CN108396237B - High-plasticity cold-rolled sheet and production method thereof - Google Patents
High-plasticity cold-rolled sheet and production method thereof Download PDFInfo
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- C21D2211/00—Microstructure comprising significant phases
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- C21D2211/00—Microstructure comprising significant phases
- C21D2211/002—Bainite
Abstract
The invention provides a high-plasticity cold-rolled sheet and a production method thereof, and the high-plasticity cold-rolled sheet comprises the following chemical components: 0.10-0.60% of C, 0.50-3.5% of Si, 1.50-3.50% of Mn, less than or equal to 0.020% of P, less than or equal to 0.010% of S, 0.02-3.00% of Al, less than or equal to 0.50% of Cr, less than or equal to 3.00% of Ni, less than or equal to 0.50% of Cu, less than or equal to 1.50% of Mo, less than or equal to 0.50% of V, less than or equal to 0.20% of Ti, and. And in the hot rolling process, the coiling temperature is controlled in a bainite transformation temperature interval to obtain a metallographic structure taking lath bainite as a main body, the steel plate after cold rolling is heated to an austenite temperature region in a continuous annealing production line and then is subjected to heat preservation for a period of time, then bainite isothermal quenching is carried out to obtain the steel plate taking the lath bainite and residual austenite as main structures, and then carbon distribution treatment is carried out. The steel has a metallographic structure with residual austenite uniformly distributed in a fine-grained bainite matrix, and has excellent plasticity, welding performance, forming performance, hole expansion performance and flange extending performance.
Description
Technical Field
The invention belongs to the technical field of cold-rolled steel plate manufacturing, and particularly relates to a high-strength and high-plasticity cold-rolled plate obtained by bainite transformation and a production method thereof.
Background
In order to improve the utilization efficiency of steel materials and save energy and resource consumption of the steel materials in the production, manufacture and use processes, researchers in various countries have developed various high-strength steel materials with excellent comprehensive performance in recent decades, wherein the high-strength steel materials are typified by dual-phase steel, TRIP steel, TWIP steel, martensite steel, bainite steel, complex phase steel, hot forming steel, Q & P steel, and the like. Compared with the common high-strength steel, the AHSS steel has the advantages of good formability, high energy absorption rate, good anti-collision concave performance, high baking hardening performance, high yield strength, high work hardening rate, good fatigue performance and the like, and shows good application prospects in automobile, machinery manufacturing, buildings and the like.
However, the plasticity of the existing steel is not required to be considered except for martensitic steel, and other steel types obtain better plasticity through two modes except that the hot-press forming steel obtains an all-martensitic structure after forming and has no plasticity: good matching of plasticity and strength is obtained through combination of soft phase with good plasticity and hard phase with poor plasticity, and the steel comprises dual-phase steel, bainite steel, complex phase steel and the like; the deformation induced plasticity of the retained austenite improves the overall deformability of the steel, while a combination of soft and hard phases also exists in the steel, including TRIP steels, TWIP steels, Q & P steels, etc.
Although a good plasticity can be obtained by combining the soft phase and the hard phase, the interface of the two phases (ferrite + martensite) having a large difference in deformability is likely to crack at the open hole portion during the forming process, the stretch flange formability is not good enough, and particularly after flash welding, the martensite phase is likely to be tempered and softened in the Heat Affected Zone (HAZ) and the fatigue strength is low.
The existing bainite steel plate production patents such as application numbers 201010283882.9, 201110383478.3, 201210195411.1 and 201210268312.1 are mainly directed to the production of hot rolled steel plates. 201010283882.9 discloses a high-elongation high-strength low-carbon bainite steel plate and its production method, the chemical components of which are C0.06-0.18%, Si 0.55-1.70%, Mn1.1-1.7, and also contains some Nb, V, Ti, Cr, Ni, Mo, Cu, etc., the process is hot rolling controlled rolling and controlled cooling, and some heat treatments are carried out subsequently; the structure is bainite, martensite and retained austenite. 201110383478.3 provides an ultra low carbon bainite steel plate and its manufacturing method, the chemical composition is C less than or equal to 0.03%, Si less than or equal to 0.15%, Mn1.2-1.6%, and also contains some Nb, V, Ti, Cu, Ni, B, etc., the ultra low carbon bainite steel plate is obtained by controlled rolling and controlled cooling, and the tempering treatment is carried out at 500-. 201210195411.1 discloses an ultra low carbon bainite steel plate and its manufacturing method, which is similar to 201110383478.3 except that the content of C is slightly high, the content of Mn is 3.0-4.5% high, and the steel plate does not contain noble elements such as Cu and Ni. 201210268312.1 provides a boron-containing bainite steel plate and its manufacturing method, wherein the chemical composition is C0.20-0.35%, Si 0.6-1.6%, Mn 1.5-2.0%, in addition, Ti, B, Al and impurity elements, the structure is bainite, the product is hot rolled plate.
The prior publications are directed to the research results of hot-rolled steel plates in most cases, and there are few reports of cold-rolled high-strength bainite steel plates.
In order to improve the performance of the bainite steel and increase the deformability of the bainite structure, the invention enables the bainite lath to deform in the deformation process by improving the deformability of the bainite, thereby improving the coordination and cooperation among various crystal grains of the steel plate in the deformation process and greatly improving the deformability.
Disclosure of Invention
The invention aims to provide a cold-rolled bainite steel plate which can improve the mutual coordination and matching of various crystal grains in the deformation process of the steel plate and has excellent plasticity, hole expansion performance and extending and flanging performance and a production method thereof.
The technical solution adopted by the invention is as follows:
a high-plasticity cold-rolled sheet comprises the following chemical components in percentage by mass: 0.10 to 0.60 percent of C, 0.50 to 3.5 percent of Si, 1.50 to 3.50 percent of Mn, less than or equal to 0.020 percent of P, less than or equal to 0.010 percent of S, 0.02 to 3.00 percent of Al, less than or equal to 0.50 percent of Cr, less than or equal to 3.00 percent of Ni, less than or equal to 0.50 percent of Cu, less than or equal to 1.50 percent of Mo, less than or equal to 0.50 percent of V, less than or equal to 0.20 percent of Ti, less than or equal to 0.20 percent of;
the cold-rolled sheet metal phase structure is lath bainite and residual austenite, the residual austenite is uniformly distributed between the bainite laths and inside the bainite laths, the volume percentage of the bainite structure is 55-85%, and the volume percentage of the residual austenite is 15-45%.
A production method of a high-plasticity cold-rolled sheet comprises the steps of smelting, casting, hot rolling and pickling steel, controlling the hot rolling finishing temperature in an austenite region, controlling the cooling starting temperature in the austenite region, cooling to the bainite transformation temperature of the steel at the cooling speed more than 20 ℃/s after rolling, and then coiling, wherein the structure of a hot-rolled steel sheet is lath bainite and residual austenite; carrying out acid pickling and cold rolling on a steel plate, then carrying out continuous annealing, wherein the heating speed of a continuous annealing production line is more than or equal to 10 ℃/s, the heating temperature is 700-930 ℃, the heat preservation time is 10-60 s, then immediately carrying out quick cooling, the cooling speed of the quick cooling is more than or equal to 30 ℃/s, the quick cooling temperature is controlled in a bainite transformation area, carrying out heat preservation at the temperature for 20-300 s, then cooling to a temperature range of 300-400 ℃ to further complete C distribution, and finally cooling to room temperature.
The reasons for selecting the above features and their specific parameters are as follows:
and controlling the hot rolling finishing temperature in an austenite region, cooling to a bainite region at a speed of not less than 20 ℃/s, and coiling to ensure that a metallurgical structure of lath bainite and residual austenite is obtained.
The heating speed of the continuous annealing production line is not less than 10 ℃/s, the heating temperature is 700-930 ℃, the heat preservation time is 10-60 seconds, then the rapid cooling is carried out immediately, the rapid cooling speed is not less than 30 ℃/s, the rapid cooling temperature is controlled in a bainite transformation area, and then the temperature is preserved for 20-300 seconds at the temperature and then the temperature is slowly cooled to the room temperature. Heating to austenite region for heat preservation to obtain uniform austenite structure; the temperature is lower than 700 ℃, the steel plate can not be austenitized, and the temperature is higher than 930 ℃, so that austenite grains are coarsened, the strength of the steel plate is reduced, and the strip breakage in the furnace is easily caused; the quenching speed is lower than 30 ℃/s, and B + A tissues cannot be obtained; the reason why B + a is the main structure is that the distribution of C atoms from B to a can be achieved in the subsequent distribution process, a carbon-rich a is obtained, the quenching temperature is controlled in the bainite transformation temperature interval, the amount of a obtained by excessively low temperature is small, and the M structure is easily generated.
The content of C in the steel plate is controlled to be 0.10-0.60 percent, C can stabilize austenite, the strength of the steel plate is insufficient due to too low carbon content, sufficient C atoms are not enriched into the retained austenite in the distribution process, the stability of the obtained retained austenite is insufficient, and the forming performance and the welding performance are not good due to too high content.
The Si content is controlled to be 0.50-3.5%, the Si content is too low, the precipitation of cementite cannot be hindered, the effect of stabilizing austenite is achieved, the Si content is too high, the selective oxidation of the surface of the steel plate in the annealing process is caused, and the generated oxide influences the surface quality of the steel plate and the post-treatment process.
The content of Mn is controlled to be 1.50-3.50%, Mn is an austenite stabilizing element, the content of Mn is too low, the strength and the hardenability of steel are insufficient, the volume of austenite is increased possibly caused by too high content of Mn, and the band-shaped structure of steel with too high content of Mn is very serious, thus affecting the uniformity of performance.
P is less than or equal to 0.020 percent, the less P, the better P, and the more P, the better P, the more P, the.
The S is less than or equal to 0.010 percent, the less the S, the better, and the determination is carried out according to the steelmaking capacity and the economical efficiency.
Al is controlled to be 0.02-3.00 percent, Al has the function of Si, but the problems of steel making and continuous casting processes, such as oxide inclusion, water gap blockage and the like, are caused by the excessive content of Al.
Cr is less than or equal to 0.50 percent, a certain Cr content can be shifted to the right by a C curve, the critical cooling speed of quenching is reduced, but the content is too high, the hardenability is increased, and the reduction and even disappearance of the residual austenite amount after quenching are caused.
Ni is less than or equal to 3.00 percent, the comprehensive mechanical property of the steel can be improved by a certain nickel content, the stability of austenite is improved, and the cost is increased due to overhigh content.
Cu is less than or equal to 0.50 percent, and the Cu element is a strong austenite forming element and is not dissolved in cementite, so that the formation of the residual austenite is facilitated, the content of the residual austenite can be improved, the strength can be improved, and the corrosion resistance can be improved.
Mo is less than or equal to 1.50 percent, Mo is a ferrite forming element, the transformation starting temperature of bainite is reduced, the phase transformation of austenite to ferrite and pearlite is strongly delayed, and the cost is increased due to the excessively high content of Mo.
V is less than or equal to 0.50 percent, Ti is less than or equal to 0.20 percent, Nb is less than or equal to 0.20 percent, and the three elements have the function of precipitation strengthening, but the content is not suitable to be too high. One or two of them can be selected when the addition is actually required.
The invention has the beneficial effects that:
the steel plate produced by the method has the advantages of high strength and good hole expansion performance, and the process route of industrial production is effectively solved. The yield strength of the steel plate is more than 800MPa, the tensile strength is more than or equal to 1000MPa, the elongation is more than or equal to 25 percent, and the lambda is more than or equal to 40 percent.
Detailed Description
The chemical compositions of the steels of the examples are shown in Table 1, and the processing parameters and properties of the production processes of the examples are shown in Table 2.
TABLE 1 chemical composition in wt.% of steel
TABLE 2 Process parameters and Properties
Claims (2)
1. The high-plasticity cold-rolled sheet is characterized by comprising the following chemical components in percentage by mass: 0.10 to 0.44 percent of C, 0.50 to 3.5 percent of Si, 1.50 to 3.50 percent of Mn, less than or equal to 0.020 percent of P, less than or equal to 0.010 percent of S, 0.02 to 3.00 percent of Al, less than or equal to 0.50 percent of Cr, less than or equal to 3.00 percent of Ni, less than or equal to 0.50 percent of Cu, less than or equal to 1.50 percent of Mo, less than or equal to 0.50 percent of V, less than or equal to 0.20 percent of Ti, less than or equal to 0.20 percent of;
the cold-rolled sheet metal phase structure is lath bainite and residual austenite, the residual austenite is uniformly distributed between the bainite laths and inside the bainite laths, the volume percentage of the bainite structure is 55-85%, and the volume percentage of the residual austenite is 15-45%; the yield strength of the steel plate is more than 800MPa, the tensile strength is more than or equal to 1000MPa, the elongation is more than or equal to 25 percent, and the lambda is more than or equal to 40 percent.
2. A production method of the high-plasticity cold-rolled sheet according to claim 1, wherein the steel with the components is smelted, cast, hot-rolled and pickled, the hot-rolling finishing temperature is controlled in an austenite region, the cooling starting temperature is controlled in an austenite region, the cooling speed after rolling is more than 20 ℃/s, the steel is cooled to the bainite transformation temperature of the steel, and then the steel is coiled, and the structure of the hot-rolled steel sheet is lath bainite + residual austenite; carrying out acid pickling and cold rolling on a steel plate, then carrying out continuous annealing, wherein the heating speed of a continuous annealing production line is more than or equal to 10 ℃/s, the heating temperature is 700-930 ℃, the heat preservation time is 10-60 s, then immediately carrying out quick cooling, the cooling speed of the quick cooling is more than or equal to 30 ℃/s, the quick cooling temperature is controlled in a bainite transformation area, carrying out heat preservation at the temperature for 20-300 s, then cooling to a temperature range of 300-400 ℃ to further complete C distribution, and finally cooling to room temperature.
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| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201710064848.4A CN108396237B (en) | 2017-02-05 | 2017-02-05 | High-plasticity cold-rolled sheet and production method thereof |
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|---|---|---|---|
| CN201710064848.4A CN108396237B (en) | 2017-02-05 | 2017-02-05 | High-plasticity cold-rolled sheet and production method thereof |
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| Publication Number | Publication Date |
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| CN108396237A CN108396237A (en) | 2018-08-14 |
| CN108396237B true CN108396237B (en) | 2020-01-07 |
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| CN108950406B (en) * | 2018-08-23 | 2019-12-27 | 东北大学 | 1000 MPa-grade low-manganese double-partition cold-rolled steel sheet and preparation method thereof |
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| CN110129670B (en) * | 2019-04-25 | 2020-12-15 | 首钢集团有限公司 | 1300 MPa-grade high-strength high-plasticity steel for hot stamping and preparation method thereof |
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| CN111945076B (en) * | 2020-09-09 | 2022-05-17 | 鞍钢股份有限公司 | 980 MPa-grade bainite-based Q & P steel for automobiles and production method thereof |
| CN112251668B (en) * | 2020-09-28 | 2022-02-18 | 首钢集团有限公司 | Forming reinforced complex phase steel and preparation method thereof |
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| CN113235005B (en) * | 2021-05-12 | 2021-12-21 | 江西耐普矿机股份有限公司 | Cast bainite steel for semi-autogenous mill, preparation method thereof and cast bainite steel lining plate for semi-autogenous mill |
| CN113462978B (en) * | 2021-06-30 | 2022-12-09 | 重庆长安汽车股份有限公司 | Ultrahigh-strength martensitic steel for automobile and rolling method |
| CN114959422A (en) * | 2022-06-06 | 2022-08-30 | 山东冀凯装备制造有限公司 | Preparation method of high-strength low-alloy bainite cast steel |
| CN115505691B (en) * | 2022-09-02 | 2023-12-19 | 中国机械总院集团北京机电研究所有限公司 | Medium-carbon low-alloy automobile brake drum and preparation method thereof |
Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101082100A (en) * | 2006-05-29 | 2007-12-05 | 株式会社神户制钢所 | Sheet made of a trip steel |
| CN101928875A (en) * | 2009-06-22 | 2010-12-29 | 鞍钢股份有限公司 | High-strength cold-rolled plate with favorable forming property and preparation method thereof |
| CN102325916A (en) * | 2008-12-24 | 2012-01-18 | Posco公司 | High-strength elongation steel sheet, hot-rolled steel sheet, cold-rolled steel sheet, zinc-coated steel sheet, and method for manufacturing alloyed zinc-coated steel sheet |
| CN103993243A (en) * | 2014-05-14 | 2014-08-20 | 东北大学 | Super-strength bainite steel plate and preparation method thereof |
Family Cites Families (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP4411221B2 (en) * | 2004-01-28 | 2010-02-10 | 株式会社神戸製鋼所 | Low yield ratio high-strength cold-rolled steel sheet and plated steel sheet excellent in elongation and stretch flangeability, and manufacturing method thereof |
| JP5780171B2 (en) * | 2012-02-09 | 2015-09-16 | 新日鐵住金株式会社 | High-strength cold-rolled steel sheet with excellent bendability, high-strength galvanized steel sheet, high-strength galvannealed steel sheet, and manufacturing method thereof |
-
2017
- 2017-02-05 CN CN201710064848.4A patent/CN108396237B/en active Active
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN101082100A (en) * | 2006-05-29 | 2007-12-05 | 株式会社神户制钢所 | Sheet made of a trip steel |
| CN102325916A (en) * | 2008-12-24 | 2012-01-18 | Posco公司 | High-strength elongation steel sheet, hot-rolled steel sheet, cold-rolled steel sheet, zinc-coated steel sheet, and method for manufacturing alloyed zinc-coated steel sheet |
| CN101928875A (en) * | 2009-06-22 | 2010-12-29 | 鞍钢股份有限公司 | High-strength cold-rolled plate with favorable forming property and preparation method thereof |
| CN103993243A (en) * | 2014-05-14 | 2014-08-20 | 东北大学 | Super-strength bainite steel plate and preparation method thereof |
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