CN110777297B - High-hole-expansibility high-drawability high-strength steel plate and manufacturing method thereof - Google Patents
High-hole-expansibility high-drawability high-strength steel plate and manufacturing method thereof Download PDFInfo
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
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- 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
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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
- 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
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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
- C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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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
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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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
- C22C38/10—Ferrous alloys, e.g. steel alloys containing cobalt
- C22C38/105—Ferrous alloys, e.g. steel alloys containing cobalt containing Co and Ni
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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
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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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
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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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
- C21D2211/001—Austenite
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/002—Bainite
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
Abstract
The invention discloses a high-hole expansibility high-drawability high-strength steel plate and a manufacturing method thereof, wherein the steel plate comprises the following chemical components in percentage by mass: c: 0.11 to 0.16%, Si: 0.83-0.99%, Mn: 1.81-1.99%, P: 0.013-0.017%, S is less than or equal to 0.008%, Al: 0.12-0.17%, Nb: 0.007-0.011%, Ti: 0.023-0.027%, V: 0.013-0.027%, Er: 0.02-0.05%, Ni: 0.21-0.27%, Co: 0.05 to 0.09 percent, and the balance of Fe and inevitable impurities; the manufacturing method comprises the working procedures of smelting, continuous casting, heating, hot rolling, cold rolling and annealing. The invention solves the problems of steel plate cracking caused by low hole expansion rate and stamping cracking caused by insufficient drawability in the stamping forming process of the traditional high-strength steel.
Description
Technical Field
The invention belongs to the technical field of metallurgy, and particularly relates to a high-drawability and high-strength steel plate with high hole expansibility and a manufacturing method thereof.
Background
With the continuous light weight of automobiles, the application proportion of high-strength steel is higher and higher, and for 980 MPa-grade advanced high-strength steel, the steel plate cracks when stamping parts due to the low hole expanding rate of the thin steel plate, and meanwhile, the drawing property is difficult to meet the stamping requirements of complex parts.
Regarding the research on the steel plate with high hole expansibility, high drawability and high strength, the invention patent of 'a 980MPa grade hot-rolled high strength and high hole expansibility steel and a manufacturing method thereof' with the application number of 201610450215.2 by Bao Steel Co., Ltd, which is disclosed by patent CN105925888A, the chemical components of the steel in percentage by mass (wt%) are: c: 0.20 to 0.30%, Si: 1.0-2.0%, Mn: 1.0-2.0%, P is less than or equal to 0.02%, S is less than or equal to 0.005%, O is less than or equal to 0.003%, Al: 0.5-1.0%, N is less than or equal to 0.006%, Nb: 0.01-0.06%, Ti: 0.08-0.20 percent of the total weight of the alloy, and the balance of Fe and inevitable impurities, wherein Nb and Ti are more than or equal to 0.10 percent and less than or equal to 0.25 percent, and Al/C is more than or equal to 2.5 and less than or equal to 5.0 percent. The high-strength high-hole-expansion steel has a structure comprising ferrite and bainite, wherein the ferrite accounts for 20-35% by volume, and the bainite accounts for 65-80% by volume. The material has yield strength of more than or equal to 700MPa, tensile strength of more than or equal to 980MPa, elongation of more than or equal to 15 percent and hole expansion rate of more than or equal to 40 percent. Such high yield strength requires higher strength for the corresponding forming die, which puts pressure on the cost of the die. The steel finished product is a hot rolled material, the thickness specification is 3-6 mm, and the steel plate with the thick specification is difficult to be applied to a car reinforcement to meet the requirement of light weight. In addition, the steel does not give a strain hardening index, namely an n value, and the n value of the steel is not higher than 0.15 as seen from a yield ratio, so that the drawing property of the steel cannot meet the stamping requirement of complex structural parts and reinforcements of automobiles. The invention patent of 980MPa low-carbon cold-rolled dual-phase steel and a preparation method thereof, which is disclosed by patent CN109280854A and is published by Panzhihua iron and Steel research institute Co., Ltd in application number 201811429155.1, the low-carbon cold-rolled dual-phase steel comprises the following chemical components in percentage by mass (wt%): c: 0.05-0.10%, Si: 0.30-0.70%, Mn: 2.0-2.5%, Cr: 0.40-0.80%, Al: 0.01-0.06%, V: 0.05-0.15%, P is less than or equal to 0.020%, S is less than or equal to 0.010%, and N is less than or equal to 0.006%. The microstructure is ferrite and martensite. The yield strength is 570-650 MPa, the tensile strength is 1000-1080 MPa, and the elongation is 10-15%. The finished product of the material is a cold rolled material, but the microstructure of the material can be obtained, the hole expansion rate of the material is difficult to meet the requirements of complex automobile parts, ferrite is mainly a soft phase, martensite is a hard phase, the hardness difference of the ferrite and the martensite is large, the two phases are difficult to cooperatively deform, so that the cracking phenomenon is caused in the punching process, in addition, the strain hardening index is not given, and the elongation rate given by the strain hardening index is not high, so that the material has insufficient ductility, and the complex punched parts are easy to crack.
Disclosure of Invention
The invention aims to provide a high-drawability and high-strength steel plate with high hole expansibility and a manufacturing method thereof. The steel plate has high strength, high hole expanding performance, high drawing performance, good coating and plating performance and corrosion resistance through reasonable chemical component design and production process control, can be used for manufacturing parts such as an A column reinforcing plate, a B column reinforcing plate, a seat mounting cross beam, an upper side beam reinforcing plate and the like of a car, and is an ideal material for middle-high automobile parts.
In order to solve the technical problems, the invention adopts the technical scheme that: the steel plate with high hole expansibility, high drawability and high strength comprises the following chemical components in percentage by mass: c: 0.11 to 0.16%, Si: 0.83-0.99%, Mn: 1.81-1.99%, P: 0.013-0.017%, S is less than or equal to 0.008%, Al: 0.12-0.17%, Nb: 0.007-0.011%, Ti: 0.023-0.027%, V: 0.013-0.027%, Er: 0.02-0.05%, Ni: 0.21 to 0.27%, Co: 0.05 to 0.09 percent, and the balance of Fe and inevitable impurities.
In order to ensure excellent comprehensive performance, the basic principle of limiting the content of each element is as follows:
c: it is possible to stabilize the austenite structure and to strengthen the matrix by solid solution hardening. The solid solubility of C in austenite is much higher than that in ferrite, and for this reason, the invention adopts a control scheme of medium C content. If the C content is too low, the strength of the steel is difficult to ensure; if the C content is too high, the plasticity and impact properties of the steel may be reduced.
Si: the method has the advantages that the formation of cementite is inhibited, the transfer of carbon in bainite to residual austenite is promoted, the residual austenite is stabilized, meanwhile, Si can play a role in solid solution strengthening, the strength of steel is improved, the effect cannot be achieved due to too low Si content, the Si content is too high, the surface quality of a material is poor, the edge crack phenomenon is easy to generate during steel hot rolling, and meanwhile, the Si promotes the material to have martensite phase change.
Mn: the austenite phase strengthening and toughening element is a conventional strengthening and toughening element, is used as an austenite forming element, enlarges an austenite region, reduces the finish rolling temperature, delays austenite transformation and can also play a role in stabilizing residual austenite. However, the content of Mn element is too high, on one hand, the cost is increased, and the crack sensitivity of a crack welding line and a heat affected zone is increased due to the hardened layer of the welding structure.
P: in the present invention, P has a similar action to Si, but too high a content affects the weldability.
S: the lower the content in the steel, the better, the adverse effect on the cracking and welding of the steel material of the present invention is avoided. In addition, the high sulfur content may consume too much manganese, affect the toughness of the material, or increase the cost of the material.
Al: the stacking fault energy of austenite is increased, martensite transformation is inhibited, and the effect similar to that of Si is achieved. The Al content is too high, the nozzle of a crystallizer in a steelmaking process can be seriously blocked during industrial production, and meanwhile, the Al content is too high, and the phenomenon of serious edge crack is generated due to the combined action of the Al content and Si element during hot rolling.
Nb, Ti and V are strong carbonitride forming elements, are beneficial to precipitation strengthening, can prevent high-temperature austenite from excessively growing, but are easy to cause partial aggregation of carbonitride due to excessively high content, and have poor processability, and meanwhile, the material cost is increased.
Er: in the invention, the coating performance of the substrate is enhanced and the formation of intermetallic compounds is avoided.
Ni and Co: in the invention, the effects of strengthening the obdurability and corrosion resistance of the steel are achieved.
The thickness of the steel plate is 0.6-2.5 mm, and the steel plate structure consists of 50-60% of low-carbon bainite, 30-40% of high-carbon ferrite and 5-15% of high-carbon retained austenite.
The steel plate has the advantages of 585-635 MPa of yield strength, 1050-1110 MPa of tensile strength, 17-21% of elongation and n value of strain hardening index: 0.15-0.20 percent, and the hole expanding rate is more than or equal to 50 percent.
The invention also provides a manufacturing method of the high-hole expansibility high-drawability high-strength steel plate, which comprises the working procedures of smelting, continuous casting, heating, hot rolling, cold rolling and annealing treatment; in the hot rolling procedure, the rough rolling temperature is controlled to be 1093-1113 ℃ during hot rolling, the final rolling temperature is controlled to be 877-887 ℃, 7-pass rolling is carried out on the blank in the hot rolling process, the plate thickness is controlled to be 2.5-5.5 mm, and the coiling temperature is controlled to be 566-589 ℃; the annealing treatment process adopts continuous annealing treatment, the soaking temperature is 803-815 ℃, and the cooling speed of a cooling section is 29-35 ℃/s.
According to the smelting process, the tapping finishing temperature of the smelted molten steel is controlled to 1651-1667 ℃, and the superheat degree of a subsequent tundish is conveniently controlled in a proper range.
The continuous casting process adopts argon protection for casting.
In the heating process, the heating temperature of the plate blank is controlled to be 1217-1229 ℃, and the heating time of the plate blank is controlled to be 167-195 min. The process parameter setting is beneficial to fully dissolving the micro-alloy elements in a solid way, and meets the performance index of the material.
In the hot rolling process, the single austenite zone rolling is realized at the final rolling temperature, so that mixed crystal tissues are avoided; the coiling temperature can realize the full precipitation of the compound and simultaneously ensure the proper grain size of the steel plate.
In the cold rolling process, the total cold rolling reduction is controlled to be 54.5-76%, and the thickness of the cold rolled plate is controlled to be 0.6-2.5 mm.
The annealing treatment process, the control of temperature and cooling rate can ensure the full precipitation of carbide and the formation of different microstructures with proper proportion, so as to realize the comprehensive mechanical property of the steel plate.
Adopt the produced beneficial effect of above-mentioned technical scheme to lie in: 1. the steel plate structure contains 50-60% of low-carbon bainite, 30-40% of high-carbon ferrite and 5-15% of high-carbon residual austenite, and the steel plate has excellent hole expansion performance and good formability and does not crack in the forming process; meanwhile, the retained austenite generates martensite phase transformation in the deformation process, so that the strength of the steel plate is further improved, the size of the deformed part is kept stable due to the release of bending deformation stress, the retained austenite can absorb the stress at the tip of a crack and relieve the formation and the expansion of the crack in the welding process, the crack and the crack are not generated in the welding process of the part, and the welding performance is good. 2. The steel plate has high strength, high hole expansibility and high drawability through reasonable chemical component design and production process control; meanwhile, because the element Er for avoiding the formation of intermetallic compounds is added in the chemical composition design and is supplemented with Nb and Ti, the effect of enhancing the coating performance of the substrate is achieved; in addition, Ni and Co elements are added, so that the corrosion resistance of the steel plate is enhanced. 3. The steel plate has the advantages of 585-635 MPa of yield strength, 1050-1110 MPa of tensile strength, 17-21% of elongation and n value of strain hardening index: 0.15-0.20, and the hole expansion rate is more than or equal to 50%, so that the problems of steel plate cracking caused by low hole expansion rate and stamping cracking caused by insufficient drawability in the stamping forming process of the traditional high-strength steel are solved, and the method has good market application prospect and remarkable social and economic benefits. 4. The steel plate has good coating and plating performance and corrosion resistance, can be used for manufacturing parts such as a column A reinforcing plate, a column B reinforcing plate, a seat mounting cross beam, a roof side rail reinforcing plate and the like of a car, and is an ideal material for middle and high-end automobile parts.
Drawings
FIG. 1 is a structural view of a metallographic microstructure of a deformed high-drawability high-strength steel sheet having a high hole expansibility according to example 1.
Detailed Description
The invention is described in further detail below with reference to the figures and specific examples.
Example 1
The thickness of the steel plate with high hole expansibility, high drawability and high strength of the embodiment is 1.0mm, and the chemical composition and the mass percentage of the steel plate are shown in table 1.
The manufacturing method of the high-hole expansibility, high-drawability and high-strength steel plate comprises the working procedures of smelting, continuous casting, heating, hot rolling, cold rolling and annealing treatment, and comprises the following specific process steps:
(1) smelting: controlling the tapping finishing temperature of the smelted molten steel at 1655 ℃;
(2) and (3) a continuous casting process: adopting argon protection for casting;
(3) a heating procedure: the heating temperature of the plate blank is controlled to be 1220 ℃, and the heating time of the plate blank is controlled to be 172 min;
(4) a hot rolling procedure: the rough rolling temperature is controlled to 1097 ℃ during hot rolling, the final rolling temperature is controlled to 880-880 ℃, 7-pass rolling is carried out on the blank in the hot rolling process, the plate thickness is controlled to 3.2mm, and the coiling temperature is controlled to 573 ℃;
(5) a cold rolling procedure: controlling the total rolling reduction rate of cold rolling to be 68.7 percent, and controlling the thickness of the cold-rolled plate to be 1.0 mm;
(6) an annealing treatment process: continuous annealing treatment is adopted, the soaking temperature is 805 ℃, and the cooling speed of a cooling section is 31 ℃/s.
The microstructure of the deformed high-ductility and high-strength steel plate with high hole expansibility of the embodiment is shown in figure 1 and consists of 52% of low-carbon bainite, 35% of high-carbon ferrite and 13% of high-carbon residual austenite; the steel sheet mechanical property indexes are shown in Table 2. (examples 2 to 8 are similar to FIG. 1 in the structure of the metallographic microstructure after deformation of the high-drawability high-strength steel sheet with high hole expansibility and are omitted.)
Example 2
The thickness of the steel plate with high hole expansibility, high drawability and high strength of the embodiment is 1.5mm, and the chemical composition and the mass percentage of the steel plate are shown in table 1.
The manufacturing method of the high-hole expansibility, high-drawability and high-strength steel plate comprises the working procedures of smelting, continuous casting, heating, hot rolling, cold rolling and annealing treatment, and comprises the following specific process steps:
(1) smelting: controlling the tapping finishing temperature of the smelted molten steel at 1662 ℃;
(2) and (3) continuous casting process: adopting argon protection for casting;
(3) a heating procedure: the heating temperature of the plate blank is controlled to be 1225 ℃, and the heating time of the plate blank is controlled to be 181 min;
(4) a hot rolling procedure: the rough rolling temperature is controlled at 1110 ℃ during hot rolling, the final rolling temperature is controlled at 883 ℃, 7-pass rolling is carried out on the blank in the hot rolling process, the plate thickness is controlled at 3.5mm, and the coiling temperature is controlled at 566-582 ℃;
(5) a cold rolling procedure: controlling the total rolling reduction rate of the cold rolling to be 57.1 percent, and controlling the thickness of the cold rolled plate to be 1.5 mm;
(6) an annealing treatment process: continuous annealing treatment is adopted, the soaking temperature is 808 ℃, and the cooling speed of the cooling section is 34 ℃/s.
The high-hole-expansibility, high-drawability, and high-strength steel plate structure of this example is composed of 55% of lower bainite, 37% of high-carbon ferrite, and 8% of high-carbon residual austenite; the steel sheet mechanical property indexes are shown in Table 2.
Example 3
The thickness of the steel plate with high hole expansibility, high drawability and high strength of the embodiment is 1.8mm, and the chemical composition and the mass percentage of the steel plate are shown in table 1.
The manufacturing method of the high-hole expansibility, high-drawability and high-strength steel plate comprises the working procedures of smelting, continuous casting, heating, hot rolling, cold rolling and annealing, and comprises the following specific process steps:
(1) a smelting process: the tapping finishing temperature of the smelting molten steel is controlled at 1660 ℃;
(2) and (3) continuous casting process: adopting argon protection for casting;
(3) a heating procedure: the heating temperature of the plate blank is controlled to be 1223 ℃, and the heating time of the plate blank is controlled to be 185 min;
(4) a hot rolling procedure: the rough rolling temperature is controlled at 1099 ℃ during hot rolling, the final rolling temperature is controlled at 885 ℃, 7 passes of rolling are carried out on the blank in the hot rolling process, the plate thickness is controlled at 4.0mm, and the coiling temperature is controlled at 585 ℃;
(5) a cold rolling procedure: controlling the total rolling reduction rate of the cold rolling to be 55 percent, and controlling the thickness of the cold rolled plate to be 1.8 mm;
(6) an annealing treatment process: continuous annealing treatment is adopted, the soaking temperature is 811 ℃, and the cooling speed of a cooling section is 35 ℃/s.
The high-hole-expansibility, high-drawability, and high-strength steel plate structure of this example is composed of 58% of lower bainite, 32% of high-carbon ferrite, and 10% of high-carbon residual austenite; the steel sheet mechanical property indexes are shown in Table 2.
Example 4
The thickness of the steel plate with high hole expansibility, high drawability and high strength of the embodiment is 2.0mm, and the chemical composition and the mass percentage of the steel plate are shown in table 1.
The manufacturing method of the high-hole expansibility, high-drawability and high-strength steel plate comprises the working procedures of smelting, continuous casting, heating, hot rolling, cold rolling and annealing, and comprises the following specific process steps:
(1) smelting: controlling the tapping finishing temperature of the smelted molten steel at 1665 ℃;
(2) and (3) continuous casting process: adopting argon protection for casting;
(3) a heating procedure: the heating temperature of the plate blank is controlled to be 1218 ℃, and the heating time of the plate blank is controlled to be 190 min;
(4) a hot rolling procedure: the rough rolling temperature is controlled to be 1112 ℃ during hot rolling, the final rolling temperature is controlled to be 878 ℃, 7-pass rolling is carried out on the blank in the hot rolling process, the plate thickness is controlled to be 4.7mm, and the coiling temperature is controlled to be 570 ℃;
(5) a cold rolling procedure: controlling the total rolling reduction rate of the cold rolling to be 57.4 percent, and controlling the thickness of the cold rolled plate to be 2.0 mm;
(6) an annealing treatment process: continuous annealing treatment is adopted, the soaking temperature is 809 ℃, and the cooling speed of the cooling section is 30 ℃/s.
The high-hole-expansibility, high-drawability, and high-strength steel plate structure of this example is composed of 54% of lower bainite, 37% of high-carbon ferrite, and 9% of high-carbon retained austenite; the steel sheet mechanical property indexes are shown in Table 2.
Example 5
The thickness of the steel plate with high hole expansibility, high drawability and high strength of the embodiment is 2.5mm, and the chemical composition and the mass percentage of the steel plate are shown in table 1.
The manufacturing method of the high-hole expansibility, high-drawability and high-strength steel plate comprises the working procedures of smelting, continuous casting, heating, hot rolling, cold rolling and annealing treatment, and comprises the following specific process steps:
(1) smelting: controlling the tapping finishing temperature of the smelted molten steel at 1658 ℃;
(2) and (3) continuous casting process: adopting argon protection for casting;
(3) a heating procedure: the heating temperature of the plate blank is controlled to be 1227 ℃, and the heating time of the plate blank is controlled to be 192 min;
(4) a hot rolling procedure: the rough rolling temperature is controlled to 1095 ℃ during hot rolling, the final rolling temperature is controlled to 882 ℃, the blank is rolled for 7 times in the hot rolling process, the plate thickness is controlled to 5.5mm, and the coiling temperature is controlled to 568 ℃;
(5) a cold rolling procedure: controlling the total rolling reduction rate of the cold rolling to be 54.5 percent, and controlling the thickness of the cold rolled plate to be 2.5 mm;
(6) an annealing treatment process: continuous annealing treatment is adopted, the soaking temperature is 803 ℃, and the cooling speed of a cooling section is 35 ℃/s.
The high-hole-expansibility, high-drawability, and high-strength steel plate structure of this example is composed of 60% of lower bainite, 30% of high carbon ferrite, and 10% of high carbon residual austenite; the mechanical property indexes of the steel plate are shown in a table 2.
Example 6
In the embodiment, the thickness of the steel plate with high hole expansibility, high drawability and high strength is 0.8mm, and the chemical composition and the mass percentage of the steel plate are shown in table 1.
The manufacturing method of the high-hole expansibility, high-drawability and high-strength steel plate comprises the working procedures of smelting, continuous casting, heating, hot rolling, cold rolling and annealing treatment, and comprises the following specific process steps:
(1) smelting: controlling the tapping finishing temperature of the smelted molten steel at 1664 ℃;
(2) and (3) continuous casting process: adopting argon protection for casting;
(3) a heating procedure: the heating temperature of the plate blank is controlled to be 1219 ℃, and the heating time of the plate blank is controlled to be 169 min;
(4) a hot rolling procedure: the rough rolling temperature is controlled to 1096 ℃ during hot rolling, the final rolling temperature is controlled to 879 ℃, 7-pass rolling is carried out on the blank in the hot rolling process, the plate thickness is controlled to 3.0mm, and the coiling temperature is controlled to 576 ℃;
(5) a cold rolling procedure: controlling the total rolling reduction rate of cold rolling to be 73.3 percent and controlling the thickness of the cold-rolled plate to be 0.8 mm;
(6) an annealing treatment process: continuous annealing treatment is adopted, the soaking temperature is 815 ℃, and the cooling speed of a cooling section is 30 ℃/s.
The high-hole-expansibility, high-drawability, and high-strength steel plate structure of this example is composed of 57% of lower bainite, 35% of high carbon ferrite, and 8% of high carbon residual austenite; the steel sheet mechanical property indexes are shown in Table 2.
Example 7
The thickness of the steel plate with high hole expansibility, high drawability and high strength of the embodiment is 0.6mm, and the chemical composition and the mass percentage of the steel plate are shown in table 1.
The manufacturing method of the high-hole expansibility, high-drawability and high-strength steel plate comprises the working procedures of smelting, continuous casting, heating, hot rolling, cold rolling and annealing treatment, and comprises the following specific process steps:
(1) smelting: controlling the tapping finishing temperature of the smelted molten steel at 1651 ℃;
(2) and (3) continuous casting process: adopting argon protection for casting;
(3) a heating procedure: the heating temperature of the plate blank is controlled to be 1229 ℃, and the heating time of the plate blank is controlled to be 167 min;
(4) a hot rolling procedure: the rough rolling temperature is controlled to be 1113 ℃ during hot rolling, the final rolling temperature is controlled to be 877 ℃, 7-pass rolling is carried out on the blank in the hot rolling process, the plate thickness is controlled to be 2.5mm, and the coiling temperature is controlled to be 589 ℃;
(5) a cold rolling procedure: controlling the total rolling reduction rate of cold rolling to be 76% and controlling the thickness of the cold-rolled plate to be 0.6 mm;
(6) an annealing treatment process: continuous annealing treatment is adopted, the soaking temperature is 815 ℃, and the cooling speed of a cooling section is 30 ℃/s.
The structure of the high-hole-expansibility, high-drawability and high-strength steel plate of this embodiment is composed of 50% of lower bainite, 35% of high carbon ferrite and 15% of high carbon residual austenite; the steel sheet mechanical property indexes are shown in Table 2.
Example 8
The thickness of the steel plate with high hole expansibility, high drawability and high strength of the embodiment is 0.6mm, and the chemical composition and the mass percentage of the steel plate are shown in table 1.
The manufacturing method of the high-hole expansibility, high-drawability and high-strength steel plate comprises the working procedures of smelting, continuous casting, heating, hot rolling, cold rolling and annealing treatment, and comprises the following specific process steps:
(1) smelting: controlling the tapping finishing temperature of the smelted molten steel at 1667 ℃;
(2) and (3) a continuous casting process: adopting argon protection for casting;
(3) a heating procedure: the heating temperature of the plate blank is controlled to be 1217 ℃, and the heating time of the plate blank is controlled to be 195 min;
(4) a hot rolling procedure: the rough rolling temperature is controlled at 1093 ℃ during hot rolling, the final rolling temperature is controlled at 887 ℃, 7 passes of rolling are carried out on the blank in the hot rolling process, the plate thickness is controlled at 2.5mm, and the coiling temperature is controlled at 566 ℃;
(5) a cold rolling procedure: controlling the total rolling reduction rate of cold rolling to be 76% and controlling the thickness of the cold-rolled plate to be 0.6 mm;
(6) an annealing treatment process: continuous annealing treatment is adopted, the soaking temperature is 805 ℃, and the cooling speed of a cooling section is 29 ℃/s.
The high-hole-expansibility, high-drawability, and high-strength steel plate structure of this example is composed of 55% of lower bainite, 40% of high-carbon ferrite, and 5% of high-carbon residual austenite; the steel sheet mechanical property indexes are shown in Table 2.
Table 1 examples 1-8 chemical composition of high hole expansibility, high drawability, and high strength steel plate
And mass percentage content (%)
The balance of the ingredients in table 1 is Fe and unavoidable impurities.
TABLE 2 examples 1-8 mechanical Properties of high-drawability high-strength steel sheets with high hole expansibility
Although the present invention has been described in detail with reference to the above embodiments, it should be understood by those skilled in the art that: modifications and equivalents may be made thereto without departing from the spirit and scope of the invention and it is intended to cover in the claims the invention as defined in the appended claims.
Claims (7)
1. The high-hole expansibility high-drawability high-strength steel plate is characterized by comprising the following chemical components in percentage by mass: c: 0.11 to 0.16%, Si: 0.83-0.99%, Mn: 1.81-1.99%, P: 0.013-0.017%, S is less than or equal to 0.008%, Al: 0.12-0.17%, Nb: 0.007-0.011%, Ti: 0.023-0.027%, V: 0.013-0.027%, Er: 0.02-0.05%, Ni: 0.21 to 0.27%, Co: 0.05 to 0.09 percent, and the balance of Fe and inevitable impurities;
the steel plate structure consists of 50-60% of low-carbon bainite, 30-40% of high-carbon ferrite and 5-15% of high-carbon residual austenite;
the steel plate has the yield strength of 585-635 MPa, the tensile strength of 1050-1110 MPa, the elongation of 17-21%, and the strain hardening index n value: 0.15-0.20 percent and the hole expansion rate is more than or equal to 50 percent;
a manufacturing method of a high-drawability high-strength steel plate with high hole expansibility comprises the working procedures of smelting, continuous casting, heating, hot rolling, cold rolling and annealing; in the hot rolling procedure, the rough rolling temperature is controlled to be 1093-1113 ℃ during hot rolling, the final rolling temperature is controlled to be 877-887 ℃, 7-pass rolling is carried out on the blank in the hot rolling process, the plate thickness is controlled to be 2.5-5.5 mm, and the coiling temperature is controlled to be 566-589 ℃; the annealing treatment process adopts continuous annealing treatment, the soaking temperature is 803-815 ℃, and the cooling speed of a cooling section is 29-35 ℃/s.
2. The high-stretch high-strength steel sheet with a high hole expansibility as recited in claim 1, wherein the steel sheet has a thickness of 0.6 to 2.5 mm.
3. The method for manufacturing a high-stretch high-strength steel sheet having a high hole expansibility according to claim 1 or 2, wherein the manufacturing method comprises the steps of smelting, continuous casting, heating, hot rolling, cold rolling, and annealing; in the hot rolling procedure, the rough rolling temperature is controlled to be 1093-1113 ℃ during hot rolling, the final rolling temperature is controlled to be 877-887 ℃, 7-pass rolling is carried out on the blank in the hot rolling process, the plate thickness is controlled to be 2.5-5.5 mm, and the coiling temperature is controlled to be 566-589 ℃; the annealing treatment process adopts continuous annealing treatment, the soaking temperature is 803-815 ℃, and the cooling speed of a cooling section is 29-35 ℃/s.
4. The method for manufacturing a high-stretch high-strength steel sheet with a high hole expansibility as recited in claim 3, wherein the steel tapping completion temperature of the molten steel is 1651-1667 ℃.
5. The method for manufacturing a high-drawability high-strength steel sheet according to claim 3, wherein the continuous casting step is performed under argon atmosphere.
6. The method for manufacturing a high-stretch steel sheet having a high hole expansibility according to any of claims 3 to 5, wherein in the heating step, the slab heating temperature is controlled to 1217 to 1229 ℃, and the slab heating time is controlled to 167 to 195 min.
7. The method for producing a high-drawability high-strength steel sheet as claimed in any one of claims 3 to 5, wherein the cold rolling step is performed so that the total reduction rate of cold rolling is controlled to 54.5 to 76% and the thickness of the cold rolled sheet is controlled to 0.6 to 2.5 mm.
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