CN115044831A - 1100 MPa-grade cold-rolled martensitic steel and manufacturing method thereof - Google Patents
1100 MPa-grade cold-rolled martensitic steel and manufacturing method thereof Download PDFInfo
- Publication number
- CN115044831A CN115044831A CN202210653524.5A CN202210653524A CN115044831A CN 115044831 A CN115044831 A CN 115044831A CN 202210653524 A CN202210653524 A CN 202210653524A CN 115044831 A CN115044831 A CN 115044831A
- Authority
- CN
- China
- Prior art keywords
- cold
- steel
- equal
- temperature
- less
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
Images
Classifications
-
- 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
- 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
-
- 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
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
-
- 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
- C22C38/28—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
- C22C38/38—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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/001—Austenite
-
- 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
- C21D2211/008—Martensite
-
- 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
Abstract
The invention discloses 1100 MPa-grade cold-rolled martensitic steel and a manufacturing method thereof, wherein the 1100 MPa-grade cold-rolled martensitic steel comprises the following chemical components in percentage by mass: 0.13-0.17%, Si: 1.05 to 1.15%, Mn: 1.70-1.80%, P: less than or equal to 0.020%, S: less than or equal to 0.010 percent, Cr: 0.25-0.35%, Alt: 0.030 to 0.050%, Ti: 0.020-0.030%, Ce: 10-20ppm, the balance being Fe and unavoidable impurities. The manufacturing method comprises a continuous annealing process, wherein the heating temperature and the soaking temperature are both 790-800 ℃. The 1100 MPa-level cold-rolled martensitic steel has good comprehensive mechanical properties.
Description
Technical Field
The invention belongs to the technical field of metallurgical plate production, and particularly relates to 1100 MPa-grade cold-rolled martensitic steel and a manufacturing method thereof.
Background
People in the modern society have increasingly greater demands on automobiles and have increasingly higher requirements on quality. According to research, the total mass of the automobile can be reduced by 6-10% of fuel consumption and CO for every 10% of the total mass of the automobile 2 The emission is reduced by 4.5%. Therefore, on the premise of ensuring the driving safety of the automobile, the weight of the automobile is reduced as much as possible, so that the effect of energy conservation and emission reduction is gradually a main research hotspot of the modern automobile technical research.
In the past, cold-rolled steel sheets of ordinary strength have been most used as vehicle body materials. However, low-strength cold-rolled steel sheets are increasingly showing limitations in today's high quality demanding society. According to researches, if high-strength steel is used as an automobile body structure, compared with a common cold-rolled steel plate, the high-strength steel can achieve the same strength and can be thinned by 0.3-0.5mm, the weight of 15-20% can be reduced, the oil consumption is reduced by about 8-10%, in addition, the advanced high-strength steel plate not only has high strength and excellent toughness, but also has the advantages and characteristics of good forming performance and good anti-collision performance, so that the advanced high-strength steel has great advantages when being applied to an automobile, the reliability and safety of the automobile are improved, and the advanced high-strength steel welding manufacturability research is of great significance.
Disclosure of Invention
Aiming at one or more problems in the prior art, the invention provides 1100 MPa-grade cold-rolled martensitic steel which comprises the following chemical components in percentage by mass: c: 0.13-0.17%, Si: 1.05 to 1.15%, Mn: 1.70-1.80%, P: less than or equal to 0.020%, S: less than or equal to 0.010 percent, Cr: 0.25-0.35%, Alt: 0.030 to 0.050%, Ti: 0.020-0.030%, Ce: 10-20ppm, and the balance of Fe and inevitable impurities;
the manufacturing method of the 1100 MPa-level cold-rolled martensite steel comprises a continuous annealing process, wherein the heating and soaking temperatures are 790-800 ℃, the rapid cooling speed is 40-50 ℃/s, the termination temperature of the rapid cooling is 260-280 ℃, the overaging temperature is 280-320 ℃, and the final cooling temperature is less than or equal to 150 ℃.
In some embodiments, the 1100MPa grade cold-rolled martensitic steel comprises the following chemical components in percentage by mass: c: 0.13-0.17%, Si: 1.05 to 1.15%, Mn: 1.73-1.79%, P: less than or equal to 0.020%, S: less than or equal to 0.010 percent, Cr: 0.27-0.33%, Alt: 0.038-0.043%, Ti: 0.020-0.025%, Ce: 13-18ppm, and the balance of Fe and inevitable impurities.
In some embodiments, the microstructure of the 1100MPa grade cold-rolled martensite steel is martensite and a small amount of ferrite and retained austenite, the grain size is grade 12, and the mechanical properties meet the following requirements: the yield strength is more than or equal to 940MPa, the tensile strength is more than or equal to 1170MPa, and the elongation A 50 Not less than 6.5%, and the yield ratio is 0.80-0.85.
In some embodiments, the 1100MPa grade cold rolled martensitic steel has a thickness of 1.5 to 2.0 mm.
The invention also provides a manufacturing method of 1100 MPa-grade cold-rolled martensite steel, which comprises the following process steps: smelting → continuous casting → hot rolling → acid rolling → continuous annealing → leveling; wherein the heating and soaking temperatures in the continuous annealing process are respectively 790-800 ℃, the rapid cooling speed is 40-50 ℃/s, the rapid cooling termination temperature is 260-280 ℃, the overaging temperature is 280-320 ℃, and the final cooling temperature is less than or equal to 150 ℃.
In some embodiments, the smelt → continuous casting process comprises the following steps: the method comprises the following steps of molten iron pretreatment, converter, RH refining and casting machine, wherein molten iron for the casting machine comprises the following components: 0.13-0.17%, Si: 1.05 to 1.15%, Mn: 1.70-1.80%, P: less than or equal to 0.020%, S: less than or equal to 0.010 percent, Cr: 0.25-0.35%, Alt: 0.030 to 0.050%, Ti: 0.020-0.030%, Ce: 10-20ppm, the balance being Fe and unavoidable impurities.
In some embodiments, the hot rolling process comprises the following steps: heating a casting blank, rough rolling, finish rolling, cooling and coiling; wherein the tapping temperature of the casting blank is 1190-.
In some embodiments, the acid rolling process is specifically: and (3) pickling the hot rolled steel strip, removing surface iron oxide scales, cold rolling the steel strip by a 5-stand cold rolling mill until the cold rolling reduction rate is 50-70% and the target thickness is 1.5-2.0mm, and obtaining the cold hard coil steel.
In some embodiments, the continuous annealing process is specifically: uncoiling the cold-hard coil steel, heating and carrying out continuous annealing, wherein the heating and soaking temperatures are 790-800 ℃, the rapid cooling speed is 40-50 ℃/s, the rapid cooling termination temperature is 260-280 ℃, the overaging temperature is 280-320 ℃, and the final cooling temperature is less than or equal to 150 ℃.
In some embodiments, the planarization process is specifically: the flat elongation is 0.50-0.60%.
The 1100 MPa-grade cold-rolled martensitic steel provided based on the technical scheme adopts the component design of C, Si, Mn, Cr, Ti and Ce, and is matched with a reasonable manufacturing method (such as a continuous annealing process) to provide the 1100 MPa-grade cold-rolled martensitic steel, the microstructure of the steel is mainly martensite, a small amount of ferrite and retained austenite, the grain size is 12 grades, and the mechanical property meets the following requirements: the yield strength is more than or equal to 940MPa, the tensile strength is more than or equal to 1170MPa, and the elongation A 50 Not less than 6.5%, and the yield ratio is 0.80-0.85. Therefore, the 1100 MPa-grade cold-rolled martensite steel provided by the invention has high strength and higher yield ratio (0.80-0.85), has the advantages of good crashworthiness, material saving, weight reduction, good forming performance and the like when being used for automobile body materials, and the yield ratio is not too high (for example, more than or equal to 0.90) to increase the brittleness of the steel, thereby further reducing the safety performance.
Drawings
FIG. 1 is a microstructure diagram of a 1100MPa grade cold-rolled martensitic steel produced in example 1.
Detailed Description
The invention aims to provide 1100 MPa-grade cold-rolled martensitic steel and a manufacturing method thereof. The method is realized by the following technical scheme.
The chemical components of the 1100MPa cold-rolled martensite steel comprise the following components in percentage by mass: c: 0.13-0.17%, Si: 1.05 to 1.15%, Mn: 1.70-1.80%, P: less than or equal to 0.020%, S: less than or equal to 0.010 percent, Cr: 0.25-0.35%, Alt: 0.030 to 0.050%, Ti: 0.020-0.030%, Ce: 10-20ppm, and the balance of Fe and inevitable impurities;
the manufacturing method of the 1100 MPa-level cold-rolled martensite steel comprises a continuous annealing process, wherein the heating and soaking temperatures are 790-800 ℃, the rapid cooling speed is 40-50 ℃/s, the termination temperature of the rapid cooling is 260-280 ℃, the overaging temperature is 280-320 ℃, and the final cooling temperature is less than or equal to 150 ℃.
In some embodiments, the 1100MPa grade cold-rolled martensitic steel comprises the following chemical components in percentage by mass: c: 0.13-0.17%, Si: 1.05 to 1.15%, Mn: 1.73-1.79%, P: less than or equal to 0.020%, S: less than or equal to 0.010 percent, Cr: 0.27-0.33%, Alt: 0.038-0.043%, Ti: 0.020-0.025%, Ce: 13-18ppm, and the balance of Fe and inevitable impurities.
The 1100 MPa-grade cold-rolled martensitic steel provided by the invention has the microstructure of martensite, a small amount of ferrite and residual austenite, the grain size is 12 grade, and the mechanical properties meet the following requirements: the yield strength is more than or equal to 940MPa, the tensile strength is more than or equal to 1170MPa, and the elongation A 50 Not less than 6.5%, and the yield ratio is 0.80-0.85.
In some embodiments, the 1100MPa grade cold rolled martensitic steel has a thickness of 1.5 to 2.0 mm.
The invention provides a method for manufacturing 1100 MPa-grade cold-rolled martensite steel, which comprises the following process steps: smelting → continuous casting → hot rolling → acid rolling → continuous annealing → leveling; wherein the heating and soaking temperatures in the continuous annealing process are respectively 790-800 ℃, the rapid cooling speed is 40-50 ℃/s, the rapid cooling termination temperature is 260-280 ℃, the overaging temperature is 280-320 ℃, and the final cooling temperature is less than or equal to 150 ℃.
In some embodiments, the smelt → continuous casting process comprises the following steps: the method comprises the following steps of molten iron pretreatment, converter, RH refining and casting machine, wherein molten iron for the casting machine comprises the following components: 0.13-0.17%, Si: 1.05 to 1.15%, Mn: 1.70-1.80%, P: less than or equal to 0.020%, S: less than or equal to 0.010 percent, Cr: 0.25-0.35%, Alt: 0.030 to 0.050%, Ti: 0.020-0.030%, Ce: 10-20ppm, the balance being Fe and unavoidable impurities.
In some embodiments, the hot rolling process comprises the following steps: heating a casting blank, rough rolling, finish rolling, cooling and coiling; wherein the tapping temperature of the casting blank is 1190-; laminar flow cooling equipment and a front dispersion cooling mode are adopted for cooling, and the coiling temperature is 600-640 ℃.
In some embodiments, the acid rolling process is specifically: and (3) pickling the hot rolled steel strip, removing surface iron oxide scales, cold rolling the steel strip by a 5-stand cold rolling mill until the cold rolling reduction rate is 50-70% and the target thickness is 1.5-2.0mm, and obtaining the cold hard coil steel.
In some embodiments, the continuous annealing process is specifically: uncoiling the cold-hard coil steel, heating and carrying out continuous annealing, wherein the heating and soaking temperatures are 790-800 ℃, the time is 160-240 seconds, the rapid cooling speed is 40-50 ℃/s, the rapid cooling termination temperature is 260-280 ℃, the overaging temperature is 280-320 ℃, and the final cooling temperature is less than or equal to 150 ℃.
In some embodiments, the planarization process is specifically: the flat elongation is 0.50-0.60%.
The present invention will be described in detail below with reference to specific examples, which are intended to facilitate understanding of the present invention and are not intended to limit the present invention.
Example 1
The molten iron is subjected to desulfurization pretreatment, a top-bottom combined blown converter is adopted for smelting to decarbonize and descale the molten iron to obtain molten steel, argon is blown in the whole smelting process of the converter, scrap steel is added into the converter, and the tapping temperature of the converter is 1650 ℃. Then, the molten steel smelted in the converter is subjected to RH external refining, and deep decarburization treatment is carried out according to the in-place components and the temperature of the RH molten steel supplied by the converter, and the chemical components of the RH external refining and casting machine are shown in Table 1. The superheat degree of the continuous casting of the slab is 25 ℃, and then slab cleaning, slow cooling and continuous casting slab quality inspection are carried out. The heating temperature of the plate blank is 1220 ℃, the heating time is 228min, and the heated plate blank is descaled by high-pressure water. The width is fixed by a width fixing press, 2 frames are adopted for rough rolling, and 7 frames are adopted for CVC finish rolling. The finish rolling temperature is 870 ℃, and the thickness of the finished product is 4.5 mm. And adopting front dispersed cooling for laminar cooling, and reducing the temperature of the steel strip to 620 ℃ for coiling. The hot-rolled strip steel is pickled by a hydrochloric acid tank, the acid tank adopts an i-BOX technology newly developed by MH, the operation and maintenance are greatly simplified, the energy and labor force are saved, after the surface oxide scale of the hot-rolled strip steel is removed, the hot-rolled strip steel is cold-rolled by a 5-frame UCM rolling mill, the cold-rolling reduction rate is 60 percent, and the target thickness is 1.8 mm. The cold-hard coil continuous annealing is carried out in a continuous vertical annealing furnace with HGJC function, the running speed of a steel strip is 98m/min, the heating and soaking temperatures are 800 ℃, the time is 200s, the fast cooling speed is 45 ℃/s, the fast cooling termination temperature is 270 ℃, the overaging temperature is 300 ℃, the final cooling temperature is 150 ℃, and the flat elongation is 0.55%. Finally, product performance detection is carried out, as shown in the following table 2.
Example 2
Carrying out desulfurization pretreatment on molten iron, carrying out decarburization and descaling on the molten iron by adopting a top-bottom combined blown converter for smelting to obtain molten steel, blowing argon in the whole process of the converter smelting, adding scrap steel into the converter, and tapping the steel at the converter at the temperature of 1640 ℃. Then, the molten steel smelted in the converter is subjected to RH external refining, and deep decarburization treatment is carried out according to the in-place components and the temperature of the RH molten steel supplied by the converter, and the chemical components of the RH external refining and casting machine are shown in Table 1. The superheat degree of the slab continuous casting is 20 ℃, and then slab cleaning, slow cooling and quality inspection of the continuous casting slab are carried out. The heating temperature of the plate blank is 1216 ℃, the heating time is 225min, and the heated plate blank is descaled by high-pressure water. The width is fixed by a width fixing press, 2 frames are adopted for rough rolling, and 7 frames are adopted for CVC finish rolling. The finish rolling temperature is 866 ℃ and the thickness of the finished product is 4.5 mm. And adopting front dispersed cooling for laminar cooling, and reducing the temperature of the steel strip to 620 ℃ for coiling. The hot-rolled strip steel is pickled by a hydrochloric acid tank, the acid tank adopts an i-BOX technology newly developed by MH, the operation and maintenance are greatly simplified, the energy and labor force are saved, after the surface oxide scale of the hot-rolled strip steel is removed, the hot-rolled strip steel is cold-rolled by a 5-frame UCM rolling mill, the cold-rolling reduction rate is 60 percent, and the target thickness is 1.8 mm. The cold-hard coil continuous annealing is carried out in a continuous vertical annealing furnace with HGJC function, the running speed of a steel strip is 102m/min, the heating and soaking temperature is 799 ℃, the time is 200s, the fast cooling speed is 45 ℃/s, the fast cooling termination temperature is 270 ℃, the overaging temperature is 300 ℃, the final cooling temperature is 150 ℃, and the flattening elongation is 0.55%. Finally, product performance detection is carried out, and the results are shown in the following table 2.
Example 3
The method comprises the following steps of carrying out desulfurization pretreatment on molten iron, carrying out decarburization and descaling on the molten iron by adopting a top-bottom combined blown converter for smelting to obtain molten steel, blowing argon in the whole process of the converter smelting, adding scrap steel into the converter, and carrying out steel tapping at the temperature of 1643 ℃ in the converter. Then, the molten steel smelted in the converter is subjected to RH external refining, and deep decarburization treatment is carried out according to the in-place components and the temperature of the RH molten steel supplied by the converter, and the chemical components of the RH external refining and casting machine are shown in Table 1. The superheat degree of the continuous casting of the slab is 23 ℃, and then slab cleaning, slow cooling and continuous casting slab quality inspection are carried out. The heating temperature of the plate blank is 1216 ℃, the heating time is 220min, and the heated plate blank is descaled by high-pressure water. The width is fixed by a width fixing press, 2 frames are adopted for rough rolling, and 7 frames are adopted for CVC finish rolling. The finish rolling temperature is 868 ℃, and the thickness of the finished product is 4.5 mm. And adopting front dispersion cooling for laminar cooling, and reducing the temperature of the steel strip to 626 ℃ for coiling. The hot-rolled strip steel is pickled by a hydrochloric acid tank, the acid tank adopts an i-BOX technology newly developed by MH, the operation and maintenance are greatly simplified, the energy and labor force are saved, after the surface oxide scale of the hot-rolled strip steel is removed, the hot-rolled strip steel is cold-rolled by a 5-frame UCM rolling mill, the cold-rolling reduction rate is 60 percent, and the target thickness is 1.8 mm. The cold-hard coil continuous annealing is carried out in a continuous vertical annealing furnace with HGJC function, the running speed of a steel strip is 100m/min, the heating and soaking temperature is 790 ℃, the time is 200s, the fast cooling speed is 45 ℃/s, the fast cooling termination temperature is 270 ℃, the overaging temperature is 300 ℃, the final cooling temperature is 150 ℃, and the flat elongation is 0.55%. Finally, product performance detection is carried out, and the results are shown in the following table 2.
Comparative example 1
The manufacturing method follows the method shown in example 1 except that the RH secondary refining for the caster chemical composition is different from that used in example 1 as shown in table 1 below. Finally, product performance detection is carried out, and the results are shown in the following table 2.
Comparative example 2
The manufacturing method follows the method shown in example 1 except that the RH secondary refining for the caster chemical composition is different from that used in example 1 as shown in table 1 below. Finally, product performance detection is carried out, and the results are shown in the following table 2.
Comparative examples 3 to 4
The manufacturing methods of comparative examples 3 to 4 were the same as those of example 1 except that the heating and soaking temperatures in the continuous annealing were different from those of example 1, specifically, the heating and soaking temperature in the continuous annealing process of comparative example 3 was 770 ℃, and the heating and soaking temperature in the continuous annealing process of comparative example 4 was 810 ℃. Finally, product performance detection is carried out, and the results are shown in the following table 2.
Table 1: chemical composition (wt%) of inventive examples 1-3 and comparative examples 1-4
| C | Si | Mn | P | S | Alt | Ti | Cr | Ce(ppm) | |
| Example 1 | 0.14 | 1.15 | 1.73 | 0.016 | 0.003 | 0.042 | 0.022 | 0.28 | 13 |
| Example 2 | 0.13 | 1.05 | 1.78 | 0.018 | 0.008 | 0.038 | 0.025 | 0.27 | 15 |
| Example 3 | 0.17 | 1.10 | 1.79 | 0.016 | 0.008 | 0.043 | 0.020 | 0.33 | 18 |
| Comparative example 1 | 0.15 | 0.96 | 1.56 | 0.012 | 0.006 | 0.034 | 0.055 | 0.35 | - |
| Comparative example 2 | 0.15 | 0.95 | 1.58 | 0.015 | 0.008 | 0.038 | 0.030 | 0.33 | 13 |
| Comparative example 3 | 0.14 | 1.15 | 1.73 | 0.016 | 0.003 | 0.042 | 0.022 | 0.28 | 13 |
| Comparative example 4 | 0.14 | 1.15 | 1.73 | 0.016 | 0.003 | 0.042 | 0.022 | 0.28 | 13 |
Table 2: mechanical properties of Steel coils according to examples 1 to 3 and comparative examples 1 to 4 of the present invention
| Examples | Yield strength R eL (MPa) | Tensile strength R m (MPa) | Elongation A 50 (％) | Yield ratio |
| Example 1 | 956 | 1190 | 7 | 0.80 |
| Example 2 | 949 | 1178 | 6.5 | 0.81 |
| Example 3 | 1000 | 1200 | 7 | 0.83 |
| Comparative example 1 | 858 | 1133 | 5.5 | 0.76 |
| Comparative example 2 | 862 | 1145 | 7 | 0.75 |
| Comparative example 3 | 924 | 1158 | 6 | 0.80 |
| Comparative example 4 | 1065 | 1167 | 12 | 0.91 |
As is clear from the contents shown in tables 1 and 2, the mechanical properties of the 1100MPa grade cold-rolled martensitic steel provided by the present invention satisfy: the yield strength is more than or equal to 940MPa, the tensile strength is more than or equal to 1170MPa, and the elongation A 50 The yield ratio is 0.80-0.85, so that the 1100 MPa-grade cold-rolled martensite steel provided by the invention has high strength and higher yield ratio, and has the advantages of good anti-collision performance, material saving, weight reduction, good forming performance and the like when being used for vehicle body materials. From the results of comparative examples 1-2, it is understood that when the chemical components and/or the contents thereof fail to satisfy the requirements of the present invention, the strength of the obtained steel sheet is low; from the results of comparative example 3, it can be seen that the annealing operation was continuedWhen the heating and soaking temperature in the process is lower, the strength of the steel plate is reduced; from the results of comparative example 4, it is understood that when the heating and soaking temperatures of the continuous annealing process are high, the yield ratio of the obtained steel sheet is excessively high, which may cause an increase in brittleness of the steel sheet, thereby resulting in a decrease in safety.
Finally, it should be noted that: although the present invention has been described in detail with reference to the foregoing embodiments, those skilled in the art will understand that various changes, modifications and substitutions can be made without departing from the spirit and scope of the invention as defined by the appended claims. Any modification, equivalent replacement, or improvement made within the spirit and principle of the present invention should be included in the protection scope of the present invention.
Claims (5)
1. The 1100 MPa-grade cold-rolled martensite steel comprises the following chemical components in percentage by mass: c: 0.13-0.17%, Si: 1.05 to 1.15%, Mn: 1.70-1.80%, P: less than or equal to 0.020%, S: less than or equal to 0.010 percent, Cr: 0.25-0.35%, Alt: 0.030 to 0.050%, Ti: 0.020-0.030%, Ce: 10-20ppm, and the balance of Fe and inevitable impurities;
the manufacturing method of the 1100 MPa-level cold-rolled martensite steel comprises a continuous annealing process, wherein the heating and soaking temperatures are 790-800 ℃, the rapid cooling speed is 40-50 ℃/s, the termination temperature of the rapid cooling is 260-280 ℃, the overaging temperature is 280-320 ℃, and the final cooling temperature is less than or equal to 150 ℃.
2. The 1100MPa grade cold-rolled martensite steel of claim 1, wherein the microstructure is martensite and a small amount of ferrite and retained austenite, the grain size is 12 grade, and the mechanical properties meet the following requirements: the yield strength is more than or equal to 940MPa, the tensile strength is more than or equal to 1170MPa, and the elongation A 50 Not less than 6.5%, and yield ratio of 0.80-0.85.
3. The 1100MPa grade cold rolled martensitic steel according to claim 1 or 2 having a thickness of 1.5-2.0 mm.
4. The method of manufacturing a 1100MPa grade cold rolled martensitic steel as claimed in any one of claims 1 to 3 comprising the process steps of: smelting → continuous casting → hot rolling → acid rolling → continuous annealing → leveling; wherein the heating and soaking temperatures in the continuous annealing process are respectively 790-800 ℃, the rapid cooling speed is 40-50 ℃/s, the rapid cooling termination temperature is 260-280 ℃, the overaging temperature is 280-320 ℃, and the final cooling temperature is less than or equal to 150 ℃.
5. The manufacturing method according to claim 4, wherein:
the smelting → continuous casting process comprises the following steps: the method comprises the following steps of molten iron pretreatment, converter, RH refining and casting machine, wherein molten iron for the casting machine comprises the following components: 0.13-0.17%, Si: 1.05-1.15%, Mn: 1.70-1.80%, P: less than or equal to 0.020%, S: less than or equal to 0.010 percent, Cr: 0.25-0.35%, Alt: 0.030 to 0.050%, Ti: 0.020-0.030%, Ce: 10-20ppm, and the balance of Fe and inevitable impurities;
the hot rolling process comprises the following steps: heating a casting blank, rough rolling, finish rolling, cooling and coiling; wherein the tapping temperature of the casting blank is 1190-;
the acid rolling process specifically comprises the following steps: pickling the hot rolled steel strip, removing surface iron oxide scales, cold rolling by a 5-frame cold rolling mill with a cold rolling reduction rate of 50-70% until the target thickness is 1.5-2.0mm, and obtaining cold hard coil steel;
the continuous annealing process specifically comprises the following steps: uncoiling the cold-hard coil steel, heating and carrying out continuous annealing, wherein the heating and soaking temperatures are 790-800 ℃, the rapid cooling speed is 40-50 ℃/s, the rapid cooling termination temperature is 260-280 ℃, the overaging temperature is 280-320 ℃, and the final cooling temperature is less than or equal to 150 ℃;
the leveling process specifically comprises the following steps: the flat elongation is 0.50-0.60%.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202210653524.5A CN115044831B (en) | 2022-06-09 | 2022-06-09 | 1100MPa grade cold-rolled martensitic steel and manufacturing method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202210653524.5A CN115044831B (en) | 2022-06-09 | 2022-06-09 | 1100MPa grade cold-rolled martensitic steel and manufacturing method thereof |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN115044831A true CN115044831A (en) | 2022-09-13 |
| CN115044831B CN115044831B (en) | 2023-08-25 |
Family
ID=83160713
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202210653524.5A Active CN115044831B (en) | 2022-06-09 | 2022-06-09 | 1100MPa grade cold-rolled martensitic steel and manufacturing method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN115044831B (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN115874112A (en) * | 2022-11-02 | 2023-03-31 | 包头钢铁（集团）有限责任公司 | Method for manufacturing 1300MPa cold-rolled martensitic steel |
| CN115874112B (en) * | 2022-11-02 | 2024-04-30 | 包头钢铁（集团）有限责任公司 | Manufacturing method of 1300 megapascal cold-rolled martensitic steel |
Citations (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2010090432A (en) * | 2008-10-08 | 2010-04-22 | Jfe Steel Corp | Super high-strength cold-rolled steel sheet excellent in ductility, and producing method of the same |
| KR20130027793A (en) * | 2011-09-08 | 2013-03-18 | 현대하이스코 주식회사 | Ultra high strength cold-rolled steel sheet and hot dip plated steel sheet with 1180mpa grade in tensile strength with excellent ductility and method of manufacturing the same |
| US20170145535A1 (en) * | 2014-07-03 | 2017-05-25 | Arcelormittal | Method for Manufacturing a High Strength Steel Sheet and Sheet Obtained |
| CN107406938A (en) * | 2015-03-03 | 2017-11-28 | 杰富意钢铁株式会社 | High-strength steel sheet and its manufacture method |
| CN107429344A (en) * | 2015-03-18 | 2017-12-01 | 杰富意钢铁株式会社 | High strength cold rolled steel plate and its manufacture method |
| CN107619993A (en) * | 2016-07-13 | 2018-01-23 | 上海梅山钢铁股份有限公司 | Yield strength 750MPa level cold rolling martensite steel plates and its manufacture method |
| CN109594020A (en) * | 2018-12-28 | 2019-04-09 | 首钢集团有限公司 | A kind of tensile strength 1000MPa grades of cold rolling Multiphase Steels and preparation method thereof |
| CN111936649A (en) * | 2018-03-30 | 2020-11-13 | 杰富意钢铁株式会社 | High-strength galvanized steel sheet, high-strength member, and method for producing same |
-
2022
- 2022-06-09 CN CN202210653524.5A patent/CN115044831B/en active Active
Patent Citations (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2010090432A (en) * | 2008-10-08 | 2010-04-22 | Jfe Steel Corp | Super high-strength cold-rolled steel sheet excellent in ductility, and producing method of the same |
| KR20130027793A (en) * | 2011-09-08 | 2013-03-18 | 현대하이스코 주식회사 | Ultra high strength cold-rolled steel sheet and hot dip plated steel sheet with 1180mpa grade in tensile strength with excellent ductility and method of manufacturing the same |
| US20170145535A1 (en) * | 2014-07-03 | 2017-05-25 | Arcelormittal | Method for Manufacturing a High Strength Steel Sheet and Sheet Obtained |
| CN107406938A (en) * | 2015-03-03 | 2017-11-28 | 杰富意钢铁株式会社 | High-strength steel sheet and its manufacture method |
| CN107429344A (en) * | 2015-03-18 | 2017-12-01 | 杰富意钢铁株式会社 | High strength cold rolled steel plate and its manufacture method |
| CN107619993A (en) * | 2016-07-13 | 2018-01-23 | 上海梅山钢铁股份有限公司 | Yield strength 750MPa level cold rolling martensite steel plates and its manufacture method |
| CN111936649A (en) * | 2018-03-30 | 2020-11-13 | 杰富意钢铁株式会社 | High-strength galvanized steel sheet, high-strength member, and method for producing same |
| CN109594020A (en) * | 2018-12-28 | 2019-04-09 | 首钢集团有限公司 | A kind of tensile strength 1000MPa grades of cold rolling Multiphase Steels and preparation method thereof |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN115874112A (en) * | 2022-11-02 | 2023-03-31 | 包头钢铁（集团）有限责任公司 | Method for manufacturing 1300MPa cold-rolled martensitic steel |
| CN115874112B (en) * | 2022-11-02 | 2024-04-30 | 包头钢铁（集团）有限责任公司 | Manufacturing method of 1300 megapascal cold-rolled martensitic steel |
Also Published As
| Publication number | Publication date |
|---|---|
| CN115044831B (en) | 2023-08-25 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN112725704B (en) | Hot-galvanized 420 MPa-grade low-alloy high-strength steel for automobiles and production method thereof | |
| CN112095046B (en) | Ultrahigh-strength cold-rolled DH1180 steel and preparation method thereof | |
| CN101338400B (en) | High strength low-temperature-used low carbon bainite steel and production process thereof | |
| CN109161805B (en) | 590 MPa-grade automobile lightweight cold-rolled dual-phase steel and production method thereof | |
| CN111485177A (en) | Low-cost 780 MPa-grade cold-rolled dual-phase steel and production method thereof | |
| CN109112433A (en) | Without 590MPa grades of cold-rolled biphase steels of striated surface defect and production method | |
| CN112080692A (en) | 280 MPa-grade cold-rolled low-yield-ratio stamping steel for automobile structure and production method thereof | |
| CN107815591A (en) | Hot-dip galvanizing sheet steel and preparation method thereof | |
| CN115011873A (en) | Hot-galvanized high-strength structural steel with yield strength of 550MPa and production method thereof | |
| CN114525449A (en) | DC04 automobile steel plate for cold rolling deep drawing and manufacturing method thereof | |
| CN114438413A (en) | Hot-dip galvanized high-strength structural steel with yield strength of 340MPa and production method thereof | |
| CN113151649B (en) | Production method of low-temperature annealing cold-rolled steel plate and cold-rolled steel plate | |
| CN111926252B (en) | Hot-rolled pickled steel plate for deep drawing and production method thereof | |
| CN113061797A (en) | Improved production method of QStE420TM hot-rolled steel plate | |
| CN113403541A (en) | 550 MPa-level low-alloy high-strength cold-rolled steel plate and production method thereof | |
| CN112226681A (en) | Low-cost high-strength galvanized sheet SGC570 for structure and production method thereof | |
| CN107513669A (en) | A kind of high-strength cold rolling square and rectangular pipe steel and its manufacture method | |
| CN115537661B (en) | 600 MPa-level hot dip galvanized dual-phase steel for automobile structure and production method thereof | |
| CN112063818A (en) | Low-temperature coiled cold-rolled steel plate with high formability and production method thereof | |
| CN109321825B (en) | 450 MPa-grade automobile lightweight cold-rolled dual-phase steel and production method thereof | |
| CN107829026B (en) | thin-specification 980 MPa-grade dual-phase steel and processing method thereof | |
| CN112226679B (en) | Cold-rolled 980 MPa-grade martensitic steel and production method thereof | |
| CN112501513B (en) | Low-carbon acid-pickled steel with excellent formability and surface quality and production method thereof | |
| CN115044831B (en) | 1100MPa grade cold-rolled martensitic steel and manufacturing method thereof | |
| CN114015938A (en) | 240 MPa-grade cold-rolled carbon structural steel and production method thereof |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| PB01 | Publication | ||
| PB01 | Publication | ||
| SE01 | Entry into force of request for substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| GR01 | Patent grant | ||
| GR01 | Patent grant |