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CN116043133B - Ultra-high forming 980 MPa-grade hot dip galvanized complex phase steel and preparation method thereof - Google Patents

Ultra-high forming 980 MPa-grade hot dip galvanized complex phase steel and preparation method thereof Download PDF

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Publication number
CN116043133B
CN116043133B CN202310062456.XA CN202310062456A CN116043133B CN 116043133 B CN116043133 B CN 116043133B CN 202310062456 A CN202310062456 A CN 202310062456A CN 116043133 B CN116043133 B CN 116043133B
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steel plate
percent
content
steel
mpa
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CN116043133A (en
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胡智评
顾兴利
刘仁东
林利
李侠
郭金宇
林春青
蒋睿婷
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Angang 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
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0236—Cold rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/04—Making ferrous alloys by melting
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
    • C23C2/06—Zinc or cadmium or alloys based thereon
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/34—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
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—Bainite
    • 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
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/009—Pearlite
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y02—TECHNOLOGIES OR APPLICATIONS FOR MITIGATION OR ADAPTATION AGAINST CLIMATE CHANGE
    • Y02P—CLIMATE CHANGE MITIGATION TECHNOLOGIES IN THE PRODUCTION OR PROCESSING OF GOODS
    • Y02P10/00—Technologies related to metal processing
    • Y02P10/20—Recycling

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Chemical Kinetics & Catalysis (AREA)
  • Heat Treatment Of Sheet Steel (AREA)

Abstract

The invention relates to ultra-high forming 980 MPa-level hot dip galvanized complex phase steel and a preparation method thereof, wherein the steel comprises the following chemical components: 0.18 to 0.24 percent of Mn:1.60 to 2.30 percent, cr:0.40 to 0.80 percent, mo:0.20 to 0.80 percent, si:0.2 to 0.8 percent of Al:0.05 to 0.80 percent; mn is more than or equal to 3Cr is more than or equal to 4Mo, and Si/Al is more than or equal to 1.0; ti:0.01% -0.03%, nb:0.02% -0.04%, B:2ppm to 5ppm, P is less than or equal to 0.015 percent, S is less than or equal to 0.005 percent, and the balance is Fe and impurities. Through chemical components and process system design, the produced hot dip galvanized composite steel plate has excellent flanging (reaming) performance and plasticity, can better meet the requirements of manufacturing new energy automobiles, and widens the application range of the composite steel.

Description

Ultra-high forming 980 MPa-grade hot dip galvanized complex phase steel and preparation method thereof
Technical Field
The invention relates to the technical field of steel manufacturing for automobiles, in particular to ultra-high forming 980 MPa-level hot dip galvanized complex phase steel for new energy automobiles and a preparation method thereof.
Background
With the longitudinal extension of energy conservation and emission reduction, "two carbons (carbon peak and carbon neutralization)" becomes a new challenge to be faced by the automobile industry. New energy automobiles have been put on the track of high-speed development, and whether the new energy automobiles are based on the existing or future battery technology, the weight and the energy consumption of the new energy automobiles are reduced. Therefore, automobile manufacturers have increased the proportion of high-strength steel in terms of component material selection. In the car body structure designed by the project of 'ultra-light steel car body-advanced car concept', the ratio of the high-strength steel with the tensile strength of more than 1000MPa is over 30 percent, and a huge high-strength steel market signal in the future is released. However, the application problem of high-strength steel is accompanied, and the contradiction between the strength and the plasticity determines that the high-strength steel can obtain the strength of more than 1000MPa and meanwhile has other properties such as plasticity, toughness, formability and the like.
Chinese patent application publication No. CN109576579 a discloses "980 MPa-grade cold-rolled steel sheet with high hole expansibility and higher elongation percentage and method for manufacturing the same". The annealing temperature is 820-870 ℃, the overaging temperature is 320-460 ℃, the overaging time is long (100-400 s), the hot dip galvanized product is not involved, and the structure is ferrite, bainite and martensite. The tensile strength of the steel plate obtained after heat treatment is greater than 980MPa, the yield strength is greater than 600MPa, the hole expansion rate is greater than or equal to 45%, and the elongation rate is greater than 11%.
The Chinese patent with the publication number of CN 109594020B discloses a cold-rolled complex phase steel with the tensile strength of 1000MPa and a manufacturing method thereof. The annealing temperature is 800-850 ℃, the overaging temperature is 300-340 ℃, the overaging time is long (300-600 s), the hot dip galvanized product is not involved, and the structure is ferrite, bainite and martensite. The tensile strength of the steel plate obtained after heat treatment is more than 1000MPa, the yield strength is more than 780MPa, the hole expansion rate is more than 50%, and the elongation rate is more than 8%.
The complex phase steel is typical high-strength steel for automobiles, and is suitable for manufacturing structures and reinforcing parts such as automobile seats, doorsills and the like by virtue of good flanging performance. With the continuous increase of the personalized demands of automobile users, the plasticity requirement on complex phase steel is gradually increased, so that the complex phase steel is hopeful to manufacture more automobile parts in the future. Therefore, the plasticity of the composite steel is improved on the basis of keeping the high flanging performance of the composite steel, and the composite steel is a new subject for the production and application of the composite steel in the future.
Disclosure of Invention
The invention provides a hot dip galvanized composite steel with ultra-high forming grade 980MPa and a preparation method thereof, and the produced hot dip galvanized composite steel plate has excellent flanging (reaming) performance and plasticity through chemical components and process system design, so that the hot dip galvanized composite steel plate can better meet the manufacturing requirements of new energy automobiles, and the application range of the composite steel is widened.
In order to achieve the above purpose, the invention is realized by adopting the following technical scheme:
the ultra-high forming 980 MPa-grade hot dip galvanized complex phase steel comprises the following chemical components in percentage by mass: 0.18 to 0.24 percent of Mn:1.60 to 2.30 percent, cr:0.40 to 0.80 percent, mo:0.20 to 0.80 percent, si:0.2 to 0.8 percent of Al:0.05 to 0.80 percent; mn is more than or equal to 3Cr is more than or equal to 4Mo, and Si/Al is more than or equal to 1.0; ti:0.01% -0.03%, nb:0.02% -0.04%, B:2ppm to 5ppm, P is less than or equal to 0.015 percent, S is less than or equal to 0.005 percent, and the balance is Fe and unavoidable impurities; the finished steel plate structure comprises ferrite F, bainite B, martensite M and retained austenite RA, wherein the ferrite F comprises ferrite IF in a critical zone and epitaxial ferrite EF; and according to the volume percentage, the F content is 30-50%, the IF content is 5-20%, the B content is 25-35%, the M content is 10-15%, and the RA content is 5-12%; in addition, the content of C in RA is 1.24-1.39%; the Ti precipitation size in the structure is 15-30 nm, and the Nb precipitation size is 20-40 nm.
Further, the tensile strength of the finished steel is over 980MPa, the yield strength is 700-850 MPa, the elongation is more than or equal to 20%, and the reaming ratio is more than or equal to 60%.
A preparation method of ultra-high forming 980 MPa-grade hot galvanizing complex phase steel comprises the procedures of continuous casting, hot rolling, acid washing, cold rolling and continuous annealing galvanization; the specific process is as follows:
1) Continuous casting; the casting blank pulling speed is less than or equal to 1.0m/min, and the tundish temperature is 1500-1600 ℃;
2) Hot rolling;
the heating temperature is controlled to 1180-1280 ℃; the initial rolling temperature is controlled at 1060-1180 ℃; the final rolling temperature is controlled between 850 and 950 ℃ and the coiling temperature is controlled between 450 and 490 ℃;
3) Acid washing;
4) Cold rolling; the cold rolling reduction is 40-58%;
5) Continuously annealing and galvanizing;
(1) heating: two-stage heating is adopted; heating the steel plate to 500-600 ℃ at a speed of more than 10 ℃/s in one stage, and heating the steel plate to 890-950 ℃ at a speed of 5-10 ℃/s in two stages;
(2) isothermal: isothermal temperature is 890-950 deg.c and isothermal time is 10-50 s;
(3) slowly cooling: the slow cooling temperature is 650-695 ℃, and the slow cooling speed is controlled to be 3-5 ℃/s;
(4) cooling the steel plate to 350-470 ℃ at a cooling rate of not less than 30 ℃/s;
(5) isothermal steel plate at 350-470 deg.c for 5-25 s and zinc pot;
(6) the steel plate is cooled to room temperature at a cooling speed of 2-5 ℃/s, then enters a finishing machine for plate shape adjustment, and the finishing elongation is controlled to be 0.1% -0.2%.
Further, in the continuous casting process, the thickness of the casting blank is 220-280 mm.
Further, in the hot rolling process, the thickness of the hot rolled steel plate is 2.2-4.0 mm; the hot rolled steel plate structure is ferrite, bainite and pearlite, wherein the ferrite content is 30-50%, the bainite content is 5-15%, the pearlite content is 40-50% and the rest is unidentified phase according to the volume percentage.
Further, in the continuous annealing galvanization process, the atmosphere in the annealing furnace is 5 to 10 percent of H 2 The balance being N 2 The method comprises the steps of carrying out a first treatment on the surface of the The Al content in the zinc pot is 0.15-0.18%; the dew point temperature is-10-0 ℃.
Further, in the step (2) of the continuous galvanizing process, the average austenite grain size in the isothermal stage is 2-2.5 μm.
Further, the continuous annealing galvanization process step (6) is replaced by an alloying galvanization process, specifically: the steel plate enters an alloying furnace after being taken out of the zinc pot, and the temperature of the steel plate entering the alloying furnace is 550-650 ℃; and then the steel plate enters a finishing machine to carry out plate shape adjustment, and the finishing elongation is controlled to be 0.1% -0.2%.
Compared with the prior art, the invention has the beneficial effects that:
(1) The ultra-high forming 980 MPa-grade hot dip galvanized composite steel is an industrial innovative product, and the produced hot dip galvanized composite steel plate has excellent flanging (reaming) performance and plasticity through chemical components and process system design, so that the requirements of manufacturing new energy automobiles can be better met, and the application range of the composite steel is widened;
(2) The alloy component design fully considers the matching and interaction among elements, such as C/Mn segregation, hot rolling temperature difference, cold rolling edge crack and the like, and breaks through the technical bottleneck of 980 MPa-grade hot dip galvanized composite steel industrial production;
(3) The product can meet the requirements of manufacturing more automobile parts by holding the design concept of thinning component, process, performance, coating and individuation requirement layer by layer.
Drawings
FIG. 1 is a typical SEM photograph of a steel sheet of the finished product prepared in example 1 of the present invention.
Detailed Description
The invention relates to ultra-high forming 980 MPa-grade hot dip galvanized complex phase steel, which comprises the following chemical components in percentage by mass: 0.18 to 0.24 percent of Mn:1.60 to 2.30 percent, cr:0.40 to 0.80 percent, mo:0.20 to 0.80 percent, si:0.2 to 0.8 percent of Al:0.05 to 0.80 percent; mn is more than or equal to 3Cr is more than or equal to 4Mo, and Si/Al is more than or equal to 1.0; ti:0.01% -0.03%, nb:0.02% -0.04%, B:2ppm to 5ppm, P is less than or equal to 0.015 percent, S is less than or equal to 0.005 percent, and the balance is Fe and unavoidable impurities; the finished steel plate structure comprises ferrite F, bainite B, martensite M and retained austenite RA, wherein the ferrite F comprises ferrite IF in a critical zone and epitaxial ferrite EF; and according to the volume percentage, the F content is 30-50%, the IF content is 5-20%, the B content is 25-35%, the M content is 10-15%, and the RA content is 5-12%; in addition, the content of C in RA is 1.24-1.39%; the Ti precipitation size in the structure is 15-30 nm, and the Nb precipitation size is 20-40 nm.
Further, the tensile strength of the finished steel is over 980MPa, the yield strength is 700-850 MPa, the elongation is more than or equal to 20%, and the reaming ratio is more than or equal to 60%.
The invention relates to a preparation method of ultra-high forming 980 MPa-grade hot galvanizing complex phase steel, which comprises the procedures of continuous casting, hot rolling, acid washing, cold rolling and continuous annealing galvanization; the specific process is as follows:
1) Continuous casting; the casting blank pulling speed is less than or equal to 1.0m/min, and the tundish temperature is 1500-1600 ℃;
2) Hot rolling;
the heating temperature is controlled to 1180-1280 ℃; the initial rolling temperature is controlled at 1060-1180 ℃; the final rolling temperature is controlled between 850 and 950 ℃ and the coiling temperature is controlled between 450 and 490 ℃;
6) Acid washing;
7) Cold rolling; the cold rolling reduction is 40-58%;
8) Continuously annealing and galvanizing;
(1) heating: two-stage heating is adopted; heating the steel plate to 500-600 ℃ at a speed of more than 10 ℃/s in one stage, and heating the steel plate to 890-950 ℃ at a speed of 5-10 ℃/s in two stages;
(2) isothermal: isothermal temperature is 890-950 deg.c and isothermal time is 10-50 s;
(3) slowly cooling: the slow cooling temperature is 650-695 ℃, and the slow cooling speed is controlled to be 3-5 ℃/s;
(4) cooling the steel plate to 350-470 ℃ at a cooling rate of not less than 30 ℃/s;
(5) isothermal steel plate at 350-470 deg.c for 5-25 s and zinc pot;
(6) the steel plate is cooled to room temperature at a cooling speed of 2-5 ℃/s, then enters a finishing machine for plate shape adjustment, and the finishing elongation is controlled to be 0.1% -0.2%.
Further, in the continuous casting process, the thickness of the casting blank is 220-280 mm.
Further, in the hot rolling process, the thickness of the hot rolled steel plate is 2.2-4.0 mm; the hot rolled steel plate structure is ferrite, bainite and pearlite, wherein the ferrite content is 30-50%, the bainite content is 5-15%, the pearlite content is 40-50% and the rest is unidentified phase according to the volume percentage.
Further, in the continuous annealing galvanization process, the atmosphere in the annealing furnace is 5 to 10 percent of H 2 The balance being N 2 The method comprises the steps of carrying out a first treatment on the surface of the The Al content in the zinc pot is 0.15-0.18%; the dew point temperature is-10-0 ℃.
Further, in the step (2) of the continuous galvanizing process, the average austenite grain size in the isothermal stage is 2-2.5 μm.
Further, the continuous annealing galvanization process step (6) is replaced by an alloying galvanization process, specifically: the steel plate enters an alloying furnace after being taken out of the zinc pot, and the temperature of the steel plate entering the alloying furnace is 550-650 ℃; and then the steel plate enters a finishing machine to carry out plate shape adjustment, and the finishing elongation is controlled to be 0.1% -0.2%.
The chemical composition design reason of the ultra-high forming 980 MPa-grade hot dip galvanized complex phase steel is as follows:
c: c is a necessary strengthening element in high-strength steel, and has the function of determining isothermal austenitizing state of a critical zone and simultaneously guaranteeing the strength of the steel plate. In the invention, C is not only critical to the strength, but also affects the plasticity of the steel plate; the content of residual austenite in steel and the content of C in the steel are directly influenced by the process adjustment C. The C content lower than the limit range of the invention can cause the steel plate to be unable to realize the strong plasticity, and the C content higher than the limit range of the invention can cause the C content in the residual austenite to be too high so as to influence the TRIP effect, and finally influence the plasticity of the steel plate.
Mn: mn is a strengthening element in high-strength steel, and has the functions of ensuring austenite stabilization in critical areas, ensuring critical cooling speed, preventing pearlite transformation, ensuring hardenability of the steel plate and further ensuring martensite content and strength. In the invention, the addition of Mn additionally considers the problem of C/Mn segregation, and prevents cold rolling cracking caused by the strength gradient of hot rolling 'in-edge'. Mn content is too low, and critical zone transition behavior cannot be guaranteed; too high Mn content may result in serious segregation, and the hot rolling process cannot be adjusted.
Cr: cr is a strengthening element in high-strength steel, and has the functions similar to Mn in promoting austenite stabilization in critical areas, ensuring critical cooling rate and preventing pearlite transformation; ensures the hardenability of the steel plate so as to promote the formation of martensite, and has obvious contribution to the strength. In the invention, the additional technical effect of adding Cr is to replace a part of Mn, thereby relieving the problem of C/Mn segregation, improving the strength gradient of 'middle-side-to-side', and reducing the risk of cold rolling cracking.
Mo: mo is a strengthening element in high-strength steel, and has similar actions to Mn and Cr, namely, the action of Mo is to promote austenite stabilization in critical areas, ensure critical cooling speed and prevent pearlite transformation; ensures the hardenability of the steel plate so as to promote the formation of martensite, and has obvious contribution to the strength. However, mo is costly, and in the present invention, as an auxiliary addition, the content is lower than the Cr element, and the Cr-rich carbide formation is prevented due to the excessive Cr content while the Mn and Cr functions.
Si: the Si element is a ferrite strengthening element, and serves to increase the strength of the steel sheet and suppress carbide precipitation. However, the excessive addition of Si element can cause the degradation of the surface quality of the steel plate, so that the phenomenon of plating omission occurs on the galvanized surface; meanwhile, the addition amount of Si needs to comprehensively consider the addition amount of Al, and a certain amount of Al is added on the premise of ensuring the surface quality of the steel plate, but the addition amount of Al is too high, so that the casting of steel is difficult due to water blocking, and the continuous casting billet longitudinal cracking phenomenon occurs.
Al: al is generally added as a deoxidizer to steel, and serves to promote ferrite formation and suppress carbide precipitation. In the invention, al is added in combination with Si to prevent the surface quality problem of the steel plate, but the content is not higher than Si, thereby ensuring the stability of continuous casting and preventing the phenomena of water gap blocking and continuous casting billet longitudinal cracking.
Ti: ti can capture free N atoms in steel, thereby playing a role of fixing N. Meanwhile, tiN can be separated out in the solidification process to play a role of pinning a grain boundary, and the pinning prior austenite grain boundary can refine prior austenite grains. Meanwhile, a small amount of Ti is precipitated in the continuous annealing stage, and can play a role in strengthening ferrite and bainite. However, adding too much Ti has limited effects and increases costs. Therefore, the Ti content is controlled to be 0.01% -0.03% in the invention.
Nb: nb element and C, N element can form Nb precipitation, so that the dragging effect and strain induction precipitation in the hot rolling stage are promoted, the prior austenite crystal grains are thinned by pinning crystal boundaries, and the final structure crystal grains are further thinned; the invention can accelerate bainite transformation, which is beneficial to improving the forming performance of the steel plate, so that the Nb content needs to be controlled in a proper range.
P: the P element is easy to combine with C in the high-strength steel to form unfavorable precipitated phase, and the lower the content is, the better the content is. The invention controls the P content below 0.015%.
S: the S element is easy to form MnS inclusion in the steel, and the lower the content is, the better the performance of the steel plate is deteriorated. The S content is controlled below 0.005%.
The invention relates to a preparation method of ultra-high forming 980 MPa-grade hot dip galvanized complex phase steel, which comprises a series of procedures of continuous casting, hot rolling, pickling, cold rolling, continuous deplating and the like. The method comprises the following specific steps:
1. continuous casting: the casting blank pulling speed is less than or equal to 1.0m/min, so that the cracking and the steel leakage of the casting blank are prevented, and the warning is performed; the temperature of the tundish is 1500-1600 ℃; the thickness of the casting blank is 220-280 mm, the rolling reduction of the hot rolling is ensured, and the size of the original austenite crystal grain is controlled below 10 mu m.
2. And (3) hot rolling:
(1) the heating temperature is controlled between 1180 and 1280 ℃, the precipitation behavior of Ti atoms is ensured, the precipitation of TiN or Ti (C, N) is formed and ensured, the effects of pinning the prior austenite grain boundary and refining the prior austenite grain are achieved, and the size of the prior austenite grain is further controlled below 10 mu m.
(2) The initial rolling temperature is controlled at 1060-1180 ℃, the rolling temperature of a recrystallization region is ensured, nb strain induced precipitation and dynamic recrystallization behavior of prior austenite grains in a hot rolling stage are promoted, the grains are refined, and the size of the prior austenite grains is ensured to be below 10 mu m.
(3) The final rolling temperature is controlled between 850 and 950 ℃, the dislocation state of the steel plate before laminar cooling is ensured, and the pre-eutectoid transformation of supercooled austenite is prevented.
(4) The coiling temperature is controlled at 450-490 ℃, the internal oxidation and the grain boundary oxidation of the steel plate are prevented, the surface quality of the steel plate is ensured, and the thickness of the hot rolled steel plate is 2.2-4.0 mm. The hot rolled steel plate structure is ferrite, bainite and pearlite, wherein the ferrite content is 30-50%, the bainite content is 5-15%, the pearlite content is 40-50%, and the rest is unidentified phase.
3. Acid washing: the method aims to remove the iron scale generated on the hot-rolled surface and ensure the surface quality of the cold-rolled steel plate.
4. Cold rolling: the cold rolling reduction rate is 40-58%, and the tissue fibrosis of the cold-rolled steel plate is promoted; meanwhile, the problem that deformation resistance is too large due to too high cold rolling reduction is prevented, and the rolling is difficult to achieve the target thickness.
5. Continuous annealing galvanization: the atmosphere in the annealing furnace is 5 to 10 percent of H 2 The balance being N 2 The method comprises the steps of carrying out a first treatment on the surface of the The Al content in the zinc pot is 0.15-0.18%; the dew point temperature is-10-0 ℃.
(1) Heating: two-stage heating, wherein the steel plate is heated to 500-600 ℃ at a speed of more than 10 ℃/s in one stage, so that the slow nucleation of austenite phase transformation caused by the recovery of excessive dislocation in the stage is prevented; the steel plate is heated to 890-950 ℃ at the speed of 5-10 ℃/s in two stages, so as to promote the austenitizing nucleation of the steel plate.
(2) Isothermal: isothermal temperature is set at 890-950 deg.c for 10-50 s to avoid ferrite formation in too low temperature to result in excessive critical area and austenite grain coarsening in the isothermal stage of average austenite grain size of 2-2.5 microns.
(3) Slowly cooling: the slow cooling temperature is 650-695 ℃, and the slow cooling speed is controlled to be 3-5 ℃/s; the content of epitaxial ferrite is controlled to be 25% -35%, and the performance of the steel plate is ensured; preventing excessive cold speed epitaxial ferrite formation from being inhibited and preventing too low temperature ferrite interface migration from being slow.
(4) Cooling the steel plate to 350-470 ℃ at a cooling rate of more than 30 ℃/s, wherein the aim of the high cooling rate is to prevent the formation of epitaxial ferrite, control the content of the epitaxial ferrite to be 25-35%, and ensure the performance of the steel plate; and at the same time, martensite is prevented from being formed due to the too low temperature, and pearlite is prevented from being formed due to the too high temperature.
(5) The steel plate enters a zinc pot after isothermal temperature is kept between 350 and 470 ℃ for 5 to 25 seconds, bainite is gradually formed in the stage, and the rest phase exists in a supercooled austenite phase, so that the volume content of the bainite is ensured to be 25 to 35 percent.
(6) Cooling the steel plate to room temperature at a cooling rate of 2-5 ℃/s, wherein carbide precipitation is caused by the excessively low cooling rate, and the martensite content is increased by the excessively high cooling rate; the content of martensite is controlled to be 10-15%. And then the steel plate enters a finishing machine for plate shape adjustment, the finishing elongation is controlled to be 0.1-0.2%, and the yield strength is regulated and controlled to be 700-850 MPa.
The (6) can be replaced by an alloying galvanization process, and the specific process is as follows: the steel plate enters an alloying furnace after being taken out of a zinc pot, the temperature of the steel plate entering the alloying furnace is 550-650 ℃, the formation of martensite with too low temperature is prevented, the formation of carbide with too high temperature is prevented, meanwhile, the diffusion of Zn-Fe is ensured, and the Fe content is 9.5-11%. And then the steel plate enters a finishing machine for plate shape adjustment, the finishing elongation is controlled to be 0.1-0.2%, and the yield strength is regulated and controlled to be 700-850 MPa.
In order to make the purposes, technical schemes and technical effects of the embodiments of the present invention more clear, the technical schemes in the embodiments of the present invention will now be clearly and completely described. The embodiments described below are only some, but not all, embodiments of the invention. All other embodiments, which can be made by those skilled in the art without the benefit of the teachings of this invention, are intended to be within the scope of the invention.
[ example ]
The chemical compositions of the example steels are shown in Table 1, the continuous casting and hot rolling process parameters of the example steels are shown in Table 2, the cold rolling and continuous annealing process parameters of the example steels are shown in Table 3, and the mechanical properties of the example steels are shown in Table 4. FIG. 1 is a typical SEM photograph of the steel sheet of the finished product produced in example 1.
Table 1 chemical composition of steel, wt%
Examples C Mn Cr Mo Si Al Ti Nb B P S
1 0.192 2.25 0.46 0.25 0.63 0.52 0.015 0.024 0.004 0.011 0.003
2 0.213 2.19 0.52 0.24 0.72 0.69 0.018 0.026 0.003 0.012 0.005
3 0.24 1.78 0.4 0.22 0.8 0.64 0.014 0.025 0.002 0.009 0.003
4 0.195 1.98 0.62 0.32 0.79 0.31 0.012 0.021 0.002 0.015 0.004
5 0.203 2.03 0.51 0.28 0.8 0.21 0.023 0.027 0.003 0.005 0.003
6 0.215 2.16 0.44 0.35 0.65 0.52 0.025 0.024 0.002 0.014 0.005
7 0.224 2.05 0.48 0.33 0.32 0.05 0.019 0.032 0.004 0.013 0.004
8 0.236 2.27 0.78 0.61 0.39 0.32 0.022 0.037 0.003 0.01 0.005
9 0.198 2.16 0.42 0.31 0.28 0.24 0.023 0.025 0.002 0.009 0.003
10 0.208 1.86 0.43 0.22 0.65 0.62 0.025 0.025 0.003 0.013 0.005
11 0.214 1.95 0.41 0.26 0.52 0.5 0.017 0.026 0.002 0.005 0.003
12 0.226 1.68 0.41 0.25 0.58 0.52 0.024 0.021 0.004 0.009 0.003
13 0.234 1.92 0.46 0.23 0.52 0.46 0.023 0.023 0.003 0.008 0.005
14 0.189 1.96 0.41 0.24 0.56 0.49 0.018 0.034 0.003 0.012 0.003
15 0.184 2.15 0.55 0.37 0.68 0.62 0.018 0.031 0.002 0.012 0.005
Table 2 continuous casting and hot rolling process parameters of steel
TABLE 3 continuous annealing process parameters (chronological order) for steels
Table 4 mechanical properties of steels
Examples F IF B M RA C/% Ti precipitation size/nm Nb precipitation size/nm Rp0.2/MPa Rm/MPa A80/％ λ/％
1 48.2 19.5 26.9 11.5 6.9 1.26 16.5 20.6 754 1088 20.6 63.6
2 47.5 17.7 31.2 12.9 7.8 1.29 28.4 39.5 724 1036 23.4 64.5
3 42.5 12.1 33.5 14.6 7.5 1.35 29.6 22.8 827 1052 26.8 63.8
4 39.6 5.8 29.8 12.4 11.4 1.38 15.8 28.4 756 1035 27.9 62.3
5 42.8 8.6 27.4 13.8 10.6 1.24 17.6 29.6 784 1026 26.2 61.4
6 36.4 7.5 29.5 12.4 11.8 1.39 22.5 25.8 793 1034 27.5 61.9
7 42.8 12 33.1 12.9 9.6 1.24 24.9 37.6 709 1019 26.5 62.2
8 42.4 10.6 31.6 12.8 9.4 1.26 26.4 22.5 736 1035 27.1 65.3
9 43.5 11.2 33.4 11.2 5.8 1.28 27.5 24.9 755 1026 26.5 62.7
10 33.9 5 32.5 10.4 6.2 1.31 18.6 26.4 724 1034 26.8 61.5
11 37.8 7.1 34.6 14.8 7.6 1.3 27.6 27.5 827 1054 20.6 63.5
12 39.6 6.1 33.5 11.2 7.5 1.35 22.9 38.6 756 1058 21.2 61.9
13 45.6 10.8 29.8 13.6 8.9 1.28 23.8 27.6 784 1086 21.8 67.3
14 42.3 9.7 25.9 13.2 9.4 1.27 28.2 37.6 783 1036 20.8 62.5
15 44.7 12.2 26.7 12.5 10.7 1.35 24.1 22.5 775 1052 21.1 61.5
In table 4, rp0.2 is the yield strength, rm is the tensile strength, a80 is the elongation, and λ is the hole expansion ratio.
The foregoing is only a preferred embodiment of the present invention, but the scope of the present invention is not limited thereto, and any person skilled in the art, who is within the scope of the present invention, should make equivalent substitutions or modifications according to the technical scheme of the present invention and the inventive concept thereof, and should be covered by the scope of the present invention.

Claims (6)

1. A preparation method of ultra-high forming 980 MPa-grade hot dip galvanized complex phase steel is characterized in that the steel comprises the following chemical components in percentage by mass: 0.18 to 0.24 percent of Mn:1.60 to 2.30 percent, cr:0.40 to 0.80 percent, mo:0.20 to 0.80 percent, si:0.2 to 0.8 percent of Al:0.05 to 0.80 percent; mn is more than or equal to 3Cr is more than or equal to 4Mo, and Si/Al is more than or equal to 1.0; ti:0.01% -0.03%, nb:0.02% -0.04%, B:2ppm to 5ppm, P is less than or equal to 0.015 percent, S is less than or equal to 0.005 percent, and the balance is Fe and unavoidable impurities; the finished steel plate structure comprises ferrite F, bainite B, martensite M and retained austenite RA, wherein the ferrite F comprises ferrite IF in a critical zone and epitaxial ferrite EF; and according to the volume percentage, the F content is 30-50%, the IF content is 5-20%, the B content is 25-35%, the M content is 10-15%, and the RA content is 5-12%; in addition, the content of C in RA is 1.24-1.39%; the Ti precipitation size in the structure is 15-30 nm, and the Nb precipitation size is 20-40 nm; the tensile strength of the finished steel is over 980MPa, the yield strength is 700-850 MPa, the elongation is more than or equal to 20%, and the reaming ratio is more than or equal to 60%;
the preparation method of the ultra-high forming 980 MPa-grade hot dip galvanized complex phase steel comprises the working procedures of continuous casting, hot rolling, acid washing, cold rolling and continuous annealing galvanization; the specific process is as follows:
1) Continuous casting; the casting blank pulling speed is less than or equal to 1.0m/min, and the tundish temperature is 1500-1600 ℃;
2) Hot rolling;
the heating temperature is controlled to 1180-1280 ℃; the initial rolling temperature is controlled at 1060-1180 ℃; the final rolling temperature is controlled between 850 and 950 ℃ and the coiling temperature is controlled between 450 and 490 ℃;
acid washing;
cold rolling; the cold rolling reduction is 40-58%;
continuously annealing and galvanizing;
(1) heating: two-stage heating is adopted; heating the steel plate to 500-600 ℃ at a speed of more than 10 ℃/s in one stage, and heating the steel plate to 890-950 ℃ at a speed of 5-10 ℃/s in two stages;
(2) isothermal: isothermal temperature is 890-950 deg.c and isothermal time is 10-50 s;
(3) slowly cooling: the slow cooling temperature is 650-695 ℃, and the slow cooling speed is controlled to be 3-5 ℃/s;
(4) cooling the steel plate to 350-470 ℃ at a cooling rate of not less than 30 ℃/s;
(5) isothermal steel plate at 350-470 deg.c for 5-25 s and zinc pot;
(6) the steel plate is cooled to room temperature at a cooling speed of 2-5 ℃/s, then enters a finishing machine for plate shape adjustment, and the finishing elongation is controlled to be 0.1% -0.2%.
2. The method for preparing the ultra-high forming 980 MPa-grade hot dip galvanized complex phase steel according to claim 1, wherein the thickness of a casting blank is 220-280 mm in the continuous casting process.
3. The method for preparing the ultra-high forming 980 MPa-grade hot-dip galvanized complex phase steel according to claim 1, wherein the thickness of the hot-rolled steel plate is 2.2-4.0 mm in the hot rolling process; the hot rolled steel plate structure is ferrite, bainite and pearlite, wherein the ferrite content is 30-50%, the bainite content is 5-15%, the pearlite content is 40-50% and the rest is unidentified phase according to the volume percentage.
4. The method for preparing the ultra-high forming 980 MPa-grade hot dip galvanized complex phase steel according to claim 1, wherein in the continuous annealing galvanization process, the annealing furnace atmosphere is 5-10% H 2 The balance being N 2 The method comprises the steps of carrying out a first treatment on the surface of the The Al content in the zinc pot is 0.15-0.18%; the dew point temperature is-10-0 ℃.
5. The method for preparing 980 MPa-grade hot-dip galvanized complex phase steel for ultra-high forming according to claim 1, wherein in the step (2) of the continuous annealing galvanization process, the austenite average grain size in the isothermal stage is 2-2.5 μm.
6. The method for preparing the ultra-high forming 980 MPa-grade hot dip galvanized complex phase steel according to claim 1, wherein the continuous annealing galvanization process step (6) is replaced by an alloying galvanization process, and specifically comprises: the steel plate enters an alloying furnace after being taken out of the zinc pot, and the temperature of the steel plate entering the alloying furnace is 550-650 ℃; and then the steel plate enters a finishing machine to carry out plate shape adjustment, and the finishing elongation is controlled to be 0.1% -0.2%.
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