfies 0.122-0.155% (C-Ti/4), and the balance of Fe and unavoidable impurities. Steel sheets are used for building 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 yield strength of 350MPa and a manufacturing method thereof, belonging to the technical field of iron-based alloy.
Background
The hot dip aluminum zinc plated steel plate is coated with a 55% Al and 43.5% Zn aluminum zinc alloy coating on the surface of a steel base, has excellent atmospheric corrosion resistance, and has beautiful spangles on the surface of the aluminum zinc plated steel plate, so that 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, and is widely applied to the building industry since the advent of the product.
In recent years, with the improvement of the requirements of building design on the grades of aluminum-zinc plated products, the industry needs products with higher strength grades, so that products with the yield strength of 350MPa are developed successively to meet the high-strength requirements of the industry. The product demand of 350MPa level is continuously increasing, and the competition is more and more vigorous.
The Chinese patent document with the application publication number of CN 104264041A discloses a high-strength low-alloy hot dip aluminum zinc plated steel strip and a production method thereof, wherein the steel substrate comprises the following chemical components in percentage by weight: c:0.02 to 0.10 percent, mn:0.5 to 1.2 percent, P:0.01 to 0.07 percent, nb:0.01 to 0.12 percent, N is less than or equal to 0.0080 percent, S is less than or equal to 0.02 percent, nb is less than or equal to 0.01 percent (Nb-0.22C-1.1N) is less than or equal to 0.1 percent, mn/1.7S is less than or equal to 8 percent, and the balance is Fe and unavoidable impurities, and the obtained low alloy hot dip galvanized steel strip has the yield strength of 410 to 570MPa, the tensile strength of more than or equal to 470MPa and the elongation of more than or equal to 15 percent. The method meets the requirements on the material performance, but adopts micro elements, the rolling difficulty in the production process is high, the alloy amount 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 500-600 MPa, 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, the yield strength of the material is too high, and the rolling difficulty in the production process is high.
The Chinese patent document with the application publication number of CN101348880A discloses a production method of a high-strength galvanized sheet for a structure, which is characterized by comprising the following chemical components in percentage by mass: c,0.16-0.20%; mn,0.9-1.1%; si is less than or equal to 0.05%; p is less than or equal to 0.020%; s is less than or equal to 0.020%; als,0.02-0.06%, and the balance of Fe; hot rolling process parameters: heating temperature is 1250+/-20 ℃; rough rolling outlet temperature, 1070 + -20 ℃; the final rolling temperature is 850+/-20 ℃; coiling temperature, 560+/-20 ℃; cold rolling reduction: according to different specifications, controlling the temperature to be 60-75%; galvanization annealing temperature: 680-720 ℃; soaking time: 30-45s. The high-carbon high-manganese rolling mill only meets the requirement that the yield strength is more than 350MPa, adopts a high-carbon high-manganese design, and has the advantages of high difficulty in the rolling production process and low production efficiency.
The existing hot dip aluminum zinc plated steel plate with the yield strength of 350MPa generally adopts a carbon-manganese reinforced or microalloyed niobium element mode to improve the yield strength so as to solve the technical problems of high alloy design cost, high hardness difficulty in cold rolling production process and low production efficiency.
Disclosure of Invention
The invention aims to provide a hot-dip aluminum-zinc-plated steel plate with the yield strength of 350MPa and a manufacturing method thereof, and mainly solves the technical problems of high cold rolling load, high manufacturing cost and low production efficiency of the existing hot-dip aluminum-zinc-plated steel plate with the yield strength of 350MPa. The hot-dip aluminum zinc plated steel plate meets the plastic processing requirement of the building industry on the roll forming of the hot-dip aluminum zinc plated steel plate.
The invention adopts the technical thought that the invention designs a soft hot rolled steel plate which is obtained by adopting low-cost component design of low-cost Ti and B elements through hot rolling without adding expensive alloying elements Nb and Mn, meets the low-load rolling requirement, and then carries out short-time annealing through a horizontal continuous annealing furnace, and the obtained metallographic structure comprises recrystallized equiaxed ferrite plus 2% -3% of bainite plus cementite plus fine titanium carbide precipitates in percentage by area through a rapid annealing process and rapid cooling, thereby realizing high-strength yield strength and cold rolling low-load rolling of the hot dip aluminum zinc plated steel plate, reducing the manufacturing cost and improving the production efficiency.
The technical idea of the invention is based on the following research of the applicant, and the yield strength of the annealed cold-rolled steel sheet is reduced by 40MPa relative to that of the hot-rolled steel sheet. In order to meet the requirement that the yield strength of a cold-rolled final product is larger than 350MPa, the yield strength of a hot-rolled steel plate is usually required to be larger than 390MPa, and the common technical method is to add reinforcing elements to improve the yield strength of the hot-rolled steel plate, so that the cold-rolling load is high and the production efficiency is low. The applicant has found through experimental study and production practice verification that the requirement that the cold rolling yield strength is more than 350MPa can be achieved by adding Ti and B elements to replace the existing Nb and Mn reinforcing elements, and the yield strength of the hot rolled steel plate after the Ti and B elements are added is 50-60MPa lower than that of the conventional design, so that the problem of high cold rolling load can be solved.
The technical scheme adopted by the invention is that the hot dip aluminum zinc plated steel plate with the yield strength of 350MPa comprises the following chemical components in percentage by weight: c:0.12 to 0.16 percent, si is less than or equal to 0.05 percent, mn:0.35 to 0.45 percent, P is less than or equal to 0.015 percent, S is less than or equal to 0.015 percent, ti:0.025 to 0.035 percent, B:0.0010 to 0.0020 percent, al:0.010 to 0.030 percent, N: 0.0040-0.0080%, and satisfies 0-0.0030% of (N-Al/3.84), 0.122-0.155% of (C-Ti/4), and the balance of Fe and unavoidable impurities.
The metallographic structure of the hot dip aluminum zinc plated steel plate comprises 2-3 percent of bainite, recrystallized equiaxed ferrite, cementite and fine titanium carbide precipitates in percentage by area, wherein the grain size grade of ferrite in the metallographic structure is grade II 10-II 11; yield strength R of 0.40-0.60 mm thick hot-dip aluminum zinc plated steel plate P0.2 350-420 MPa, tensile strength R m 420-500 MPa, elongation after break A 80mm 16% -25%, 180 ° bending test, d=0a is qualified.
The reason why the chemical components of the substrate of the hot-dip aluminum zinc plated steel sheet with the yield strength of 350MPa level are limited in the above range is as follows:
carbon: carbon is the most economical solid solution strengthening element and can form carbide with the economical titanium element in steel to strengthen the matrix. With the increase of the carbon content, the strength of the steel matrix is increased, in order to consider the low-cost design concept, the carbon content is more than 0.12 percent and can meet the requirement that the tensile strength is more than 420MPa, the carbon content is more than 0.16 percent, the yield and the tensile strength of a hot rolled plate can be obviously increased, the cold rolling load is large, the lower limit of the production efficiency is caused, and meanwhile, the material elongation rate is less than 16 percent; according to the design, carbon which needs to be consumed by adding low-cost titanium is fully considered, and through a large number of experiments, when the (C-Ti/4) content is less than 0.122%, the tensile strength can not reach 420MPa, and when the (C-Ti/4) content is more than 0.155%, the requirement that pearlite in a tissue is aggregated and the elongation rate can not reach 16% can be brought; the applicant research finds that when the content of C, ti element in the hot-dip aluminized zinc-coated steel sheet satisfies the following relationship: according to the weight percentage, the C content is less than or equal to 0.122 percent and less than or equal to 0.155 percent (C-Ti/4), the cost and the mechanical property are relatively economic, and the invention limits the C content to 0.12 percent to 0.16 percent in consideration of the characteristics of low cost.
Silicon: silicon is the residual element in steel, no silicon alloy is added in the production and manufacturing process, and the Si content is less than or equal to 0.05 percent.
Manganese: the important solid solution strengthening elements are added with proper Mn to effectively improve the strength of the steel plate, but the price of the manganese alloy is more expensive, and the addition of Mn can also bring about the increase of cold rolling load caused by solid solution strengthening, thereby lowering the production efficiency. Thus, the present invention defines a Mn content of 0.35% to 0.45% by trial and error and verification.
Titanium: titanium is an economic strengthening element, plays a role in precipitation strengthening in steel, and precipitates fine titanium carbide in an annealing process to play a role in refining grains. The combination of the hot rolling coiling temperature and the annealing temperature setting is more beneficial to the strengthening effect of the titanium element. A titanium content of more than 0.035% results in an increase in the strength of the hot rolled sheet, which results in unstable cold rolling and insufficient annealing, and a titanium content of less than 0.025% results in a sheet yield strength of less than 350MPa. The applicant research finds that when the content of C, ti element in the hot-dip aluminized zinc-coated steel sheet satisfies the following relationship: according to the weight percentage, the C-Ti/4 is less than or equal to 0.122 and less than or equal to 0.155 percent, and the economic cost and mechanical property can be obtained; the invention limits the Ti content to 0.025% -0.035%.
Sulfur: s in the invention is an impurity element, and the S 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 P is limited to be less than or equal to 0.015 percent according to actual steelmaking production capacity.
Aluminum: al is added in the steel to deoxidize, and can be combined with N in the steel to produce AlN, when the Al content is more than 0.030%, excessive aluminum can bring about cost increase, meanwhile, the strengthening effect of nitrogen element in the steel is not facilitated, and when the Al content is less than 0.10%, the problem of inclusion caused by insufficient deoxidization of molten steel is easily caused, and bending cracks occur. Therefore, the addition control range of aluminum in the steel ensures deoxidization and simultaneously plays a role in strengthening nitrogen element. The invention sets Al:0.010 to 0.030 percent.
Nitrogen: the nitrogen strengthening mode can effectively reduce the production cost. In combination with 0.010 to 0.030 percent of Al in steel, the steel is ensured to have free nitrogen to achieve the solid solution strengthening purpose, and the applicant researches find that when the content of N, al element in the hot-dip aluminum-zinc-plated steel plate meets the following relation: according to the weight percentage, the N-Al/3.84 is less than or equal to 0.0030 percent, the economic strengthening purpose of nitrogen in steel can be effectively exerted, and the production efficiency is improved. Thus setting N: 0.0040-0.0080%.
Boron: boron is combined with carbon and nitrogen in steel, precipitation of a grain boundary is achieved, the purpose of stabilizing an austenite phase is achieved, one of the most economical elements of a bainite structure is obtained, a cooling process after plating is combined, and meanwhile, the added economy is considered, and B:0.0010 to 0.0020 percent.
A method for manufacturing a hot dip aluminized zinc-coated steel sheet having a yield strength of 350MPa, 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:0.12 to 0.16 percent, si is less than or equal to 0.05 percent, mn:0.35 to 0.45 percent, P is less than or equal to 0.015 percent, S is less than or equal to 0.015 percent, ti:0.025 to 0.035 percent, B:0.0010 to 0.0020 percent, al:0.010 to 0.030 percent, N: 0.0040-0.0080%, and satisfies 0-0.0030% of (N-Al/3.84), 0.122-0.155% of (C-Ti/4), and the balance of Fe and unavoidable impurities;
heating a continuous casting plate blank to 1200-1250 ℃ 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 820-840 ℃, and the finish rolling reduction rate is 92-93%; after finish rolling, the thickness of the hot rolled steel plate is 2.0-2.3 mm, the laminar cooling adopts front-stage cooling, and the coiling temperature is 650-680 ℃ to obtain a hot rolled steel coil;
the hot rolled steel coil is uncoiled again and then subjected to acid washing, cold rolling, annealing by a horizontal continuous annealing furnace, hot dip aluminum zinc plating and coiling to obtain a finished hot dip aluminum zinc plated steel plate with the thickness of 0.40-0.60 mm, wherein the cold rolling reduction rate is 70-80%, the annealing heating temperature of the strip steel in a rolled hard state after cold rolling in the horizontal continuous annealing furnace is 630-650 ℃, the soaking section temperature is 785-795 ℃, the annealing time of the strip steel in the soaking section is 22-25 s, and the temperature of the strip steel entering an aluminum zinc pot is 601-620 ℃; the strip steel is cooled after being discharged from the aluminum zinc pot, the air cooling speed of the strip steel is 40-60 ℃/s, and the air cooling ending temperature of the strip steel is 380-400 ℃.
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 sufficiently dissolve second phase particles such as TiC and the like, so as to sufficiently exert the grain refining effect of Ti element, 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 1200 ℃, the strengthening effect of Ti element cannot be well exerted, the requirement that the yield strength is less than 350MPa can be brought, 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 1200-1250 ℃.
2. Setting of finish finishing temperature
The microalloy elements of carbon, manganese, titanium and boron 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 order to achieve the purpose of austenite rolling and ensure the tissue stability of the material, experimental research shows that when the finishing temperature of finish rolling is less than 820 ℃, the finish rolling process rolls in a ferrite-austenite two-phase region, the ferrite tissue is easy to be uneven, the elongation after fracture is less than 16 percent, and the bending crack occurs; if the finish rolling finishing temperature is higher than 840 ℃, austenite grains are overlarge before phase transformation, and the yield strength of the material is unstable. Therefore, the finish rolling temperature is set to 820-840 ℃.
3. Laminar cooling method and hot rolling coiling temperature setting
In order to obtain fine grains, rapid cooling is required during the phase transition. In order to achieve the aim of soft hot-rolled materials and small cold rolling load, the requirement of mechanical properties of the materials is met, and the medium-temperature coiling temperature is adopted for testing. When the coiling temperature is higher than 680 ℃, the yield strength of the material part is easily lower than 350MPa, the carbide precipitation strengthening effect in the cold rolling annealing process is not easily exerted, and when the coiling temperature is lower than 650 ℃, the yield strength of the hot plate is higher, the cold rolling load is high, and the production efficiency is not high. Considering comprehensively, the laminar cooling adopts front-stage cooling, and the coiling temperature is 650-680 ℃ 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 after cold rolling is carried out on a cold continuous rolling mill or a reciprocating single-stand rolling mill for a plurality of times, the cold rolling reduction is less than 70%, the recrystallization annealing is insufficient, the elongation rate is less than 16%, the cold rolling reduction is more than 80%, the cold rolling load is obviously increased, the limitation of rolling capability is met, and the cold rolling reduction is determined to be 70% -80% by comprehensively considering.
5. Setting of annealing temperature and annealing time
Through material annealing process research, the initial temperature of the annealing recrystallization temperature of the components and the hot rolling process conditions is 700-720 ℃, and the rapid heating capacity of the horizontal continuous annealing furnace is combined, so that partial ferrite austenitizing is promoted by utilizing the advantage of short-time rapid annealing, and conditions are created for obtaining complex phase structure strengthening. In order to obtain the metallographic structure of the hot dip aluminum zinc plated steel plate, the metallographic structure comprises 2 to 3 percent of bainite, recrystallized equiaxed ferrite, cementite and tiny titanium carbide precipitates in percentage by area, the too high or the too low temperature can bring about the change of the grain size of the recrystallized ferrite, the grain size II of the ferrite is not up to the level II 10 to II 11, and thus the yield strength R of the steel plate is not up to P0.2 350-420 MPa and tensile strength R m Is 420-500 MPa, elongation after break A 80mm The requirement of 16-25% is met, so that the heating temperature of the strip steel in the horizontal continuous annealing furnace is 630-650 ℃, the temperature of the soaking section is 785-795 ℃, and the annealing time of the strip steel in the soaking section is 22-25 s.
6. Setting of temperature of strip steel entering aluminum zinc pot
Through researches on different entering temperatures of the strip steel, the entering temperature is higher than 601 ℃, the elongation of the steel plate is more stable, the fluctuation is small, when the entering temperature is higher than 620 ℃, the surface of the steel plate is easy to generate zinc slag and other defects, and therefore, the temperature of the strip steel entering an aluminum zinc pot is set to be 601-620 ℃ in combination with the actual test result.
7. Setting of cooling speed of strip steel after aluminum-zinc pot
The cooling speed and the cooling end temperature of the strip steel after the aluminum zinc pot determine the content of the residual bainite of the steel plate, in order to regulate and control the matching of the performance and the structure of materials, the cooling speed of the strip steel after the aluminum zinc pot is less than 40 ℃/s, the cooling end temperature is more than 400 ℃, the area percentage of the bainite in the strip steel is less than 2-3%, the cooling strengthening effect is not achieved, the actual capacity of an air cooling device is combined, the strip steel after the zinc pot is subjected to air cooling, the air cooling speed of the strip steel is 40 ℃/s-60 ℃/s, and the air cooling end temperature of the strip steel is 380-400 ℃; and after the air cooling is finished, the strip steel is naturally cooled.
The metallographic structure of the hot rolled steel plate produced by the method is ferrite and pearlite, and the ferrite grain size grade in the metallographic structure is 10-11 grade; yield strength R of hot rolled steel sheet of 2.0-2.3 mm thickness P0.2 335-385 MPa, tensile strength R m 427-499 MPa, elongation after break A 80mm 25% -33%.
The metallographic structure of the hot dip aluminum zinc plated steel plate produced by the method comprises 2-3 percent of bainite, recrystallized equiaxed ferrite, cementite and fine titanium carbide precipitates in percentage by area, wherein the grain size grade of the ferrite in the metallographic structure is grade II 10-II 11; yield strength R of 0.40-0.60 mm thick hot-dip aluminum zinc plated steel plate P0.2 350-420 MPa, tensile strength R m 420-500 MPa, elongation after break A 80mm 16% -25%, 180 ° bending test, d=0a is qualified.
According to the 180-degree bending test of the hot-dip aluminum zinc plated steel plate, d=0a, the phenomena of zinc layer falling and base plate cracking are avoided, and the rolling forming plastic processing requirement of the hot-dip aluminum zinc plated building steel is met.
Compared with the prior art, the invention has the following positive effects: 1. the method is a development of an economic low-alloy element added hot dip aluminum zinc plated steel plate, adopts economic Ti and B elements to replace the existing strengthening of Nb and Mn elements, reduces the alloy addition by 0.02 percent and the cost of per ton steel by 60 yuan, and is a design method of a low-cost high-yield product. 2. The invention adopts Ti and B alloy component design, the hot rolling process is easy to implement, the produced hot rolled plate obtains the soft hot rolled steel plate with low yield strength, the technical problem of high cold rolling load is solved, the production efficiency is greatly improved, and the manufacturing cost is greatly reduced. 3. The invention fully utilizes the advantages and characteristics of the horizontal continuous annealing furnace equipment through low-cost alloy component design, fully exerts the characteristics of rapid annealing and rapid cooling after plating of the annealing furnace, fully exerts the effect of strengthening the heat treatment of the process, has high production efficiency, and is a very economical production mode. 4. The invention not only realizes the stability of mechanical properties and bending properties of materials by low-cost alloy component design and achieves the aim of low cost by combining the hot rolling finishing temperature, the cooling mode and the temperature of the zinc pot, but also greatly improves the use reliability of a user terminal.
Drawings
FIG. 1 is a photograph showing the metallographic structure of a hot rolled steel sheet according to example 4 of the 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 1-5.
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, ti, N and Al elements in the substrate of the hot dip aluminum zinc plated steel plate simultaneously satisfy the following relations: 0.122 to 0.155 percent of (C-Ti/4) and 0 to 0.0030 percent of (N-Al/3.84) in percentage by weight; in examples 1 to 6, (C-Ti/4) were 0.1238%, 0.1413%, 0.1330%, 0.1538%, 0.1413%, 0.1220%, respectively; (N-Al/3.84) was 0.0013%, 0.0023%, 0.0018%, 0.0003%, 0.0013% and 0.0008%, 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 1200-1250 ℃ by a heating furnace and then is subjected to hot rolling, wherein the hot rolling is a two-section rolling process, rolling is controlled by a roughing mill and a finish rolling continuous rolling unit, the roughing is 6-pass rolling, and the finishing temperature of the roughing is 1050-1090 ℃; finish rolling is 7-pass continuous rolling, laminar cooling adopts front-stage cooling, and then coiling is carried out to produce a hot rolled steel coil, wherein the thickness of the hot rolled steel plate is 2.0-2.3 mm; the hot rolling process control parameters are shown in Table 2.
TABLE 2 Hot Rolling Process control parameters according to the examples of the invention
The hot rolled steel plate obtained by the method is shown in figure 1, the metallographic structure of the hot rolled steel plate is ferrite and pearlite, and the ferrite grain size grade in the metallographic structure is 10-11 grade; yield strength R of hot rolled steel sheet of 2.0-2.3 mm thickness P0.2 335-385 MPa, tensile strength R m 427-499 MPa, elongation after break A 80mm 25% -33%.
The hot rolled steel plate obtained by the invention is subjected to a tensile test of metal materials according to GB/T228.1-2010 part 1: room temperature test method the tensile test was performed and the mechanical properties of the hot rolled steel sheet are shown in table 3.
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 acid washing, cold rolling, horizontal continuous annealing furnace annealing and hot dip aluminum zinc plating, and a finished hot dip aluminum zinc steel plate with the thickness of 0.40-0.60 mm is obtained by coiling, wherein the cold rolling reduction rate is 70-80%, the annealing heating temperature of the cold rolled strip steel in a hard rolling state in the horizontal continuous annealing furnace after cold rolling is 630-650 ℃, the soaking section temperature is 785-795 ℃, the annealing time of the strip steel in the soaking section is 22-25 s, the temperature of the strip steel entering an aluminum zinc pot is 601-620 ℃, the strip steel is air-cooled after being discharged from the aluminum zinc pot, the air cooling speed of the strip steel is 40-60 ℃/s, and the air cooling end temperature of the strip steel is 380-400 ℃; and after the air cooling is finished, the strip steel is naturally cooled. The control parameters of the cold rolling and annealing processes are shown in Table 4.
TABLE 4 control parameters of the cold rolling and annealing processes according to the embodiment of the invention
The hot dip aluminized zinc plated steel sheet obtained by the method, referring to fig. 2, the metallographic structure of the hot dip aluminized zinc plated steel sheet comprises 2% -3% of bainite+recrystallized equiaxed ferrite+cementite+fine titanium carbide precipitates in percentage by area, and the grain size grade of the ferrite in the metallographic structure is grade II 10-II 11; yield strength R of 0.40-0.60 mm thick hot-dip aluminum zinc plated steel plate P0.2 350-420 MPa, tensile strength R m 420-500 MPa, elongation after break A 80mm 16% -25%, 180 ° bending test, d=0a is qualified.
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, bending test was performed with reference to GB/T232-2010 metal material bending test method. The mechanical properties 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
As shown in table 5, the yield strength of the hot-dip aluminum zinc plated steel sheet of example 4 is 380MPa, the tensile strength is 465MPa, and the elongation is 20.9%, which indicates that the hot-dip aluminum zinc plated steel sheet manufacturing with low cold rolling load, low manufacturing cost and high production efficiency is realized by combining the hot-rolled refined grains and the rapid annealing process technology through the low-cost component design.
According to the 180-degree bending test of the hot dip aluminum zinc plated steel plate, d=0a, and no phenomenon of zinc layer falling and substrate cracking exists.
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 350MPa grade yield strength comprises the following chemical components in percentage by weight: c:0.12 to 0.16 percent, si is less than or equal to 0.05 percent, mn:0.35 to 0.45 percent, P is less than or equal to 0.015 percent, S is less than or equal to 0.015 percent, ti:0.025 to 0.035 percent, B:0.0010 to 0.0020 percent, al:0.010 to 0.030 percent, N: 0.0040-0.0080%, and satisfies 0-0.0030% of (N-Al/3.84), 0.122-0.155% of (C-Ti/4), and the balance of Fe and unavoidable impurities; yield strength R of 0.40-0.60 mm thick hot-dip aluminum zinc plated steel plate P0.2 350-420 MPa, tensile strength R m 420-500 MPa, elongation after break A 80mm 16% -25%, 180 ° bending test, d=0a is qualified.
2. The hot-dip aluminized zinc sheet with the yield strength of 350MPa grade according to claim 1, wherein the metallographic structure of the hot-dip aluminized zinc sheet comprises 2-3% of bainite+recrystallized equiaxed ferrite+cementite+fine titanium carbide precipitates in terms of area percentage, and the grain size grade of ferrite in the metallographic structure is grade ii 10-ii 11.
3. The manufacturing method of the hot dip aluminum zinc plated steel plate with the yield strength of 350MPa 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:0.12 to 0.16 percent, si is less than or equal to 0.05 percent, mn:0.35 to 0.45 percent, P is less than or equal to 0.015 percent, S is less than or equal to 0.015 percent, ti:0.025 to 0.035 percent, B:0.0010 to 0.0020 percent, al:0.010 to 0.030 percent, N: 0.0040-0.0080%, and satisfies 0-0.0030% of (N-Al/3.84), 0.122-0.155% of (C-Ti/4), and the balance of Fe and unavoidable impurities;
heating a continuous casting plate blank to 1200-1250 ℃ 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 820-840 ℃, and the finish rolling reduction rate is 92-93%; after finish rolling, the thickness of the hot rolled steel plate is 2.0-2.3 mm, the laminar cooling adopts front-stage cooling, and the coiling temperature is 650-680 ℃ to obtain a hot rolled steel coil;
the hot rolled steel coil is uncoiled again and then subjected to acid washing, cold rolling, annealing by a horizontal continuous annealing furnace, hot dip aluminum zinc plating and coiling to obtain a finished hot dip aluminum zinc plated steel plate with the thickness of 0.40-0.60 mm, wherein the cold rolling reduction rate is 70-80%, the annealing heating temperature of the strip steel in a rolled hard state after cold rolling in the horizontal continuous annealing furnace is 630-650 ℃, the soaking section temperature is 785-795 ℃, the annealing time of the strip steel in the soaking section is 22-25 s, and the temperature of the strip steel entering an aluminum zinc pot is 601-620 ℃; the strip steel is cooled after being discharged from the aluminum zinc pot, the air cooling speed of the strip steel is 40-60 ℃/s, and the air cooling ending temperature of the strip steel is 380-400 ℃.
4. The method for producing a hot dip aluminized zinc coated steel sheet having a yield strength of 350MPa grade according to claim 3, wherein the hot rolled steel sheet has a metallographic structure of ferrite + pearlite, and the ferrite grain size level in the metallographic structure is 10 to 11 grades; yield strength R of hot rolled steel sheet of 2.0-2.3 mm thickness P0.2 335-385 MPa, tensile strength R m 427-499 MPa, elongation after break A 80mm 25% -33%.
5. A method for producing a hot dip aluminized zinc plated steel sheet having a yield strength of 350MPa grade according to claim 3, wherein the metallurgical structure of the hot dip aluminized zinc plated steel sheet comprises 2 to 3% by area percent of bainite+recrystallized equiaxed ferrite+cementite+fine titanium carbide precipitates, and the ferrite in the metallurgical structure has a grain size grade of ii 10II 11 grades; yield strength R of 0.40-0.60 mm thick hot-dip aluminum zinc plated steel plate P0.2 350-420 MPa, tensile strength R m 420-500 MPa, elongation after break A 80mm 16% -25%, 180 ° bending test, d=0a is qualified.
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