CN111349771A - 980 MPa-grade cold-rolled Q & P steel with excellent plasticity and manufacturing method thereof - Google Patents
980 MPa-grade cold-rolled Q & P steel with excellent plasticity and manufacturing method thereof Download PDFInfo
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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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/18—Hardening; Quenching with or without subsequent tempering
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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
- C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
- C21D1/26—Methods of annealing
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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
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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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
- 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
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
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- 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
Abstract
The invention provides 980 MPa-grade cold-rolled Q & P steel with excellent plasticity and a manufacturing method thereof, and the steel comprises the following components: c: 0.18-0.21%, Si: 1.4-1.6%, Mn: 1.8-2.1%, Nb: 0.04-0.06%, Al: 0.02-0.05%, P is less than or equal to 0.01%, S is less than or equal to 0.01%, and the balance is Fe. Compared with the prior art, the invention does not add noble metal elements such as Al, Ni and Mo, the content of Mn is relatively low, the Mn element is mainly utilized to enrich and stabilize austenite in austenite, the plasticity of the material is obviously improved, and the product of strength and elongation can reach 25 GPa%; the two-phase zone annealing is adopted, the annealing temperature is low, and the quenching partition treatment by adopting an approximate one-step method can be implemented on the existing continuous annealing production line; on the other hand, the influence of the alloy element Mn on the material performance is improved through hot rolled coil annealing treatment, and the equipment does not need to be modified or input.
Description
Technical Field
The invention belongs to the technical field of material heat treatment, and particularly relates to 980 MPa-grade cold-rolled Q & P steel with excellent plasticity and a manufacturing method thereof.
Background
In order to meet the continuously tightening requirements of energy, environmental protection and safety regulations in the automobile industry, research and development work of third-generation automobile steel products with higher strength and better forming performance is developed in scientific research institutions and steel enterprises at home and abroad. Q & P (quench distribution) steels have been attracting attention as a representative of the third generation automotive steels due to their excellent ductility properties and the most commercial production possibilities.
The Q & P steel base process route is as follows: austenitizing is firstly carried out, the obtained high-Temperature austenite structure is rapidly cooled to a certain Temperature (QT) of Ms-Mf for Quenching, and part of austenite is transformed into martensite; and then heated to a certain dispensing Temperature (PT) for a certain period of time to dispense carbon. The temperature of the carbon distribution may be equal to or higher than the initial quench temperature. The Q & P process in which the temperature of carbon distribution is equal to the initial quenching temperature is referred to as a one-step (1-step) process, and the Q & P process in which the temperature of carbon distribution is higher than the initial quenching temperature is referred to as a two-step (2-step) process.
At present, Q & P steel production has two problems: firstly, the continuous annealing production line has high cooling speed according to the requirement of the traditional distribution process (namely, two-step distribution), and the conventional continuous annealing production line cannot realize the high cooling speed; secondly, if the quenching distribution treatment is carried out by a one-step method, the process adjustment needs to be carried out on the existing production line, the production process window is limited by continuous annealing production line equipment and materials, and the performance cannot reach the optimum. At present, the research on the one-step method for producing Q & P steel is only limited to the process improvement after continuous annealing treatment.
The patents with the application numbers of 201210092207.7 and 201210429983.1 both provide a production method of the ultra-high strength steel plate for cold forming, the production of the ultra-high strength steel plate is realized, and alloying elements such as Mo, Ni, V and the like are added to different degrees in the design of alloy components, so that the production cost is improved; patent publication No. CN110093552A proposes a method for producing 980MPa grade Q & P by using a conventional continuous annealing production line, but is limited to process adjustment in the continuous annealing production line, and because the residual content of the residual austenite which cannot be obtained by high-temperature distribution is less than that of the residual austenite obtained by two-step Q & P treatment, more excellent material plasticity cannot be obtained; the patent of publication No. CN102766818A is distributed at the quenching temperature, although the process operability is relatively strong, the alloy cost is high because relatively high noble metal elements Cr, Mo and the like are added; patents CN109988970A and CN109988969A propose cold rolled Q & P980/Q & P1180 steel with different yield ratios and a method for producing the same, but the Mn content is high, which deteriorates weldability; the patent publication No. CN103361547A discloses a method for producing an ultra-high strength steel sheet for cold forming and a steel sheet, which adopts a method of distributing and processing steel sheets in a continuous annealing line and a hood-type annealing furnace to obtain the ultra-high strength steel sheet, but the process needs higher cooling speed to obtain martensite structure, and is still the process improvement after the continuous annealing process; the Q & P steel manufacturing method provided by the patent with the publication numbers of CN110129680A and CN110055465A has the advantages that the content of Mn is high, and in addition, a light element Al is added, so that the smelting and casting difficulty is increased; the 1180 MPa-grade ultrahigh-strength low-cost cold-rolled quenching distribution steel and the manufacturing method thereof, which are disclosed in the patent publication No. CN110093564A, can realize one-step quenching distribution treatment, but the material is required to be heated to 880-920 ℃ and kept warm for 240-300 s for complete austenitization, and the maximum heating temperature of a conventional continuous annealing production line is only 850 ℃.
Therefore, the method has important significance in further optimizing the production process of the Q & P steel from the feasibility of the conventional continuous annealing production line process and more excellent obdurability.
Disclosure of Invention
The invention aims to provide 980MPa grade cold-rolled Q & P steel with excellent plasticity.
The invention also aims to provide a method for manufacturing 980MPa cold-rolled Q & P steel with excellent plasticity, ferrite and pearlite structures are obtained after a hot rolling process, then the steel enters a cover annealing furnace for annealing treatment (preferably by adopting a DDQ process), and the temperature is kept for 4h-5h (more preferably 5h), so that the alloy element Mn can be converted from a solid solution state to carbide to obtain a Mn-rich carbide structure, in the subsequent continuous annealing treatment process, the Mn-rich carbide forms Mn-rich austenite, the Mn element can play a role in stabilizing austenite, and through series Q & P treatment, more stable retained austenite is obtained, and the plasticity of the material is improved.
The specific technical scheme of the invention is as follows:
the invention provides a method for manufacturing 980 MPa-grade cold-rolled Q & P steel with excellent plasticity, which comprises the following process flows of:
molten iron pretreatment → converter smelting → alloy fine tuning station → LF furnace refining → RH vacuum degassing → continuous casting → hot rolling → leveling → hot rolled coil → cover annealing → acid pickling cold rolling → continuous annealing → finished product.
Further, smelting in a steel area by adopting a converter → an alloy fine-tuning station → LF furnace refining → RH vacuum degassing → continuous casting process;
the continuous casting production casting blank adopts a hot charging (hot peeling) process, and a dynamic soft reduction and electromagnetic stirring system is used for ensuring the quality of the casting blank;
the hot rolling is specifically as follows: the heating temperature of the casting blank is 1200-180 ℃, the temperature is kept for 2-3 hours, the casting blank is rolled for 5-7 times by a roughing mill, hot rolled to an intermediate blank of 30-50mm, the finish rolling is carried out for 7 times by a hot continuous rolling unit, and the final rolling temperature is 870-910 ℃;
rolling the hot plate to a target thickness, coiling the hot plate at the temperature of 630-670 ℃, air-cooling the hot plate to room temperature, and obtaining a final structure of the hot rolled coil which is ferrite plus pearlite or ferrite plus pearlite plus a small amount of bainite;
the cover annealing: feeding the hot rolled coil into a hood-type annealing furnace, adopting a DDQ hood annealing process, and cooling the hot rolled coil at the hot/cold point temperature of 710/680 ℃;
the method specifically comprises the following steps: annealing at 680-710 ℃ for 4-5h, and cooling by air and water.
Acid pickling and cold rolling: pickling the hot rolled strip steel subjected to cover annealing, removing surface iron oxide scales, and carrying out cold continuous rolling to a target thickness, wherein the cold rolling reduction rate is 50-65%;
and (3) continuous annealing:
and (3) continuous annealing: heating the steel plate treated in the acid-washing and cold-rolling step to 840-860 ℃ for two-phase region annealing, slowly cooling to 710-730 ℃, then rapidly cooling to 240-270 ℃ for quenching, and then heating to 290-350 ℃ for distribution.
Preferably, the continuous annealing: heating the steel plate treated in the acid-washing and cold-rolling step to 840-860 ℃, preserving heat for 90-170s, carrying out two-phase region annealing, slowly cooling to 710-730 ℃ at a cooling speed of 3-5 ℃/s to form a certain amount of ferrite for improving plasticity, then cooling to 240-270 ℃ at a cooling rate of more than or equal to 35 ℃/s, quenching, heating to 290-350 ℃ for distributing at 380-720s, then coiling and air cooling to room temperature to obtain the finished steel coil.
The 980MPa cold-rolled Q & P steel with excellent plasticity is manufactured by the method, and comprises the following chemical components in percentage by mass: c: 0.18-0.21%, Si: 1.4-1.6%, Mn: 1.8-2.1%, Nb: 0.04-0.06%, Al: 0.02-0.06%, P is less than or equal to 0.02%, S is less than or equal to 0.01%, and the balance is Fe.
C: the carbon content directly affects the martensite transformation point and the enrichment of carbon into austenite during heat treatment results in a decrease in the Ms point temperature. Carbon can stabilize austenite, the strength of the steel plate is insufficient due to the low carbon content, and sufficient C atoms are not enriched into the retained austenite in the distribution process, so that the stability of the obtained retained austenite is insufficient. However, since too high a carbon content is disadvantageous in formability and weldability, it is not generally preferable that the higher the carbon content is. In the present invention, the content of C is controlled to be in a lower range of 0.18 to 0.21%.
Si: ferrite forming elements which play a role in solid solution strengthening; can prevent cementite from being precipitated and play a role in stabilizing austenite; on the other hand, too high a silicon content causes selective oxidation of the surface of the steel sheet during annealing, and scales are generated during heating, and when scales are pressed into the surface of the sheet during hot rolling, the surface quality of the sheet is deteriorated, which causes difficulty in welding the material, difficulty in hot galvanizing, poor coating properties of the surface layer, and the like. Therefore, the weight percentage of Si in the invention is controlled as follows: 1.4-1.6%.
Mn: the strength of a ferrite matrix is improved through a solid solution strengthening effect, the temperature of Ac1 and Ac3 can be reduced by increasing the content of Mn element, and low-temperature critical zone annealing is realized; the other function of adding Mn element into the low-carbon steel is to shift the pro-eutectoid ferrite precipitation line to the right, so that the precipitation amount of ferrite in the annealing and cooling process is less to ensure the content of residual austenite in the final microstructure. Further, Mn has an effect of stabilizing austenite, and can form retained austenite having a high degree of stability. However, too high Mn content results in a severe band-shaped structure of the steel sheet, high cost and difficult working. Therefore, the Mn content of the invention is controlled to be 1.8-2.1% by weight.
Nb: the crystal grains are refined, and the strength and the plasticity are improved; the annealing austenite grains are refined, the Ms temperature is reduced, the adjustment of the overaging temperature of the existing continuous annealing line is facilitated, and the difference between the flash cooling temperature of the existing continuous annealing line and the overaging isothermal temperature cannot be too large. Meanwhile, the hot rolling structure is refined, which is beneficial to the diffusion of alloy elements during annealing. The invention designs Nb: 0.04-0.06%.
Al: during smelting, a small amount of aluminum is added to perform deoxidation, but excessive Al can block a nozzle during continuous casting and increase the difficulty of continuous casting, so that the content of Als is preferably controlled to be 0.02-0.06%.
P, S: the content of P, S in the steel is strictly controlled in order to reduce the adverse effect of harmful impurities in the steel on the punching properties of the steel.
The 980 MPa-grade cold-rolled Q & P steel with excellent plasticity finally obtains a structure with the ferrite content of 40-50%, the residual austenite content of 12-14% and the balance of martensite or martensite and a small amount of bainite.
The 980 MPa-grade cold-rolled Q & P steel with excellent plasticity has the yield strength of more than or equal to 650MPa, the tensile strength of more than or equal to 980MPa and the product of strength and elongation of more than or equal to 25 GPa%.
Compared with the prior art, in the aspect of components, precious metal elements such as Al, Ni and Mo are not added, the content of Mn is relatively low, a cover annealing process is mainly added after hot rolling, and according to the thermodynamic equilibrium principle, the content of Mn in cementite is inevitably far greater than that in ferrite, so that Mn is led to be inward from ferrite crystals to grain boundary Fe during hot rolling and coiling3C is diffused, so that the Mn element is favorably enriched in stable austenite in the subsequent cold rolling and annealing process, the content of the residual austenite is increased to 12-14% from 8-10% of the original process, the plasticity of the material is obviously improved, and the product of strength and elongation can reach 25 GPa%; in the aspect of process, the invention adopts two-phase zone annealing, the annealing temperature is lower, and the quenching proportioning is similar to a one-step method (a small amount of temperature rise)The treatment can be implemented on the existing continuous annealing production line; on the other hand, the influence of the alloy element Mn on the material performance is improved through hot rolled coil annealing treatment, and the equipment does not need to be modified or input.
Drawings
FIG. 1 is a process diagram of the manufacturing method of the present invention.
Detailed Description
The following are specific embodiments of the present invention, but the present invention is not limited to these embodiments.
Example 1 example 2
A980 MPa grade cold rolled Q & P steel with excellent plasticity has the smelting components shown in the table 1, and the balance not shown in the table 1 is Fe.
Comparative example 1, a cold rolled Q & P steel whose metallurgical composition is shown in table 1, and the balance not shown in table 1 is Fe.
TABLE 1 EXAMPLES AND COMPARATIVE EXAMPLES actual smelting Components (mass%,%)
| Steel grade | C | Si | Mn | P | S | Als | Nb |
| Example 1 | 0.20 | 1.52 | 1.90 | 0.012 | 0.0025 | 0.060 | 0.047 |
| Example 2 | 0.20 | 1.48 | 1.93 | 0.012 | 0.0025 | 0.060 | 0.050 |
| Comparative example 1 | 0.20 | 1.48 | 1.50 | 0.012 | 0.0025 | 0.060 | 0.045 |
The manufacturing method of the 3 steel grades comprises the following process flows:
molten iron pretreatment → converter smelting → alloy fine tuning station → LF furnace refining → RH vacuum degassing → continuous casting → hot rolling → leveling → hot rolled coil → cover annealing → acid pickling cold rolling → continuous annealing → finished product.
Specifically, the method comprises the following steps:
the steel area is smelted by adopting a converter → an alloy fine tuning station → an LF furnace for refining → RH vacuum degassing → continuous casting process for smelting;
the continuous casting production casting blank adopts a hot charging (hot peeling) process, and a dynamic soft reduction and electromagnetic stirring system is used for ensuring the quality of the casting blank;
the hot rolling is specifically as follows: the heating temperature of the casting blank is 1200-1260 ℃, the temperature is kept for 2-3 hours, the casting blank is rolled for 5-7 times by a roughing mill, hot rolled to an intermediate blank of 30-50mm, the finish rolling is carried out for 7 times by a hot continuous rolling unit, and the final rolling temperature is 890 +/-20 ℃;
rolling the steel plate to a target thickness by a hot plate, coiling the steel plate at the temperature of 650 +/-20 ℃, cooling the steel plate to room temperature in an air mode, and enabling the final structure of the hot rolled coil to be ferrite and pearlite or ferrite, pearlite and a small amount of bainite;
the cover annealing: feeding the hot rolled coil into a hood-type annealing furnace, adopting a DDQ hood annealing process, and then cooling (air cooling and water cooling); specific process parameters are shown in table 2 below;
acid pickling and cold rolling: pickling the hot rolled strip steel subjected to cover annealing, removing surface iron oxide scales, and carrying out cold continuous rolling to a target thickness, wherein the cold rolling reduction rate is 50-65%;
and (3) continuous annealing: heating the steel plate treated in the acid-washing and cold-rolling step to 840-860 ℃, preserving heat for 90-170s, carrying out two-phase region annealing, slowly cooling to 710-730 ℃ at a cooling speed of 3-5 ℃/s to form a certain amount of ferrite for improving plasticity, then cooling to 240-270 ℃ at a cooling rate of more than or equal to 35 ℃/s, quenching, heating to 290-350 ℃ for distributing at 380-720s, then coiling and air cooling to room temperature to obtain the finished steel coil.
The specific process parameters of the examples and comparative examples are shown in table 2:
TABLE 2 production of steel grades for the examples and comparative examples
980MPa grade cold rolled Q & P steels with excellent plasticity produced by processes B and C were used as examples within the scope of the invention, and the steel grades of example 1, example 2 and comparative example 1 produced by other processes were used as comparative examples. The mechanical properties and residual austenite content are shown in Table 3.
The thickness of the product produced in each example and comparative example was 1.2mm, and the residual austenite content was measured by a Pasnake MRD diffractometer.
TABLE 3 mechanical Properties and residual austenite contents of the examples and comparative examples
The 980MPa cold-rolled Q & P steel with excellent plasticity has yield strength of more than or equal to 650MPa, tensile strength of more than or equal to 980MPa and a product of strength and elongation of more than or equal to 25 GPa%.
What has been described above is a preferred embodiment of the present invention. Any equivalent embodiments that may be changed or modified into equivalent variations by those skilled in the art can be applied to other fields without departing from the technical spirit of the present invention, and any simple modification, equivalent variation and modification made to the above embodiments according to the technical spirit of the present invention still belong to the protection scope of the technical solution of the present invention.
Claims (10)
1. A manufacturing method of 980MPa cold-rolled Q & P steel with excellent plasticity is characterized by comprising the following process flows of:
molten iron pretreatment → converter smelting → alloy fine tuning station → LF furnace refining → RH vacuum degassing → continuous casting → hot rolling → leveling → hot rolled coil → cover annealing → acid pickling cold rolling → continuous annealing → finished product.
2. The manufacturing method according to claim 1, wherein the hood annealing: the hot rolled coil was fed into a hood-type annealing furnace, subjected to a DDQ hood annealing process at a hot/cold point temperature of 710/680 ℃ and then cooled.
3. The manufacturing method according to claim 1 or 2, characterized in that the hood annealing: annealing at 680-710 ℃ for 4-5h, cooling in air, and then cooling in water.
4. The manufacturing method according to claim 1, characterized in that the continuous annealing: heating the steel plate treated in the acid-washing and cold-rolling step to 840-860 ℃ for two-phase region annealing, slowly cooling to 710-730 ℃, then rapidly cooling to 240-270 ℃ for quenching, and then heating to 290-350 ℃ for distribution.
5. The method as claimed in claim 4, wherein the two-phase annealing is performed by heating to 840-860 ℃ for 90-170 seconds.
6. The method of claim 4 or 5, wherein the rapid cooling is cooling at a cooling rate of 35 ℃/s or more.
7. The method as claimed in any one of claims 4-6, wherein the distribution is performed by heating to 290 ℃ and 350 ℃ for 380 seconds and 720 seconds.
8. The manufacturing method according to claim 1, wherein the hot rolling is specifically: the heating temperature of the casting blank is 1200-1260 ℃, the temperature is kept for 2-3 hours, the rough rolling mill is used for rolling for 5-7 times, the hot rolling is carried out to an intermediate blank of 30-50mm, the hot continuous rolling mill is used for carrying out 7-time finish rolling, and the final rolling temperature is 870-910 ℃.
9. The method as claimed in claim 1, wherein the hot plate is rolled to a target thickness and then coiled at a temperature of 630-670 ℃ and then cooled to room temperature.
10. A 980MPa grade cold rolled Q & P steel with excellent plasticity manufactured by the manufacturing method according to any one of claims 1 to 9, characterized in that the 980MPa grade cold rolled Q & P steel with excellent plasticity contains the following chemical components in percentage by mass: c: 0.18-0.21%, Si: 1.4-1.6%, Mn: 1.8-2.1%, Nb: 0.04-0.06%, Al: 0.02-0.06%, P is less than or equal to 0.02%, S is less than or equal to 0.01%, and the balance is Fe.
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| CN111979489A (en) * | 2020-09-07 | 2020-11-24 | 鞍钢股份有限公司 | 780 MPa-grade high-plasticity cold-rolled DH steel and preparation method thereof |
| CN112048681A (en) * | 2020-09-07 | 2020-12-08 | 鞍钢股份有限公司 | 980 MPa-grade high-formability cold-rolled DH steel and preparation method thereof |
| CN112095046A (en) * | 2020-09-07 | 2020-12-18 | 鞍钢股份有限公司 | Ultrahigh-strength cold-rolled DH1180 steel and preparation method thereof |
| CN113025795A (en) * | 2021-02-04 | 2021-06-25 | 首钢集团有限公司 | Method for improving structure uniformity of cold-rolled high-strength steel |
| CN113186461A (en) * | 2021-04-15 | 2021-07-30 | 鞍钢股份有限公司 | High-strength-ductility deep cold-rolled steel plate and preparation method thereof |
| WO2022206911A1 (en) * | 2021-04-02 | 2022-10-06 | 宝山钢铁股份有限公司 | Low-carbon low-alloy q&p steel or hot-dip galvanized q&p steel with tensile strength greater than or equal to 1180 mpa, and manufacturing method therefor |
| CN115181898A (en) * | 2021-04-02 | 2022-10-14 | 宝山钢铁股份有限公司 | 1280 MPa-grade low-carbon low-alloy Q & P steel and rapid thermal treatment manufacturing method thereof |
| CN115233092A (en) * | 2022-06-24 | 2022-10-25 | 马鞍山钢铁股份有限公司 | 900 MPa-grade high-strength steel with excellent ductility and toughness and heat treatment method for improving residual austenite content of high-strength steel |
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| WO2022206911A1 (en) * | 2021-04-02 | 2022-10-06 | 宝山钢铁股份有限公司 | Low-carbon low-alloy q&p steel or hot-dip galvanized q&p steel with tensile strength greater than or equal to 1180 mpa, and manufacturing method therefor |
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| CN115181898B (en) * | 2021-04-02 | 2023-10-13 | 宝山钢铁股份有限公司 | 1280 MPa-level low-carbon low-alloy Q & P steel and rapid heat treatment manufacturing method thereof |
| CN113186461A (en) * | 2021-04-15 | 2021-07-30 | 鞍钢股份有限公司 | High-strength-ductility deep cold-rolled steel plate and preparation method thereof |
| CN115233092A (en) * | 2022-06-24 | 2022-10-25 | 马鞍山钢铁股份有限公司 | 900 MPa-grade high-strength steel with excellent ductility and toughness and heat treatment method for improving residual austenite content of high-strength steel |
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