CN111893378A - Low-cost high-plasticity cold-rolled galvanized steel plate and preparation method thereof - Google Patents
Low-cost high-plasticity cold-rolled galvanized steel plate and preparation method thereof Download PDFInfo
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
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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
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- 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
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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
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- C21D8/0236—Cold 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
- C21D8/0273—Final recrystallisation annealing
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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
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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
- C23C2/34—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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- 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
- C21D2211/001—Austenite
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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
- 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
- C21D2211/005—Ferrite
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- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
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Abstract
The invention provides a low-cost high-plasticity cold-rolled galvanized steel plate, which belongs to the field of manufacturing of high-strength steel for automobiles, and comprises the following chemical components in percentage by mass: c: 0.10% -0.15%, Si: 0.3% -0.6%, Mn: 1.1% -1.7, Al: 0.3 to 0.6 percent of the total weight of the alloy, less than or equal to 0.01 percent of P, less than or equal to 0.005 percent of S, and the balance of Fe and inevitable impurities; the metallographic structure of the steel sheet had the following composition in terms of area ratio: ferrite: 50% -75%, bainite + martensite: 20% -40%, retained austenite: 3 to 8 percent. The steel plate solves the problem that the traditional high-strength steel is difficult to form on a complex stamping structural part, and effectively reduces the alloy cost. The invention also provides a preparation method of the low-cost high-plasticity cold-rolled galvanized steel sheet.
Description
Technical Field
The invention belongs to the field of manufacturing of high-strength steel for automobiles, and relates to a low-cost high-plasticity cold-rolled galvanized steel sheet and a preparation method thereof.
Background
In order to achieve a light weight of an automobile body and to improve the collision safety of automobiles, the use of advanced high-strength steel in a body-in-white is increasing day by day. At present, dual-phase steel has become the most widely used steel grade in advanced high-strength steel based on its higher strength, good work hardening performance and continuous yield property. However, conventional dual phase steels have not been satisfactory for forming high-drawability automobile parts. Although C-Mn-Al based hot dip galvanized Transformation induced plasticity (TRIP) steel has good plasticity, its strength is generally low when Al is used for Si. In order to compensate the strength loss of part of hot galvanizing TRIP steel, elements such as Cu, Nb, V, Ti, P and the like are added, so that the alloy cost or the process cost is increased.
Disclosure of Invention
In order to solve the technical problem of insufficient steel plasticity of the existing high-strength steel, the invention provides a low-cost high-plasticity cold-rolled galvanized steel sheet, which solves the problem of difficult forming of the traditional high-strength steel on a complex stamping structural member and effectively reduces the alloy cost.
The invention also provides a preparation method of the low-cost high-plasticity cold-rolled galvanized steel sheet.
The invention is realized by the following technical scheme:
a low-cost high-plasticity cold-rolled galvanized steel sheet comprises the following chemical components in percentage by mass:
c: 0.10% -0.15%, Si: 0.3% -0.6%, Mn: 1.1% -1.7%, Al: 0.3 to 0.6 percent of the total weight of the alloy, less than or equal to 0.01 percent of P, less than or equal to 0.005 percent of S, and the balance of Fe and inevitable impurities;
the metallographic structure of the steel sheet had the following composition in terms of area ratio:
ferrite: 50% -75%, bainite + martensite: 20% -40%, retained austenite: 3% -8%;
the proportion of the retained austenite existing in the ferrite grain boundary is more than or equal to 90 percent.
Furthermore, in the chemical components of the steel plate, the impurity content meets the following requirements in percentage by mass:
Cu≤0.01％，Ni≤0.01％，Mo≤0.003％，Nb≤0.003％，V≤0.005％，Ti≤0.005％，B≤0.0004％，N≤0.008％。
further, the surface of the steel plate is provided with a hot dip galvanizing layer.
A preparation method of a low-cost high-plasticity cold-rolled galvanized steel sheet comprises the following steps:
continuously casting molten steel into a slab, wherein the chemical composition of the molten steel is the same as that of the steel plate according to claim 1 or 2;
carrying out hot rolling on the plate blank to obtain a hot rolled plate;
carrying out acid pickling on the hot rolled plate, and then carrying out cold rolling to obtain a cold-hardened steel plate;
and performing surface hot galvanizing on the cold-hardened steel plate after continuous annealing.
Further, in the hot rolling process: the heating temperature of the plate blank is 1250-1300 ℃, the soaking is carried out for 30-100 min, the finishing temperature is controlled to be 860-900 ℃, and the plate blank is coiled at 640-680 ℃ after laminar cooling.
Furthermore, the thickness of the hot rolled plate is 3.0-5.0 mm, and the thickness of the cold-hardened steel plate is 0.8-2.0 mm.
Further, in the continuous annealing process, the preheating temperature is 200-240 ℃, the heating temperature is 750-830 ℃, the soaking temperature is 750-830 ℃, the slow cooling temperature is 650-720 ℃, and the flash cooling temperature is 450-470 ℃.
Furthermore, in the hot galvanizing process, the galvanizing temperature is 450-470 ℃, and the finishing elongation of the steel plate is 0.2-0.5%.
Further, in the continuous annealing process, the running speed of the steel plate in the furnace zone is 60-110 m/min.
Furthermore, in the continuous annealing process, the dew point is controlled to be-30 ℃ to-10 ℃.
One or more technical solutions in the embodiments of the present invention have at least the following technical effects or advantages:
1. the invention relates to a low-cost high-plasticity cold-rolled galvanized steel sheet, which adopts a C-Si-Mn-Al alloy system design, does not contain any other noble alloy elements (Mo, Ni, Nb and the like), obviously reduces the material cost on the premise of meeting the strength requirement, introduces a certain amount of residual austenite on the basis of a traditional two-phase steel body and martensite two-phase structure through chemical composition improvement and process optimization, generates a TRIP effect in the deformation process, and increases the elongation after fracture of the steel sheet to more than 30 percent so as to adapt to the production of automobile parts with complex drawing and forming requirements.
2. According to the preparation method of the low-cost high-plasticity cold-rolled galvanized steel sheet, the high-plasticity cold-rolled steel sheet is obtained by replacing Si with Al and strictly controlling the atmosphere and the dew point of an annealing furnace, the galvanized surface quality is good, and the additional value of the steel sheet is improved.
Drawings
In order to more clearly illustrate the technical solutions in the embodiments of the present invention, the drawings needed to be used in the description of the embodiments are briefly introduced below, and it is obvious that the drawings in the following description are some embodiments of the present invention, and it is obvious for those skilled in the art to obtain other drawings based on the drawings without creative efforts.
FIG. 1 is a metallographic photograph showing a microstructure of a low-cost high-plasticity cold-rolled galvanized steel sheet obtained in example 1 of the present invention;
FIG. 2 is an Electron Back Scattering Diffraction (EBSD) analysis chart of the microstructure of the low-cost high-plasticity cold-rolled galvanized steel sheet prepared in example 1 of the invention.
Detailed Description
The present invention will be described in detail below with reference to specific embodiments and examples, and the advantages and various effects of the present invention will be more clearly apparent therefrom. It will be understood by those skilled in the art that these specific embodiments and examples are for the purpose of illustrating the invention and are not to be construed as limiting the invention.
Throughout the specification, unless otherwise specifically noted, terms used herein should be understood as having meanings as commonly used in the art. Accordingly, unless defined otherwise, all technical and scientific terms used herein have the same meaning as commonly understood by one of ordinary skill in the art to which this invention belongs. If there is a conflict, the present specification will control.
Unless otherwise specifically stated, various raw materials, reagents, instruments, equipment and the like used in the present invention are commercially available or can be prepared by existing methods.
In order to solve the technical problems, the embodiment of the invention provides the following general ideas:
the inventor repeatedly improves the chemical components and the preparation process of the steel plate, so that the microstructure of the steel plate is changed, and specifically, the microstructure comprises 50-75% of ferrite, 20-40% of bainite + martensite and 3-8% of retained austenite in terms of area ratio, wherein the retained austenite at the ferrite grain boundary accounts for more than 90% of the total amount of the retained austenite. By passingInnovative components and process design thought, the elongation after fracture (A) of 590 MPa-grade steel plate80) The alloy reaches 30 percent or more, is obviously higher than the traditional dual-phase steel at the same level, solves the problem of difficult forming of the dual-phase steel on a complex stamping structural part, and achieves the technical effect of reducing the alloy cost.
Firstly, the low-cost high-plasticity cold-rolled galvanized steel sheet comprises the following chemical components in percentage by mass: c: 0.10% -0.15%, Si: 0.3% -0.6%, Mn: 1.1% -1.7%, Al: 0.3 to 0.6 percent of the total weight of the alloy, less than or equal to 0.01 percent of P, less than or equal to 0.005 percent of S, and the balance of Fe and other impurities. Wherein, the content of impurity elements is limited as follows: cu is less than or equal to 0.01 percent, Ni is less than or equal to 0.01 percent, Mo is less than or equal to 0.003 percent, Nb is less than or equal to 0.003 percent, V is less than or equal to 0.005 percent, Ti is less than or equal to 0.005 percent, B is less than or equal to 0.0004 percent, and N is less than or equal to 0.008 percent.
The scope and reason for the chemical composition of the low-cost high-plasticity cold-rolled galvanized steel sheet according to the present invention will be described below.
C：0.10％～0.15％
C is a strong austenite stabilizing element, which can increase the residual fraction of austenite at room temperature to improve plasticity, and C, as a solid solution strengthening element, can also increase the hardness of martensite. In order to ensure the 590 MPa-level tensile strength and the elongation rate of the cold-rolled galvanized steel sheet of the invention exceeding 30 percent, the content of C needs to reach 0.10 percent; on the other hand, if the C content exceeds 0.15%, the tensile strength margin becomes too large, and the weldability is impaired. The content of C is preferably 0.12-0.15%.
Si：0.3％～0.6％
Si is important as a solid-solution strengthening element for securing the strength of the steel sheet. Meanwhile, Si can effectively inhibit precipitation of carbide, promote enrichment of C in austenite and contribute to stabilization of austenite. However, the Si content is too high, and the weldability and galvanized surface quality of the steel sheet deteriorate. Therefore, the Si is limited to the range of 0.3% to 0.6%, preferably 0.35% to 0.55%.
Mn：1.1％～1.7％
Mn is an important element for solid solution strengthening and austenite stabilization, and contributes to the improvement of the strength of the steel sheet and the content of residual austenite, and in order to obtain such an effect, the Mn content in the 590MPa grade dual-phase steel of the present invention needs to be 1.1% or more. However, when the Mn content exceeds 1.7%, the steel sheet is excessively high in strength and deteriorated in plasticity, and the alloy cost increases. The preferable Mn content is 1.3-1.6%.
Al：0.3％～0.6％
Similar to Si, Al can effectively inhibit the decomposition of residual austenite and the precipitation of carbide, and Al is adopted to replace partial Si, so that the surface quality of the galvanized steel sheet can be effectively improved, and the addition amount of Al is not less than 0.3 percent considering the C content of the steel sheet. However, excessive addition of Al saturates the carbide precipitation suppressing effect and increases the material cost, so the upper limit of the Al content is set at 0.6%. The Al content is preferably 0.4 to 0.6%.
P≤0.01％
P is likely to be segregated at grain boundaries to deteriorate the plasticity of the steel sheet, so that the P content is not more than 0.01%, but excessive P removal causes an increase in production cost, and therefore the P content is preferably 0.005% to 0.01%.
S≤0.005％
S is mainly bonded to Mn in steel to form coarse MnS inclusions, which deteriorate formability of steel sheet such as punching, and therefore, the S content is controlled to 0.005% or less, and is preferably 0.001% to 0.005% in order to avoid an increase in cost due to excessive S removal.
Cu≤0.01％，Ni≤0.01％，Mo≤0.003％，B≤0.0004％
Cu, Ni, Mo and B all improve hardenability, promote martensite formation, and improve the strength of the steel sheet. However, the content of these elements increases, and inevitably affects the plasticity of the steel sheet to some extent. More importantly, they are expensive alloying elements and must be limited from the viewpoint of material cost, so that the content of these elements, if any, is limited to 0.01% or less of Cu, 0.01% or less of Ni, 0.003% or less of Mo, and 0.0004% or less of B under the condition that the strength can be ensured by properly increasing the content of C and Mn.
Nb≤0.003％，V≤0.005％，Ti≤0.005％
Nb, V and Ti are easy to form carbonitrides and have the functions of grain refinement or precipitation strengthening. However, the addition of these elements and the formation of carbonitrides inevitably consume C in the steel, resulting in insufficient enrichment of C in austenite, and these microalloy elements are expensive, which undoubtedly increases the material cost. Therefore, these elements are not intentionally added in the present invention, and if they exist as impurity elements, the contents thereof are limited to Nb 0.003% or less, V0.005% or less, and Ti 0.005% or less.
N≤0.008％
N is inevitably present in the steel, and the content thereof is limited to 0.008% or less, preferably 0.005% or less, in order to reduce the adverse effect of N on the material properties.
Next, the scope and reason for defining the microstructure of the low-cost high-plasticity cold-rolled galvanized steel sheet according to the present invention will be described.
The low-cost high-plasticity cold-rolled galvanized steel sheet has the following metallographic structure in area percentage:
ferrite: 50 to 75 percent
Bainite + martensite: 20 to 40 percent
Retained austenite: 3 to 8 percent.
Wherein: the proportion of the retained austenite existing at the ferrite grain boundary to the total retained austenite is 90% or more.
Ferrite: 50 to 75 percent
Ferrite belongs to a soft phase structure, is generated in the heating, soaking and slow cooling processes of continuous annealing, and contributes to improving the plasticity of the steel plate. Meanwhile, the residual austenite is transformed into hard martensite during the deformation process, and the ferrite can also play a role in synergistic deformation. When the area ratio of ferrite in the structure is less than 50%, it is difficult to obtain excellent plasticity, and when the area ratio of ferrite exceeds 75%, the required strength cannot be secured. Therefore, the ferrite area ratio is set to be 50% to 75%.
Bainite + martensite: 20 to 40 percent
In the present invention, a part of bainite and martensite, both of which belong to hard phases, particularly martensite, are important constituent phases for securing a desired strength, are generated in the continuous annealing galvanization and the subsequent cooling process. When the total area ratio of both is less than 20%, the required strength cannot be secured, and when the total area ratio of both exceeds 40%, the desired plasticity and formability cannot be obtained. Therefore, the total area ratio of bainite and martensite is set to be 20% to 40%.
Retained austenite: 3 to 8 percent of
In the deformation process, the residual austenite is transformed into martensite, so that stress concentration can be relieved, and the plasticity of the material is improved. The presence of retained austenite is therefore clearly essential for high strength steel sheets with high plasticity requirements. In the present invention, the content of retained austenite is at least 3% or more in order to secure the plasticizing effect of the TRIP effect. However, if the content of retained austenite exceeds 10%, the stability is lowered, transformation is liable to occur at an early stage of deformation, and too high content of retained austenite increases crack sensitivity in flange forming. Therefore, the residual austenite content is limited to 3% to 8%, preferably 4% to 7%.
The ratio of the retained austenite at the ferrite grain boundary to the total retained austenite is 90% or more
Whether the residual austenite can generate the TRIP effect in the deformation process or not is closely related to the stability of the residual austenite. The residual austenite in the ferrite crystal grains is small in size, high in C, Mn enrichment degree and high in stability, and is not easy to change phase in the deformation process, so that the effect of improving the plasticity of the steel plate and further improving the stamping performance is lost. In contrast, the retained austenite stability at the ferrite grain boundary is moderate, and a positive TRIP effect can occur. Therefore, in order to obtain a good plasticizing effect, it is necessary to ensure that the proportion of the retained austenite present at the ferrite grain boundary to the total retained austenite is 90% or more.
Finally, the scope and reasons for the method of manufacturing the low-cost high-plasticity cold-rolled galvanized steel sheet according to the present invention will be described.
A preparation method of a low-cost high-plasticity cold-rolled galvanized steel sheet comprises the following steps:
(1) continuously casting molten steel into a plate blank, wherein the chemical composition of the molten steel is the same as that of the steel plate;
the process is not particularly limited as long as a desired slab is obtained.
(2) Hot rolling the plate blank to obtain a hot rolled plate with the thickness of 3.0-5.0 mm; the heating temperature of the plate blank is 1250-1300 ℃, the soaking is carried out for 30-100 min, the finishing temperature is controlled to be 860-900 ℃, and the plate blank is coiled at 640-680 ℃ after laminar cooling.
The finishing temperature is as follows: 860-900 DEG C
The steel plate has low alloy content, can adopt low finish rolling temperature, and in order to obtain fine hot rolling crystal grain size, the finish rolling temperature is not more than 900 ℃; the finishing temperature is lower than 860 ℃, the deformation resistance of the hot rolled plate is too large, and mixed crystals are easy to appear.
Coiling temperature: 640-680 DEG C
The problems of coil collapse and surface quality are easy to occur when the coiling temperature is too high; bainite and martensite are excessively generated due to too low coiling temperature, and the cold rolling difficulty is increased.
(3) Carrying out acid pickling on the hot rolled plate, and then carrying out cold rolling to obtain a cold-hardened steel plate with the thickness of 0.8-2.0 mm;
(4) carrying out surface hot galvanizing on the cold-hardened steel plate after continuous annealing; the open point of the continuous annealing furnace zone is controlled to be-30 ℃ to-10 ℃, the preheating temperature is 200 ℃ to 240 ℃, the heating temperature is 750 ℃ to 830 ℃, the soaking temperature is 750 ℃ to 830 ℃, the slow cooling temperature is 650 ℃ to 720 ℃, the flash cooling temperature is 450 ℃ to 470 ℃, the galvanizing temperature is 450 ℃ to 470 ℃, the finishing elongation of the steel plate is 0.2 percent to 0.5 percent, and the running speed of the steel plate in the furnace zone is 60m/min to 110 m/min.
Furnace area dew point: -30 ℃ to-10 DEG C
Inhibit the external oxidation of the strip steel and ensure the platability of the product.
Soaking temperature: 750-830 deg.C
Setting the soaking temperature of the continuous annealing process based on the alloy components of the steel plate and the temperature interval of the two-phase region, wherein when the soaking temperature is higher than 830 ℃, the proportion of ferrite in the two-phase region is reduced, the plasticity of the two-phase steel is influenced, and the energy consumption is increased; when the soaking temperature is lower than 750 ℃, the proportion of austenite is insufficient, bainite and martensite with expected proportion cannot be obtained in the subsequent cooling process, and the drought strength is insufficient.
Slow cooling temperature: 650-720 DEG C
The slow cooling temperature higher than 720 ℃ causes the ferrite proportion to be reduced, the average C, Mn content in austenite is reduced, the stability is reduced, and finally, stable residual austenite cannot be obtained; the slow cooling temperature lower than 650 ℃ causes the ferrite proportion to be too high, and the tensile strength of more than 590MPa cannot be ensured.
Running speed of the steel plate in the furnace zone: 60 m/min-110 m/min
The operation speed of the steel plate in the furnace zone can be controlled to adjust the soaking time of the strip steel in the high-temperature zone, if the operation speed is too high, the soaking time is too short, the recrystallization is insufficient, and a banded structure can be reserved; if the operation speed is too slow, the soaking time is too long, and crystal grains grow excessively, so that the final mechanical property is influenced.
Hereinafter, a low-cost high-plasticity cold-rolled galvanized steel sheet and a method for manufacturing the same according to the present application will be described in detail with reference to examples, comparative examples and experimental data.
Example 1
The low-cost high-plasticity cold-rolled galvanized steel sheet comprises the following chemical components in percentage by mass: c: 0.13%, Si: 0.42%, Mn: 1.58%, Al: 0.52%, P: 0.01%, S: 0.0038% and the balance of Fe and inevitable impurities, wherein the content of possible impurity elements is limited as follows: cu is less than or equal to 0.01 percent, Ni is less than or equal to 0.01 percent, Mo is less than or equal to 0.003 percent, Nb is less than or equal to 0.003 percent, V is less than or equal to 0.005 percent, Ti is less than or equal to 0.005 percent, B is less than or equal to 0.0004 percent, and N is less than or equal to 0.008 percent.
The preparation method of the low-cost high-plasticity cold-rolled galvanized steel sheet comprises the following steps:
s1: smelting and continuous casting
Smelting molten steel in a 220t converter according to the component proportion of the low-cost high-plasticity cold-rolled galvanized steel plate, and then casting the molten steel into a plate blank in a continuous casting mode;
s2: hot rolling
Heating the plate blank to 1260 ℃, soaking for 90min, wherein the finishing temperature is 880 ℃, and coiling at 660 ℃ after laminar cooling to obtain a hot rolled plate with the thickness of 3.0 mm;
s3: cold rolling
Pickling the hot rolled plate, and then cold rolling to obtain a cold-hardened steel plate with the thickness of 1.25 mm;
s4: continuous annealing hot galvanizing
And annealing and galvanizing the cold-hardened steel plate. The running speed of the steel plate in a furnace zone is 70m/min, the dew point of the furnace zone is-20 ℃, the preheating temperature is 220 ℃, the average temperature of an outlet of a heating section is 802 ℃, the average temperature of an outlet of a soaking section is 807 ℃, the average temperature of an outlet of a slow cooling section is 695 ℃, the average temperature of an outlet of a flash cooling section is 463 ℃, the galvanizing temperature is 460 ℃, the finishing elongation of the steel plate after galvanizing is 0.3%, and finally the cold-rolled galvanized steel plate with low cost and high plasticity is obtained.
Example 2
The low-cost high-plasticity cold-rolled galvanized steel sheet comprises the following chemical components in percentage by mass: c: 0.139%, Si: 0.40%, Mn: 1.52%, Al: 0.47%, P: 0.009%, S: 0.0035% and the balance of Fe and inevitable impurities, wherein the content of impurity elements possibly existing is limited as follows: cu is less than or equal to 0.01 percent, Ni is less than or equal to 0.01 percent, Mo is less than or equal to 0.003 percent, Nb is less than or equal to 0.003 percent, V is less than or equal to 0.005 percent, Ti is less than or equal to 0.005 percent, B is less than or equal to 0.0004 percent, and N is less than or equal to 0.008 percent.
The preparation method of the low-cost high-plasticity cold-rolled galvanized steel sheet comprises the following steps:
s1: smelting and continuous casting
Smelting molten steel in a 220t converter according to the component proportion of the low-cost high-plasticity cold-rolled galvanized steel plate, and then casting the molten steel into a plate blank in a continuous casting mode;
s2: hot rolling
Heating the plate blank to 1263 ℃, soaking for 90min, controlling the finishing rolling temperature to 878 ℃, and coiling at 678 ℃ after laminar cooling to obtain a hot rolled plate with the thickness of 5.0 mm;
s3: cold rolling
Pickling the hot rolled plate, and then cold rolling to obtain a cold-hardened steel plate with the thickness of 2.0 mm;
s4: continuous annealing hot galvanizing
And annealing and galvanizing the cold-hardened steel plate. The running speed of the steel plate in a furnace zone is 80m/min, the dew point of the furnace zone is-10 ℃, the preheating temperature is 220 ℃, the average temperature of the outlet of a heating section is 783 ℃, the average temperature of the outlet of a soaking section is 779 ℃, the average temperature of the outlet of a slow cooling section is 684 ℃, the average temperature of the outlet of a flash cooling section is 461 ℃, the galvanizing temperature is 460 ℃, the finishing elongation of the steel plate after galvanizing is 0.5%, and finally the cold-rolled galvanized steel plate with low cost and high plasticity is obtained.
Example 3
The low-cost high-plasticity cold-rolled galvanized steel sheet comprises the following chemical components in percentage by mass: c: 0.135%, Si: 0.43%, Mn: 1.6%, Al: 0.6%, P: 0.009%, S: 0.004%, and the balance of Fe and inevitable impurities, wherein the content of impurity elements possibly existing is limited as follows: cu is less than or equal to 0.01 percent, Ni is less than or equal to 0.01 percent, Mo is less than or equal to 0.003 percent, Nb is less than or equal to 0.003 percent, V is less than or equal to 0.005 percent, Ti is less than or equal to 0.005 percent, B is less than or equal to 0.0004 percent, and N is less than or equal to 0.008 percent.
The preparation method of the low-cost high-plasticity cold-rolled galvanized steel sheet comprises the following steps:
s1: smelting and continuous casting
Smelting molten steel in a 220t converter according to the component proportion of the low-cost high-plasticity cold-rolled galvanized steel plate, and then casting the molten steel into a plate blank in a continuous casting mode;
s2: hot rolling
Heating the plate blank to 1255 ℃, soaking for 100min, wherein the finish rolling temperature is 870 ℃, and coiling at 659 ℃ after laminar cooling to obtain a hot rolled plate with the thickness of 3.5 mm;
s3: cold rolling
Pickling the hot rolled plate, and then cold rolling to obtain a cold-hardened steel plate with the thickness of 1.5 mm;
s4: continuous annealing hot galvanizing
And annealing and galvanizing the cold-hardened steel plate. The running speed of the steel plate in a furnace zone is 95m/min, the dew point of the furnace zone is-10 ℃, the preheating temperature is 220 ℃, the average temperature of an outlet of a heating section is 764 ℃, the average temperature of an outlet of a soaking section is 768 ℃, the average temperature of an outlet of a slow cooling section is 671 ℃, the average temperature of an outlet of a flash cooling section is 459 ℃, the galvanizing temperature is 460 ℃, the finishing elongation of the steel plate after galvanizing is 0.4%, and finally the cold-rolled galvanized steel plate with low cost and high plasticity is obtained.
Example 4
The low-cost high-plasticity cold-rolled galvanized steel sheet comprises the following chemical components in percentage by mass: c: 0.142%, Si: 0.42%, Mn: 1.55%, Al: 0.5%, P: 0.01 percent of the total weight of the mixture,
s: 0.004%, and the balance of Fe and inevitable impurities, wherein the content of impurity elements possibly existing is limited as follows: cu is less than or equal to 0.01 percent, Ni is less than or equal to 0.01 percent, Mo is less than or equal to 0.003 percent, Nb is less than or equal to 0.003 percent, V is less than or equal to 0.005 percent, Ti is less than or equal to 0.005 percent, B is less than or equal to 0.0004 percent, and N is less than or equal to 0.008 percent.
The preparation method of the low-cost high-plasticity cold-rolled galvanized steel sheet comprises the following steps:
s1: smelting and continuous casting
Smelting molten steel in a 220t converter according to the component proportion of the low-cost high-plasticity cold-rolled galvanized steel plate, and then casting the molten steel into a plate blank in a continuous casting mode;
s2: hot rolling
Heating the plate blank to 1260 ℃, soaking for 90min, wherein the finishing temperature is 865 ℃, and coiling at 650 ℃ after laminar cooling to obtain a hot rolled plate with the thickness of 3.5 mm;
s3: cold rolling
Pickling the hot rolled plate, and then cold rolling to obtain a cold-hardened steel plate with the thickness of 1.5 mm;
s4: continuous annealing hot galvanizing
And annealing and galvanizing the cold-hardened steel plate. The running speed of the steel plate in a furnace zone is 85m/min, the dew point of the furnace zone is-20 ℃, the preheating temperature is 220 ℃, the average temperature of an outlet of a heating section is 781 ℃, the average temperature of an outlet of a soaking section is 783 ℃, the average temperature of an outlet of a slow cooling section is 691 ℃, the average temperature of an outlet of a flash cooling section is 464 ℃, the galvanizing temperature is 460 ℃, the finishing elongation of the steel plate after galvanizing is 0.4%, and finally the cold-rolled galvanized steel plate with low cost and high plasticity is obtained.
Comparative example 1
The chemical components of the comparative example 1 are as follows by mass percent: c: 0.07%, Si: 0.51%, Mn: 1.34%, Al: 0.52%, P: 0.01%, S: 0.0038% and the balance of Fe and inevitable impurities, wherein the content of possible impurity elements is limited as follows: cu is less than or equal to 0.01 percent, Ni is less than or equal to 0.01 percent, Mo is less than or equal to 0.003 percent, Nb is less than or equal to 0.003 percent, V is less than or equal to 0.005 percent, Ti is less than or equal to 0.005 percent, B is less than or equal to 0.0004 percent, and N is less than or equal to 0.008 percent.
The preparation method of comparative example 1 includes the following steps:
s1: smelting and continuous casting
Smelting the molten steel in a 220t converter according to the chemical component ratio, and then casting the molten steel into a plate blank in a continuous casting mode;
s2: hot rolling
Heating the plate blank to 1250 ℃, soaking for 90min, wherein the finishing temperature is 885 ℃, and coiling at 660 ℃ after laminar cooling to obtain a hot rolled plate with the thickness of 3.0 mm;
s3: cold rolling
Pickling the hot rolled plate, and then cold rolling to obtain a cold-hardened steel plate with the thickness of 1.25 mm;
s4: continuous annealing hot galvanizing
And annealing and galvanizing the cold-hardened steel plate. The running speed of the steel plate in a furnace zone is 70m/min, the dew point of the furnace zone is-20 ℃, the preheating temperature is 220 ℃, the average temperature of an outlet of a heating section is 800 ℃, the average temperature of an outlet of a soaking section is 804 ℃, the average temperature of an outlet of a slow cooling section is 699 ℃, the average temperature of an outlet of a flash cooling section is 459 ℃, the galvanizing temperature is 460 ℃, the finishing elongation of the steel plate after galvanizing is 0.3%, and finally the cold-rolled galvanized steel plate is obtained.
Comparative example 2
The chemical components of the comparative example 2 are as follows by mass percent: c: 0.141%, Si: 0.47%, Mn: 1.49%, Al: 0.51%, P: 0.008%, S: 0.004%, and the balance of Fe and inevitable impurities, wherein the content of impurity elements possibly existing is limited as follows: cu is less than or equal to 0.01 percent, Ni is less than or equal to 0.01 percent, Mo is less than or equal to 0.003 percent, Nb is less than or equal to 0.003 percent, V is less than or equal to 0.005 percent, Ti is less than or equal to 0.005 percent, B is less than or equal to 0.0004 percent, and N is less than or equal to 0.008 percent.
The preparation method of comparative example 2 includes the following steps:
s1: smelting and continuous casting
Smelting the molten steel in a 220t converter according to the chemical component ratio, and then casting the molten steel into a plate blank in a continuous casting mode;
s2: hot rolling
Heating the plate blank to 1250 ℃, soaking for 90min, wherein the finish rolling temperature is 870 ℃, and coiling at 665 ℃ after laminar cooling to obtain a hot rolled plate with the thickness of 3.0 mm;
s3: cold rolling
Pickling the hot rolled plate, and then cold rolling to obtain a cold-hardened steel plate with the thickness of 1.5 mm;
s4: continuous annealing hot galvanizing
And annealing and galvanizing the cold-hardened steel plate. The running speed of the steel plate in a furnace area is 85m/min, the dew point of the furnace area is-20 ℃, the preheating temperature is 220 ℃, the average temperature of an outlet of a heating section is 842 ℃, the average temperature of an outlet of a soaking section is 845 ℃, the average temperature of an outlet of a slow cooling section is 720 ℃, the average temperature of an outlet of a flash cooling section is 463 ℃, the galvanizing temperature is 460 ℃, the finishing elongation of the steel plate after galvanizing is 0.4%, and finally the cold-rolled galvanized steel plate is obtained.
Comparative example 3
The chemical components of the comparative example 3 are as follows by mass percent: c: 0.148%, Si: 0.55%, Mn: 1.53%, Al: 0.48%, P: 0.008%, S: 0.004%, and the balance of Fe and inevitable impurities, wherein the content of impurity elements possibly existing is limited as follows: cu is less than or equal to 0.01 percent, Ni is less than or equal to 0.01 percent, Mo is less than or equal to 0.003 percent, Nb is less than or equal to 0.003 percent, V is less than or equal to 0.005 percent, Ti is less than or equal to 0.005 percent, B is less than or equal to 0.0004 percent, and N is less than or equal to 0.008 percent.
The preparation method of comparative example 3 includes the following steps:
s1: smelting and continuous casting
Smelting the molten steel in a 220t converter according to the chemical component ratio, and then casting the molten steel into a plate blank in a continuous casting mode;
s2: hot rolling
Heating the plate blank to 1255 ℃, soaking for 90min, wherein the finishing temperature is 875 ℃, and coiling at 660 ℃ after laminar cooling to obtain a hot rolled plate with the thickness of 3.0 mm;
s3: cold rolling
Pickling the hot rolled plate, and then cold rolling to obtain a cold-hardened steel plate with the thickness of 1.5 mm;
s4: continuous annealing hot galvanizing
And annealing and galvanizing the cold-hardened steel plate. The running speed of the steel plate in a furnace zone is 90m/min, the dew point of the furnace zone is-20 ℃, the preheating temperature is 220 ℃, the average temperature of an outlet of a heating section is 801 ℃, the average temperature of an outlet of a soaking section is 804 ℃, the average temperature of an outlet of a slow cooling section is 630 ℃, the average temperature of an outlet of a flash cooling section is 456 ℃, the galvanizing temperature is 460 ℃, the finishing elongation of the steel plate after galvanizing is 0.4%, and finally the cold-rolled galvanized steel plate is obtained.
Table 1 annealing process parameters for each of the examples and comparative examples
TABLE 2 results of microstructure analysis of examples of the cold-rolled galvanized steel sheets of the present invention and comparative examples
The yield, tensile strength and elongation after fracture of each example and comparative example were measured by using a ZWICK/RoeII Z100 tensile tester in accordance with GB/T228.1-2010 standard, and the results are shown in Table 3.
TABLE 3 mechanical Properties of examples of cold-rolled galvanized steel sheets according to the invention and comparative examples
From examples 1 to 4, it can be seen that: by improving the components and the preparation process of the dual-phase steel, the yield strength is 386MPa to 401MPa, the tensile strength is 627MPa to 648MPa, and the elongation after fracture (A)80) Compared with the traditional galvanized DP590, the novel dual-phase steel with the elongation percentage of more than 30 percent is greatly improved and is obviously superior to the comparative example.
As can be seen from FIG. 1: the dual-phase steel structure contains a gray ferrite matrix, bright white martensite and a small amount of dark black bainite; FIG. 2 shows that the retained austenite (black lumps) is mostly distributed at the ferrite grain boundary and a small amount is distributed in the ferrite grain
Finally, it should also be noted that the terms "comprises," "comprising," or any other variation thereof, are intended to cover a non-exclusive inclusion, such that a process, method, article, or apparatus that comprises a list of elements does not include only those elements but may include other elements not expressly listed or inherent to such process, method, article, or apparatus.
While preferred embodiments of the present invention have been described, additional variations and modifications in those embodiments may occur to those skilled in the art once they learn of the basic inventive concepts. Therefore, it is intended that the appended claims be interpreted as including preferred embodiments and all such alterations and modifications as fall within the scope of the invention.
It will be apparent to those skilled in the art that various changes and modifications may be made in the present invention without departing from the spirit and scope of the invention. Thus, if such modifications and variations of the present invention fall within the scope of the claims of the present invention and their equivalents, the present invention is also intended to include such modifications and variations.
Claims (10)
1. A low-cost high-plasticity cold-rolled galvanized steel plate is characterized by comprising the following chemical components in percentage by mass:
c: 0.10% -0.15%, Si: 0.3% -0.6%, Mn: 1.1% -1.7%, Al: 0.3 to 0.6 percent of the total weight of the alloy, less than or equal to 0.01 percent of P, less than or equal to 0.005 percent of S, and the balance of Fe and inevitable impurities;
the metallographic structure of the steel sheet had the following composition in terms of area ratio:
ferrite: 50% -75%, bainite + martensite: 20% -40%, retained austenite: 3% -8%;
the proportion of the retained austenite existing in the ferrite grain boundary is more than or equal to 90 percent.
2. The low-cost high-plasticity cold-rolled galvanized steel sheet as claimed in claim 1, wherein the chemical components of the steel sheet have impurity contents meeting the following requirements in mass fraction:
Cu≤0.01％，Ni≤0.01％，Mo≤0.003％，Nb≤0.003％，V≤0.005％，Ti≤0.005％，B≤0.0004％，N≤0.008％。
3. the low-cost high-plasticity cold-rolled galvanized steel sheet according to claim 1, wherein the surface of the steel sheet is provided with a hot-dip galvanizing layer.
4. A method for manufacturing a low-cost high-plasticity cold-rolled galvanized steel sheet according to any one of claims 1 to 3, comprising:
continuously casting molten steel into a slab, wherein the chemical composition of the molten steel is the same as that of the steel plate according to claim 1 or 2;
carrying out hot rolling on the plate blank to obtain a hot rolled plate;
carrying out acid pickling on the hot rolled plate, and then carrying out cold rolling to obtain a cold-hardened steel plate;
and performing surface hot galvanizing on the cold-hardened steel plate after continuous annealing.
5. The method for preparing the low-cost high-plasticity cold-rolled galvanized steel sheet according to the claim 4, wherein the hot rolling process comprises the following steps: the heating temperature of the plate blank is 1250-1300 ℃, the soaking is carried out for 30-100 min, the finishing temperature is controlled to be 860-900 ℃, and the plate blank is coiled at 640-680 ℃ after laminar cooling.
6. The method for preparing the low-cost high-plasticity cold-rolled galvanized steel sheet according to claim 4, wherein the thickness of the hot-rolled steel sheet is 3.0-5.0 mm, and the thickness of the chilled steel sheet is 0.8-2.0 mm.
7. The method for preparing the low-cost high-plasticity cold-rolled galvanized steel sheet according to claim 4, wherein in the continuous annealing process, the preheating temperature is 200-240 ℃, the heating temperature is 750-830 ℃, the soaking temperature is 750-830 ℃, the slow cooling temperature is 650-720 ℃, and the flash cooling temperature is 450-470 ℃.
8. The method for preparing the low-cost high-plasticity cold-rolled galvanized steel sheet according to claim 4, wherein in the hot galvanizing process, the galvanizing temperature is 450-470 ℃, and the finishing elongation of the steel sheet is 0.2-0.5%.
9. The method for preparing the low-cost high-plasticity cold-rolled galvanized steel sheet according to the claim 4, wherein in the continuous annealing process, the running speed of the steel sheet in a furnace zone is 60-110 m/min.
10. The method for preparing a low-cost high-plasticity cold-rolled galvanized steel sheet according to claim 4, wherein the dew point in the continuous annealing process is controlled to be-30 ℃ to-10 ℃.
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