CN116288024A - High-strength hot-base galvanized steel sheet with good forming performance and manufacturing method thereof - Google Patents

High-strength hot-base galvanized steel sheet with good forming performance and manufacturing method thereof Download PDF

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CN116288024A
CN116288024A CN202310196444.6A CN202310196444A CN116288024A CN 116288024 A CN116288024 A CN 116288024A CN 202310196444 A CN202310196444 A CN 202310196444A CN 116288024 A CN116288024 A CN 116288024A
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equal
steel sheet
hot
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percent
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CN116288024B (en
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陈泓业
李伟刚
王滕
谢义康
李志庆
李超
孙霖
何峰
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Maanshan Iron and Steel Co Ltd
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Maanshan Iron and Steel Co Ltd
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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
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B1/00—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations
    • B21B1/22—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length
    • B21B1/24—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length in a continuous or semi-continuous process
    • B21B1/26—Metal-rolling methods or mills for making semi-finished products of solid or profiled cross-section; Sequence of operations in milling trains; Layout of rolling-mill plant, e.g. grouping of stands; Succession of passes or of sectional pass alternations for rolling plates, strips, bands or sheets of indefinite length in a continuous or semi-continuous process by hot-rolling, e.g. Steckel hot mill
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B3/00—Rolling materials of special alloys so far as the composition of the alloy requires or permits special rolling methods or sequences ; Rolling of aluminium, copper, zinc or other non-ferrous metals
    • B21B3/02—Rolling special iron alloys, e.g. stainless steel
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B37/00—Control devices or methods specially adapted for metal-rolling mills or the work produced thereby
    • B21B37/74—Temperature control, e.g. by cooling or heating the rolls or the product
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
    • B21B—ROLLING OF METAL
    • B21B45/00—Devices for surface or other treatment of work, specially combined with or arranged in, or specially adapted for use in connection with, metal-rolling mills
    • B21B45/04—Devices for surface or other treatment of work, specially combined with or arranged in, or specially adapted for use in connection with, metal-rolling mills for de-scaling, e.g. by brushing
    • B21B45/08—Devices for surface or other treatment of work, specially combined with or arranged in, or specially adapted for use in connection with, metal-rolling mills for de-scaling, e.g. by brushing hydraulically
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    • C21D1/26—Methods of annealing
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    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
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    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
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    • 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
    • C21D8/0257—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment with diffusion of elements, e.g. decarburising, nitriding
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0278—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips involving a particular surface treatment
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    • C22C33/00—Making ferrous alloys
    • C22C33/04—Making ferrous alloys by melting
    • C—CHEMISTRY; METALLURGY
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    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
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    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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    • 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
    • C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
    • C23C2/022—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by heating
    • C23C2/0224—Two or more thermal pretreatments
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    • 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
    • C23C2/02—Pretreatment of the material to be coated, e.g. for coating on selected surface areas
    • C23C2/024—Pretreatment of the material to be coated, e.g. for coating on selected surface areas by cleaning or etching
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    • 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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    • 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
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    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/14—Removing excess of molten coatings; Controlling or regulating the coating thickness
    • C23C2/16—Removing excess of molten coatings; Controlling or regulating the coating thickness using fluids under pressure, e.g. air knives
    • C23C2/18—Removing excess of molten coatings from elongated material
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    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23G—CLEANING OR DE-GREASING OF METALLIC MATERIAL BY CHEMICAL METHODS OTHER THAN ELECTROLYSIS
    • C23G1/00—Cleaning or pickling metallic material with solutions or molten salts
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Abstract

The invention discloses a high-strength hot-base galvanized steel sheet with good forming performance and a manufacturing method thereof, belonging to the technical field of metallurgy. The hot-base galvanized steel sheet comprises the following chemical components in percentage by weight: 0.07 to 0.12 percent, si is less than or equal to 0.06 percent, mn:0.9 to 1.2 percent, less than or equal to 0.015 percent of P, less than or equal to 0.010 percent of S and less than or equal to Als:0.035 to 0.055 percent of Ti:0.015% -0.025%, nb:0.030% -0.045%, N is less than or equal to 0.0030%, nb+Ti is less than or equal to 0.045% -0.070%, the ratio of Ti to Nb is less than or equal to 0.5% -0.7, the yield strength Reh of the prepared hot-base galvanized steel sheet is 605-625 MPa, the tensile strength is 640-665 MPa, the elongation is more than or equal to 20%, the yield ratio is more than or equal to 0.9, and the surface quality meets the FC surface grade requirement in GB 2518.

Description

High-strength hot-base galvanized steel sheet with good forming performance and manufacturing method thereof
Technical Field
The invention belongs to the technical field of metallurgy, and particularly relates to a high-strength hot-base galvanized steel sheet with good formability and a manufacturing method thereof.
Background
The hot-base galvanized sheet has good mechanical property, forming property, welding property and corrosion resistance, and is widely applied to the industries such as building steel construction industry, storage industry, photovoltaic manufacturing industry and the like at the present stage. Compared with the traditional cold-base galvanized sheet material, the hot-base galvanized product directly uses the pickled hot-rolled sheet as the raw material for coating operation, can produce thicker products, and meanwhile, has the advantages of shorter production flow, lower cost, environmental protection and environmental protection due to the reduction of cold rolling procedures, and is increasingly replacing cold-rolled galvanized sheets with higher prices.
In the existing production technology, the high-strength grade hot-base galvanized steel sheet mainly has yield strength of 420-550 Mpa, tensile strength of 560-650 Mpa, lower elongation after fracture and poorer matching of strength and plasticity; meanwhile, the complex preparation process of the limited heat-base galvanized sheet is easy to cause poor surface quality of a galvanized steel sheet coating and poor platability, and finally, a high-strength grade steel heat-base galvanized steel coil with excellent performance and excellent surface quality cannot be obtained, so that the application field of the high-strength grade steel heat-base galvanized steel coil is greatly limited.
Through retrieval, patent CN111621706A discloses an aluminum-flower-free aluminum-silicon-plated steel plate and a preparation process and application thereof, and belongs to the field of metal materials. The steel plate comprises a substrate and a coating, wherein the chemical components of the substrate are as follows, by mass, C is less than or equal to 0.0030%, si is less than or equal to 0.030%, mn is less than or equal to 0.20%, P is less than or equal to 0.015%, S is less than or equal to 0.010%, als:0.030% -0.055%, nb is less than or equal to 0.10%, ti is less than or equal to 0.10%, N is less than or equal to 0.0040%, and the balance is Fe and unavoidable impurities; the main component of the plating layer is aluminum, and the size of aluminum flowers on the plating layer is smaller than 1mm; the preparation process comprises the following steps: and (3) carrying out steel making, continuous casting, hot rolling, cold rolling, hot dip aluminum-silicon plating, cooling after plating, aluminum powder spraying and finishing on molten iron, and continuing to carry out processes such as withdrawal straightening, roller coating, drying, oiling, coiling and the like to obtain the aluminum-flower-free aluminum-silicon plated steel plate. Although the components of the patent are similar, the cold rolling process is included, so that the manufacturing cost of the product is increased, the strength of the steel plate is limited, and the steel plate cannot be suitable for hot-base galvanized plates.
Chinese patent document of application publication number CN102703815A discloses 600 MPa-grade hot-rolled dual-phase steel and a preparation method thereof. The 600 MPa-level hot-rolled dual-phase steel comprises the following chemical components in percentage by mass: 0.05 to 0.07 percent, si:0.1 to 0.4 percent, mn:1.10 to 1.50 percent, cr:0.5 to 0.7 percent and the balance of Fe; the structure is soft phase ferrite and hard phaseMartensite, its yield strength Rp 0.2 355-375 MPa, tensile strength R m The tensile strength of the steel plate is similar to that of the steel plate, but the yield strength and the yield ratio of the steel plate are limited, wherein the yield ratio is 590-650 MPa, the yield ratio is 0.56-0.60, and the total elongation after fracture is 24-30%.
The invention discloses a 600 MPa-level high-yield-ratio high-plasticity cold-rolled steel plate and a preparation method thereof, wherein the steel plate comprises the following chemical components in percentage by mass: 0.06% -0.12%, si:0.02% -0.10%, mn:1.40% -2.00%, P: less than or equal to 0.015 percent, S: less than or equal to 0.010 percent of Al:0.02% -0.10%, N: less than or equal to 0.0050 percent, nb:0.015% -0.045%, ti:0.020% -0.055% and satisfies 0.035% -0.100% of Nb+Ti, and the balance of Fe and other unavoidable impurities. The yield strength is more than 500MPa, the tensile strength is more than 600MPa, the elongation after fracture is more than 19%, the yield ratio is more than 0.8, the steel plate does not belong to the field of plating products, and the surface lacks a pure zinc layer with a certain thickness, so that the steel plate cannot provide excellent corrosion resistance.
The invention discloses a hot-base zinc-flower-free galvanized steel coil and a production method thereof, wherein the steel plate comprises the following chemical components in percentage by mass: 0.15 to 0.18 percent; si is less than or equal to 0.1 percent; mn:0.67 to 0.7 percent; p is less than or equal to 0.02 percent; s is less than or equal to 0.01%; als:0.022 to 0.04 percent; nb: 0.009-0.012%; v:0.003 to 0.007 percent; ti: 0.048-0.06%, and the balance of Fe and unavoidable impurities. The yield strength reaches 500-600 MPa, the tensile strength reaches 600-700 MPa, and the elongation is more than or equal to 18%; the hot-base galvanized plate has tensile strength similar to that of the product of the patent, but has lower yield strength, and the manufacturing cost of the product is higher because a certain vanadium (V) alloy is added to adjust the performance of the steel plate.
The invention discloses a hot-base galvanized steel coil and a preparation method thereof, wherein the steel plate comprises the following chemical components in percentage by mass: 0.06-0.09%, si:0.04 to 0.08 percent, mn:1.0 to 1.2 percent, P is less than or equal to 0.02 percent, S is less than or equal to 0.01 percent, cu is less than or equal to 0.02 percent, ni is less than or equal to 0.03 percent, cr is less than or equal to 0.01 percent, and the balance is Fe and unavoidable impurities. The hot-base galvanized sheet is easy to cause surface quality defects such as plating omission, zinc slag and the like of the plating product because the front-stage manufacturing procedures such as steelmaking, hot rolling, acid washing and the like are not controlled.
The invention discloses a hot-dip aluminum-zinc steel plate with tensile strength of 600MPa and a manufacturing method thereof, wherein the hot-dip aluminum-zinc steel plate has a patent publication number of CN 110541107A. The steel plate comprises the following chemical components in percentage by mass: 0.12 to 0.15 percent, si:0.1 to 0.2 percent, mn:1.0 to 1.2 percent, ti:0.025 to 0.035 percent, P:0 to 0.015 percent, S:0 to 0.015 percent, B:0.0020 to 0.0040 percent, and the balance of Fe and unavoidable impurities. Its yield strength Rp 0.2 350-450 MPa, tensile strength R m The content of Si in the steel plate is 600-700 MPa, but the steel plate is easy to deteriorate in surface quality, poor in coating adhesion and low in yield strength and yield ratio.
The hot-base galvanized steel sheet in the above patent has problems of low strength and yield ratio.
Disclosure of Invention
1. Problems to be solved
Aiming at the problem that the strength, the yield ratio and the plasticity of the hot-base galvanized plate cannot be considered in the prior art, the invention provides the high-strength hot-base galvanized steel plate with good forming performance and the manufacturing method thereof, and the manufactured steel plate has high strength and high yield ratio and simultaneously maintains higher plasticity.
2. Technical proposal
In order to solve the problems, the technical scheme adopted by the invention is as follows:
the invention provides a high-strength hot-base galvanized steel sheet with good forming performance and a manufacturing method thereof, wherein the hot-base galvanized steel sheet comprises the following chemical components in percentage by weight: 0.07 to 0.12 percent, si is less than or equal to 0.06 percent, mn:0.9 to 1.2 percent, less than or equal to 0.015 percent of P, less than or equal to 0.010 percent of S and less than or equal to Als:0.035 to 0.055 percent of Ti:0.015% -0.025%, nb:0.030% -0.045%, N is less than or equal to 0.0030%, and the balance is iron and other impurities. The chemical composition ratio of the hot-base galvanized steel sheet meets the formula: nb+Ti is more than or equal to 0.045% and less than or equal to 0.070, and the ratio of Ti to Nb is more than or equal to 0.5 and less than or equal to 0.7.
The steel grade composition control principle of the invention is as follows:
c: is a solid solution strengthening element with stronger economy in steel, and can effectively balance the strength and the ductility of the steel. The strength of the steel matrix is obviously increased along with the increase of the carbon content, but the plasticity of the material is also rapidly reduced, so that the high strength and the high yield ratio of the steel are ensured, and meanwhile, the plasticity and the processability of the material are considered. In the invention, C is controlled to be 0.07-0.12%.
Si: the invention mainly adopts precipitation strengthening of niobium-titanium carbonitride in ferrite phase, and improves the strength, plasticity and yield ratio of the steel plate by grain refinement. However, the silicon content is too high, so that the silicon element on the surface of the steel plate is easily enriched and oxidized, the binding force of a plating layer is affected, the conditions of plating omission, zinc slag and the like are easily caused, and the surface quality of the plating layer is deteriorated. The Si content in the invention is controlled below 0.06 percent.
Mn: the important solid solution strengthening elements can enlarge the austenite phase region, stabilize austenite, improve the hardenability of the steel plate and ensure the comprehensive performance of the steel, but the too high manganese content easily causes the formation of a strip-shaped structure in the material, influences the welding performance of the steel plate, and causes insufficient material strength. Therefore, the Mn content of the invention is controlled to be 0.9-1.2 percent of Mn.
P, S: both are detrimental elements in steel in this patent. P is easy to gather on the grain boundary to cause embrittlement, and causes cold embrittlement; s is liable to form inclusions such as MnS with Mn element in steel, and the performance and weldability of steel are deteriorated. Meanwhile, too high S element is easy to consume the precipitation strengthening elements such as Ti, nb and the like in the material of the invention, and precipitates in the smelting or hot rolling process to form coarse (Ti/Nb) 4 C 2 S 2 And the like, and affects the precipitation strengthening effect of the carbonitride of niobium titanium. Therefore, the P and S contents in the present invention are controlled to be 0.015% and 0.010% or less, respectively.
Al: al is an important deoxidizer, and forms AlN at the same time, thereby playing a role in refining grains. Als in the steel is not too low, otherwise, oxides of a large amount of Mn, si and other elements are easily dispersed in the steel to deteriorate the quality of the steel, but excessive Al is added to easily form aluminum oxide to increase inclusions, so that the plasticity of the steel and the surface state of a steel substrate are affected, and the Al content is controlled to be 0.035-0.055%.
N: the steel sheet can be reinforced, and the low-temperature toughness and weldability of the steel sheet are improved, but a large amount of nitrides are precipitated, so that the precipitation strengthening elements such as Ti, nb and the like in the material are easily excessively consumed, and the material strength, the elongation and the weldability are deteriorated, and the N content is controlled to be less than 0.0030 percent.
Nb, ti: both are precipitation strengthening elements, can effectively improve the strength of steel and have the function of refining grains. Nb and Ti elements are added into the steel, nitrides, carbonitrides and carbosulfides of (Ti/Nb) are formed at high temperature, a ferrite matrix is purified, the grain size is refined, fine and dispersed carbides are formed at low temperature, and the strength and plasticity of the steel plate are effectively ensured. Considering the economical efficiency and low cost of the materials, the Ti content of the invention is controlled to be 0.015-0.025%, and the Nb content is controlled to be 0.030-0.045%.
The total value of the chemical components Ti+Nb and the ratio Ti/Nb of the invention need to satisfy the formula: nb+Ti is more than or equal to 0.045% and less than or equal to 0.070, and the reason that the ratio of Ti to Nb is more than or equal to 0.5 and less than or equal to 0.7 is satisfied: if the total value of ti+nb is less than 0.045%, insufficient precipitation of fine carbides and carbonitrides dispersed in ferrite is likely to occur, resulting in insufficient strength of the product. If the content exceeds 0.070%, the precipitation strengthening effect is too strong, the plasticity is easily low, the processability of the material is weakened, and the economical and low-cost properties of the material are not met. Under the condition of keeping the total value of Ti and Nb unchanged, if the ratio of Ti to Nb is less than or equal to 0.5, the Ti element in solid solution in the steel is lower, and as the precipitation temperature of the nitride or the carbonitride of titanium is higher than that of the niobium element, the material is easy to cause that enough carbonitride cannot be precipitated in the continuous casting or hot rolling process, the growth of the grain size cannot be effectively inhibited, the grain size of the material is lower, and the strength, the yield ratio and the plasticity are obviously insufficient; similarly, if the ratio of Ti to Nb is more than or equal to 0.7, insufficient precipitation of niobium carbonitride in the hot rolling coiling or subsequent galvanization annealing process of the material is easy to cause the reduction of the strength and yield ratio of the material.
The invention also discloses a method for manufacturing the high-strength hot-base galvanized steel sheet with good forming performance, which mainly comprises converter smelting, continuous casting, hot rolling, acid washing, horizontal annealing, galvanization treatment and leveling, wherein a continuous casting plate blank is heated to 1210-1250 ℃ by a heating furnace and then hot rolled, the hot rolling is a two-section rolling process, rough rolling is 5-pass continuous rolling, finish rolling is 7-pass continuous rolling, high-temperature coiling and heat preservation are carried out by a hot coiling box after rough rolling, the temperature is controlled to 1150-1180 ℃, the finish rolling starting temperature is 1010-1150 ℃, the finish rolling temperature is 860-900 ℃, high-pressure water is adopted for dephosphorization or cooling between an inlet, an outlet and a frame of rough rolling and finish rolling, the inclination angle of a water spray nozzle is downward 0-15 ℃, the maximum pressure value of the nozzle is 180-200 bar, the distance from the nozzle to the plate blank is 70-100 mm, a laminar cooling mode of front-stage cooling is adopted after finish rolling, and the coiling temperature is controlled to 580-600 ℃ to obtain a hot rolled steel coil.
The hot rolled steel coil is uncoiled again and then is cooled and polished after being subjected to acid washing, annealing in a horizontal continuous annealing furnace, hot galvanizing, air knife blowing and plating, and a finished hot-base galvanized steel plate with the thickness of 2.50 mm-6.5 mm is obtained after coiling, in the acid washing treatment procedure, a withdrawal straightening machine is adopted to withdraw and straighten oxide scales on the surface of the steel plate, the withdrawal straightening elongation is 1.2-1.8%, a pickling tank consists of three acid tanks which are connected in series and are mutually independent, three-section continuous hydrochloric acid pickling is adopted, and the HCL concentration of a No. 1 acid tank is 40-75 g/L; the HCL concentration of the No. 2 acid tank is 95-140 g/L; the concentration of HCL in the No. 3 acid tank is 140-180 g/L, the pickling temperature is 70-80 ℃, the temperature of the rinse water after pickling is 50-80 ℃, and the drying temperature is 80-110 ℃; in the annealing treatment, the steel plate is annealed in a modified Sendzimir horizontal annealing furnace, the temperature of a direct-fired section (NOF section) is 650-670 ℃, the temperature of a radiation section (RTF section) is 630-650 ℃, the temperature of an electromagnetic heat preservation section (ESF section) is 630-650 ℃, the temperature of a cooling section (JCS section) is 455-465 ℃, and H in the furnace 2 The content is 12 to 16 percent, and the oxygen content (O) 2 ) Less than or equal to 20ppm, and the dew point (Dp) is less than or equal to-25 ℃; controlling the running speed of the strip steel to be 50-75m/min, and enabling the annealed steel plate to enter a hot galvanizing process, wherein the temperature of a zinc pot is 450-460 ℃; the zinc liquid in the zinc pot mainly comprises the following components: 0.18 to 0.25 percent of Fe:0.010 to 0.030 percent and the balance of Zn. The production line speed in the air knife blowing process is 50-75m/min, the air knife distance is 14-21mm, the air knife pressure is 110-130 mbar, and the air knife height is 160-200mm. After platingThe temperature of an upper cooling tower in the cooling process is less than or equal to 200 ℃, and the water quenching temperature in the water quenching treatment process is 40-60 ℃; the finishing elongation is 0.5-1.0%.
The reason why the above process parameters are selected in the invention is as follows:
the soaking temperature of the plate blank in a heating furnace is 1210-1250 ℃, if the soaking temperature is controlled below 1210 ℃, the solid solution quantity of Nb is easily reduced, the precipitation strengthening effect is weakened, but the soaking temperature is not higher than 1250 ℃, so that excessive primary iron scales of the plate blank are avoided, and the dephosphorization difficulty is increased.
After rough rolling, the steel plate is coiled at high temperature by adopting a hot coiling box, the temperature is controlled to be 1150-1180 ℃, and the hot coiling box has the functions of breaking scales and guaranteeing the temperature uniformity of strip steel. The mechanical bending deformation of the plate blank in the coiling and uncoiling processes is adopted to break the secondary iron oxide scale with brittle and hard surface, and then the high-speed coiling is adopted to throw the iron oxide scale away from the strip steel, so that a good descaling effect on the surface is realized; for temperature control, if the temperature is lower than 1150 ℃, the difference of the strip steel temperature in the subsequent finish rolling is easy to be larger, and the stability of the performance is not facilitated; and is higher than 1180 ℃, the secondary iron scale is easy to increase, which is not beneficial to the surface quality of the subsequent steel plate.
The initial rolling temperature of the finish rolling is controlled to be 1010-1150 ℃, and the finish rolling is mainly used for realizing the rolling in a complete austenite region and reducing the rolling load of a front stand of a rolling mill;
the finishing temperature is controlled to 860-900 ℃ and lower than 860 ℃ for rolling, which is not beneficial to the precipitation of carbonitride of microalloy elements such as Ti, nb and the like, weakens the grain refining effect and easily increases the banded structure in the steel. If the finish rolling temperature exceeds 900 ℃, recrystallized grains are easy to grow abnormally, performance stability is affected, meanwhile, the excessive finish rolling temperature leads to increased oxide generation amount, the difficulty of pickling the steel plate is increased, the surface quality of the steel plate is poor, and the surface grade is reduced.
The maximum pressure value of spray water from the spray nozzle between the inlet and outlet of rough rolling and finish rolling and the frame is 180-200 bar, and the distance from the spray nozzle to the slab is 70-100 mm. The dip angle of the nozzle is 0-15 degrees downwards, the process mainly removes primary and secondary iron scales formed on the surface of a billet in the heating and hot rolling processes, prevents iron oxides from being pressed into the surface of a substrate too deeply, increases the pickling difficulty, and further causes the surface quality defects such as plating omission, chromatic aberration and the like of a steel plate in the subsequent plating process;
the coiling temperature is controlled at 580-600 ℃, if the temperature is higher than 600 ℃, the coarsening of carbonitride of microalloy elements such as Ti, nb and the like and the increase of grain size are easily caused, so that the strength of the steel plate is reduced and the plasticity is deteriorated; meanwhile, more ferric oxide is formed on the surface, so that the surface quality of the subsequent steel plate is easily deteriorated, and if the temperature is lower than 580 ℃, the precipitation amount of carbonitrides of microalloy elements such as Ti, nb and the like is easily reduced, so that the strength of the steel plate is lower, and the yield ratio is reduced.
In the pickling process, the elongation of the withdrawal and straightening is set to be 1.2-1.8%, the primary function is to destroy the continuity and adhesiveness of the iron scale on the surface of the steel plate, and if the elongation is lower than 1.2%, the pickling effect is insufficient easily, so that the problems of plating omission and the like in the subsequent galvanization process are caused; if the loss exceeds 1.8%, the degree of loss of the withdrawal and straightening unit is increased.
In the pickling process, the HCL concentration of a No. 1 pickling tank in the pickling tank is 40-75 g/L; the HCL concentration of the No. 2 acid tank is 95-140 g/L; the concentration of HCL in the No. 3 acid tank is 140-180 g/L, the pickling temperature is 70-80 ℃, the temperature of the rinse water after pickling is 50-80 ℃, and the drying temperature is 80-110 ℃; the method mainly removes greasy dirt, rust and oxide skin on the surface of the hot rolled steel substrate to increase the binding force between a zinc layer and the substrate and ensure good surface quality of a steel plate coating.
In the annealing treatment, the steel plate is annealed in an improved Sendzimir horizontal annealing furnace, the temperature of a direct-fired section (NOF section) is 650-670 ℃, the temperature of a radiation section (RTF section) is 630-650 ℃, the temperature of an electromagnetic heat preservation section (ESF section) is 630-650 ℃, and the temperature of a cooling section (JCS section) is 455-465 ℃; the running speed of the strip steel is controlled to be 50-75m/min, and the process can further combine trace chemical elements such as Ti, nb and the like dissolved in the steel with carbon in the hot rolling coiling process to form more dispersed and fine carbide in ferrite, so that the strength and yield ratio of the steel plate are improved. Meanwhile, the temperature of the plate belt of the direct-fired section (NOF section) is slightly higher than that of the plate belt of the radiation section (RTF section), so that the plate belt can be ensured to finish the heating annealing and heat preservation processes in the direct-fired section, the energy consumption can be saved, and the production cost can be reduced. The annealing temperature of the hot-base galvanized steel sheet is lower than that of a cold-rolled steel sheet, and in the cold-rolling process, as the crystal grains are required to be rolled, broken and grown again, the crystal grains are easier to be coarser as the temperature is higher, so that the strength and the yield ratio of the steel sheet are reduced, and the preparation of the hot-base galvanized steel sheet is not required to be subjected to cold rolling, so that the lower annealing temperature can be selected, and the higher strength can be obtained.
H in annealing furnace 2 The content is 12 to 16 percent, the oxygen content is oxygen content (O) 2 ) Less than or equal to 20ppm, and the dew point (Dp) is less than or equal to-25 ℃; the limitation of the hydrogen content, the oxygen content and the dew point can ensure that the residual ferric oxide on the surface of the steel plate is fully reduced to form spongy reduced iron, thereby being beneficial to improving the adhesive force of a zinc layer and simultaneously reducing the occurrence of surface quality problems such as missing plating, zinc slag and the like of strip steel in the coating process.
The temperature of the zinc pot is 450-460 ℃; the zinc liquid mainly comprises the following components: al:0.18 to 0.25 percent of Fe:0.010 to 0.030 percent and the balance of Zn. The control of the temperature and the aluminum content of the zinc pot can improve the adhesive force between the plating layer and the steel plate, improve the purity of the plating solution and prevent the surface quality of the plating layer from deteriorating.
The distance between the air knives in the air knife blowing process is 14-21mm, the pressure of the air knives is 110-130 mbar, and the height of the air knives is 160-200mm. The temperature of the upper cooling tower is less than or equal to 200 ℃, the water quenching temperature is 40-60 ℃, and the finishing elongation is 0.5-1.0%. By adopting the air knife and the subsequent coating cooling parameters and combining the finishing elongation control, the uniformity and corrosion resistance of the zinc layer thickness can be ensured, and good surface quality of the steel plate coating can be obtained.
Compared with the conventional cold-base galvanized steel sheet, the hot-base galvanized steel sheet has the advantages that the cold rolling process is reduced, the work hardening effect cannot be generated, so that the hot-base galvanized steel sheet is difficult to reach higher strength, the strength of a base plate is usually improved by adding various reinforcing elements, but the strength is often reduced due to the improvement of the strength, so that the hot-base galvanized steel sheet has the problem of insufficient strength and yield ratio, the high-strength hot-base galvanized steel sheet with good forming performance and the manufacturing method thereof are provided.
Furthermore, the invention further improves the surface quality of the steel plate, si with lower content is added, and injection parameters of high-pressure water in the dephosphorization or cooling process are controlled at the same time, so that iron oxide scales formed on the surface of a steel billet in the heating and hot rolling processes are removed, the iron oxide is prevented from being pressed into the surface of the substrate too deeply, the pickling difficulty is increased, further, the surface quality defects such as plating omission, chromatic aberration and the like of the steel plate in the subsequent plating process are caused, and the surface quality of the steel plate is improved.
The hot-base galvanized steel sheet with higher strength and yield ratio, better plasticity, low cost and economical efficiency is finally obtained through controlling the smelting components of the steel and the technological parameters such as hot rolling, acid washing, annealing, galvanization and the like, the mechanical property of the hot-base galvanized steel sheet meets the requirements of upper yield strength Reh reaching 605-625 MPa, tensile strength reaching 640-665 MPa, elongation being more than or equal to 20%, yield ratio being more than or equal to 0.9, grain size being more than or equal to 12, the coating quality of the steel sheet is high, and the surface quality meets the requirements of FC surface grade in GB 2518.
3. Advantageous effects
Compared with the prior art, the invention has the beneficial effects that:
(1) According to the invention, on the basis of adding a proper amount of economical C element and Mn element into the steel plate, a certain amount of Ti and Nb element are added, a certain manufacturing process is matched, and the content ratio of the Ti and Nb elements is controlled, so that the precipitation strengthening and grain refinement combined action is generated, and the hot-base galvanized steel plate compatible with high strength, high yield ratio and high plasticity is realized, the yield strength Reh of the prepared hot-base galvanized steel plate reaches 605-625 MPa, the tensile strength reaches 640-665 MPa, the elongation is more than or equal to 20%, and the yield ratio is more than or equal to 0.9;
(2) The reasonable hot rolling structure and the hot rolled base plate with excellent surface state are obtained through the controlled rolling and cooling and dephosphorization processes during hot rolling, the grain size is more than or equal to 12 grades, and the surface quality meets the FC surface grade requirement in GB 2518;
(3) The invention utilizes the characteristics of short-time annealing, rapid cooling, high-reducibility furnace atmosphere and the like of the horizontal furnace annealing furnace to control the working procedure parameters of a zinc pot, an air knife, cooling after plating and the like, and finally the obtained hot-base galvanized steel sheet can meet the requirements of industries such as building, storage industry, photovoltaic manufacturing industry and the like on strength, plasticity and high surface quality.
Drawings
The technical solution of the present invention will be described in further detail below with reference to the accompanying drawings and examples, but it should be understood that these drawings are designed for the purpose of illustration only and thus are not limiting the scope of the present invention. Moreover, unless specifically indicated otherwise, the drawings are intended to conceptually illustrate the structural configurations described herein and are not necessarily drawn to scale.
FIG. 1 is a metallographic structure diagram of a steel plate according to the invention;
FIG. 2 shows the surface state of the steel sheet according to the present invention.
Detailed Description
The following detailed description of exemplary embodiments of the invention refers to the accompanying drawings, which form a part hereof, and in which are shown by way of illustration exemplary embodiments in which the invention may be practiced. While these exemplary embodiments are described in sufficient detail to enable those skilled in the art to practice the invention, it is to be understood that other embodiments may be realized and that various changes to the invention may be made without departing from the spirit and scope of the invention. The following more detailed description of the embodiments of the invention is not intended to limit the scope of the invention, as claimed, but is merely illustrative and not limiting of the invention's features and characteristics in order to set forth the best mode of carrying out the invention and to sufficiently enable those skilled in the art to practice the invention. Accordingly, the scope of the invention is limited only by the attached claims.
The invention is further illustrated by the following examples. The composition of the example steel is shown in Table 1, the hot rolling process parameters are shown in Table 2, the pickling process parameters are shown in Table 3, the annealing process parameters are shown in Table 4, the hot dip and air knife process parameters are shown in Table 5, and the mechanical properties and surface quality are shown in Table 6.
TABLE 1 chemical composition (mass%) of the steels according to the examples of the present invention
Examples 1 2 3 4 5 6
C 0.1 0.07 0.12 0.08 0.09 0.09
Si 0.04 0.03 0.05 0.05 0.06 0.05
Mn 1 0.9 1.2 1 1.1 1
P 0.007 0.006 0.008 0.008 0.008 0.007
S 0.008 0.009 0.007 0.008 0.006 0.006
Als 0.045 0.035 0.05 0.045 0.035 0.045
N 0.002 0.002 0.0015 0.002 0.0015 0.002
Ti 0.02 0.015 0.025 0.018 0.02 0.022
Nb 0.04 0.03 0.035 0.035 0.035 0.039
Ti+Nb 0.06 0.045 0.07 0.053 0.055 0.061
Ti/Nb 0.5 0.5 0.7 0.51 0.57 0.56
TABLE 2 Hot Rolling Process parameters for steels according to various embodiments of the present invention
Examples 1 2 3 4 5 6
Casting blank heating temperature (DEG C) 1230 1210 1250 1230 1210 1220
Thermal insulation temperature (DEG C) of thermal coiling box 1160 1150 1180 1160 1170 1160
Finish rolling start temperature (. Degree. C.) 1140 1150 1010 1100 1090 1150
Finish rolling finishing temperature (. Degree. C.) 880 900 880 900 890 885
Coiling temperature (. Degree. C.) 580 600 580 590 585 585
Maximum nozzle pressure (bar) 195 195 180 190 200 200
Distance of nozzle from slab (mm) 80 80 70 75 100 90
Nozzle angle (°) 14 13 15 13 15 13
TABLE 3 pickling process parameters for the steels of the examples of the invention
Figure BDA0004107342460000081
Figure BDA0004107342460000091
TABLE 4 annealing process parameters for steels according to various embodiments of the present invention
Examples 1 2 3 4 5 6
Direct combustion section (DEG C) 660 670 650 655 665 650
Radiant section (DEG C) 640 640 630 650 635 645
Thermal insulation section (DEG C) 640 640 630 650 635 645
Cooling section (DEG C) 455 460 455 465 460 460
In-furnace H 2 Content (%) 13 12 15 16 14 12
In-furnace O 2 Content (ppm) 18 19 20 19 17 18
Dew point (. Degree. C.) -25 -26 -30 -28 -29 -27
Running speed (m/min) 55 60 70 75 50 60
TABLE 5 hot dip coating and air knife process parameters for the steels of the various embodiments of the present invention
Examples 1 2 3 4 5 6
Zinc pot temperature (DEG C) 455 460 450 453 459 455
Content of Al in Zinc pot (%) 0.2 0.23 0.25 0.18 0.21 0.22
Fe content (%) 0.02 0.03 0.01 0.015 0.02 0.025
Distance of air knife (mm) 15 21 14 18 16 20
Air knife pressure (mba) 120 110 130 120 125 130
Height of air knife (mm) 160 170 180 200 180 190
Upper cooling tower temperature (DEG C) 200 195 190 190 195 200
Water quenching temperature (DEG C) 50 40 60 55 45 50
Gloss elongation (%) 0.8 1 0.5 0.9 1 0.8
TABLE 6 mechanical Properties and surface quality of the steels according to the examples of the invention
Figure BDA0004107342460000092
Figure BDA0004107342460000101
According to the invention, a low-cost component design is adopted, the embodiment steel is smelted and continuously cast, rolling and cooling are controlled according to a set hot rolling process, high-pressure dephosphorization is carried out, a hot rolled plate with certain strength and surface quality is obtained, the hot rolled plate is annealed on a horizontal annealing line after pickling, galvanization and finishing are carried out, the finally obtained steel plate structure consists of a plain body and pearlite, the grain size is fine, the ferrite contains a large number of fine and dispersed niobium-titanium carbonitride precipitates, the mechanical property meets the upper yield strength Reh reaching 605-625 MPa, the tensile strength reaching 640-665 MPa, the elongation being more than or equal to 20%, the yield ratio being more than or equal to 0.9, the grain size being more than or equal to 12 levels, and the hot-base galvanized steel plate with high surface quality grade of a coating and economy and low manufacturing cost is manufactured.

Claims (10)

1. The high-strength hot-base galvanized steel sheet with good forming performance is characterized in that the hot-base galvanized steel sheet comprises the following chemical components in percentage by weight: 0.07 to 0.12 percent, si is less than or equal to 0.06 percent, mn:0.9 to 1.2 percent, less than or equal to 0.015 percent of P, less than or equal to 0.010 percent of S and less than or equal to Als:0.035 to 0.055 percent of Ti:0.015% -0.025%, nb:0.030% -0.045%, N is less than or equal to 0.0030%, and the balance is iron and other impurities, wherein the chemical composition ratio satisfies the formula: nb+Ti is more than or equal to 0.045% and less than or equal to 0.070%, and the ratio of Ti to Nb is more than or equal to 0.5 and less than or equal to 0.7.
2. The high-strength hot-base galvanized steel sheet with good formability according to claim 1, characterized in that the hot-base galvanized steel sheet has an upper yield strength Reh of 605-625 MPa, a tensile strength of 640-665 MPa, an elongation of 20% or more, a yield ratio of 0.9 or more, a grain size of 12 or more, and a surface quality satisfying the FC surface grade requirements in GB 2518.
3. A method for producing the high-strength hot-base galvanized steel sheet having excellent formability as claimed in any one of claims 1 to 2, characterized in that the steps include converter smelting, continuous casting, hot rolling, pickling, annealing, galvanization, air knife purging, cooling after plating, and leveling.
4. The method for producing a high-strength hot-base galvanized steel sheet having excellent formability as recited in claim 3, wherein the continuous casting slab is heated to 1210 to 1250 ℃ by a heating furnace.
5. The method for manufacturing a high-strength hot-base galvanized steel sheet with good formability according to claim 4, wherein the hot rolling is a two-stage rolling process, the rough rolling is 5-pass continuous rolling, the finish rolling is 7-pass continuous rolling, the hot rolling box is adopted for high-temperature coiling and heat preservation after the rough rolling, the temperature is controlled to 1150-1180 ℃, the finish rolling start rolling temperature is 1010-1150 ℃, and the finish rolling temperature is 860-900 ℃; and after finish rolling, adopting a laminar cooling mode of front-stage cooling, and controlling the coiling temperature to be 580-600 ℃ to obtain the hot rolled steel coil.
6. The method for manufacturing a high-strength hot-base galvanized steel sheet with excellent formability according to claim 5, characterized in that high-pressure water is used for dephosphorization or cooling between an inlet, an outlet and a frame of rough rolling and finish rolling, an inclination angle of a water spray nozzle is downward 0 to 15 degrees, a maximum pressure value of the nozzle is 180 to 200bar, and a distance from the nozzle to a slab is 70 to 100mm.
7. The method for manufacturing a high-strength hot-base galvanized steel sheet with good formability according to claim 6, characterized in that in the pickling treatment process, a withdrawal straightening machine is adopted to withdraw and straighten iron scale on the surface of the steel sheet, the withdrawal straightening elongation is 1.2-1.8%, the pickling tank consists of three acid tanks which are connected in series and are mutually independent, three-section continuous hydrochloric acid pickling is adopted, and the HCL concentration of the No. 1 acid tank is 40-75 g/L; the HCL concentration of the No. 2 acid tank is 95-140 g/L; the HCL concentration of the No. 3 acid tank is 140-180 g/L, the acid washing temperature is 70-80 ℃, the rinse water temperature after acid washing is 50-80 ℃, and the drying temperature is 80-110 ℃.
8. The method for producing a high-strength hot-base galvanized steel sheet with excellent formability as claimed in claim 7, wherein in the annealing treatment, the steel sheet is annealed in a modified sendzimir horizontal annealing furnace at a direct combustion stage temperature of 650 to 670 ℃, a radiation stage temperature of 630 to 650 ℃, an electromagnetic heat-insulating stage temperature of 630 to 650 ℃, a cooling stage temperature of 455 to 465 ℃ and an in-furnace H 2 The content is 12-16%, the oxygen content is less than or equal to 20ppm, and the dew point is less than or equal to-25 ℃.
9. The method for manufacturing a high-strength hot-base galvanized steel sheet with good formability according to claim 8, wherein the annealed steel sheet enters a hot galvanizing process, the running speed of strip steel is 50-75m/min, and the temperature of a zinc pot is 450-460 ℃; the zinc liquid in the zinc pot comprises the following components: 0.18 to 0.25 percent of Fe:0.010 to 0.030 percent and the balance of Zn.
10. The method for producing a high-strength hot-base galvanized steel sheet with excellent formability according to claim 9, characterized in that a line speed in the air knife purging process is 50-75m/min, an air knife distance is 14-21mm, an air knife pressure is 110-130 mbar, an air knife height is 160-200mm, an upper cooling tower temperature in a post-plating cooling process is not more than 200 ℃, and a water quenching temperature in a water quenching process is 40-60 ℃; the finishing elongation is 0.5-1.0%.
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