CN112779474A - Hot forming strip steel with zinc-based coating at 2000MPa level and production method thereof - Google Patents
Hot forming strip steel with zinc-based coating at 2000MPa level and production method thereof Download PDFInfo
- Publication number
- CN112779474A CN112779474A CN202011321138.3A CN202011321138A CN112779474A CN 112779474 A CN112779474 A CN 112779474A CN 202011321138 A CN202011321138 A CN 202011321138A CN 112779474 A CN112779474 A CN 112779474A
- Authority
- CN
- China
- Prior art keywords
- hot
- zinc
- strip steel
- production method
- 2000mpa
- 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.)
- Pending
Links
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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing 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
- 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
-
- 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
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C33/00—Making ferrous alloys
- C22C33/04—Making ferrous alloys by melting
- C22C33/06—Making ferrous alloys by melting using master alloys
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
-
- C—CHEMISTRY; METALLURGY
- 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
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
- C23C2/06—Zinc or cadmium or alloys based thereon
-
- C—CHEMISTRY; METALLURGY
- C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
- C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
- C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
- C23C2/34—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the shape of the material to be treated
- C23C2/36—Elongated material
- C23C2/40—Plates; Strips
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/008—Martensite
Landscapes
- Chemical & Material Sciences (AREA)
- Engineering & Computer Science (AREA)
- Materials Engineering (AREA)
- Mechanical Engineering (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Physics & Mathematics (AREA)
- Thermal Sciences (AREA)
- Crystallography & Structural Chemistry (AREA)
- Chemical Kinetics & Catalysis (AREA)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
The invention discloses a hot-formed strip steel with a zinc-based coating of 2000MPa and a production method thereof, belonging to the technical field of metallurgy. The strip steel substrate comprises the following chemical components in percentage by mass: c: 0.25 to 0.40%, Mn: 1.10-1.70%, S is less than or equal to 0.012%, P is less than or equal to 0.020%, and Si: 0.1-0.3%, Als: 0.030-0.050%, Cr: 0.20-0.40%, B: 0.0010-0.0030%, Ti: 0.035-0.050%, V: 0.15-0.30%, N is less than or equal to 0.0030%, and the balance is iron and inevitable impurities. The production method comprises the working procedures of molten iron pretreatment, converter steelmaking, LF refining, RH refining, continuous casting, hot rolling, cold rolling, continuous galvanizing and finishing. The strip steel has ultrahigh strength and excellent welding performance and forming performance.
Description
Technical Field
The invention belongs to the technical field of metallurgy, and particularly relates to 2000 MPa-level hot forming strip steel with a zinc-based coating and a production method thereof.
Background
With the improvement of the safety performance requirement of the automobile, the automobile host factory adopts more and more hot forming steel of 1500-2000MPa grade, thereby achieving the purpose of reducing weight and improving the safety of the automobile. However, the surface is oxidized during the hot forming process, so that the surface of the current hot forming steel is provided with a layer of aluminum-silicon coating to prevent the oxidation of the steel strip during the hot forming process. In the hot forming process, the steel plate is heated at high temperature in the air to cause the surface oxidation and decarburization of the steel plate, the mechanical property of the steel plate is influenced, and meanwhile, in order to ensure the requirements of subsequent coating and the like, the hot forming part with the iron scale needs to be subjected to shot blasting or acid pickling treatment to remove oxides, so that the hot forming cost is greatly increased. In addition, automotive parts generally require certain corrosion resistance, and the development of coated hot-formed steel sheets is an urgent need for the development of hot-forming techniques.
Disclosure of Invention
In order to solve the technical problems, the invention provides hot forming strip steel with a zinc-based plating layer of 2000MPa and a production method thereof; the hot formed strip steel produced by the method has good corrosion resistance and hot stamping forming performance.
In order to realize the purpose of the invention, the invention adopts the technical scheme that:
a hot forming strip steel with a zinc-based coating of 2000MPa level comprises the following chemical components by mass percent: c: 0.25 to 0.40%, Mn: 1.10-1.70%, S is less than or equal to 0.012%, P is less than or equal to 0.020%, and Si: 0.10-0.30%, Als: 0.030-0.050%, Cr: 0.20-0.40%, B: 0.0010-0.0030%, Ti: 0.035-0.050%, V: 0.15-0.30%, N is less than or equal to 0.0030%, and the balance is iron and inevitable impurities.
The tensile strength of the strip steel is less than or equal to 1000MPa, and the tensile strength of the strip steel is more than or equal to 2000MPa after heat treatment.
The production method of the hot forming strip steel with the zinc-based coating of 2000MPa comprises the working procedures of molten iron pretreatment, converter steelmaking, LF refining, RH refining, continuous casting, hot rolling, cold rolling, continuous galvanizing and finishing; in the RH refining process, V and Ti are added, the mass percentage of V is adjusted to be 0.15-0.30%, and the mass percentage of Ti is adjusted to be 0.035-0.050%.
In the converter steelmaking process, the end point temperature is 1660-1690 ℃, and the oxygen level is 5-20 ppm; the converter end point control is as follows: c: 0.022-0.040%, P is less than or equal to 0.009%; adding medium-carbon ferromanganese, aluminum particles, low-carbon ferrochromium and ferrovanadium in the tapping process, and controlling the weight percentage of each element of the converter ladle to be C: 0.30-0.32%, Mn: 1.20-1.30%, Cr: 0.18 to 0.25%, Als: 0.030-0.050%, V: 0.18-0.20%, and the temperature of the converter ladle is 1620-1640 ℃.
In the continuous casting process, the superheat degree of the tundish is 35-45 ℃, and the continuous casting drawing speed is 1.0-1.2 m/min.
In the hot rolling process, the heating temperature of a casting blank is 1250-1320 ℃, the heating time is 160-240 min, the inlet temperature of finish rolling is 1020-1100 ℃, the finishing temperature is 860-900 ℃, and the coiling temperature is 630-670 ℃.
In the cold rolling process, the cold rolling reduction is 55-70%.
The continuous galvanizing procedure comprises a preheating section, a heating 1 section, a heating 2 section and a soaking section; the dew point of the preheating section is-5 ℃ to +15 ℃, the dew point of the heating section 1 is-5 ℃ to +10 ℃, the dew point of the heating section 2 is-10 ℃ to-40 ℃, and the dew point of the soaking section is-10 ℃ to-40 ℃.
In the continuous galvanizing procedure, the soaking temperature is 770-860 ℃, and the soaking time is 100-200 s; slowly cooling to 660-720 ℃, and then quickly cooling to 420-450 ℃; the slow cooling rate is 10-20 ℃/s, and the fast cooling rate is 35-65 ℃/s; the galvanizing temperature is 458-462 ℃, and the galvanizing time is 5-15 s.
In the finishing process, the finishing elongation is 0.2-0.8%, and the rolling force is 5000-8000 kN.
The hot forming strip steel is processed into a standard tensile sample and is subjected to heat treatment, and the method comprises the following specific steps: heating to 870-950 ℃, preserving heat for 3-20 min for austenitizing, then water quenching to room temperature, and then tempering at 120-250 ℃ for 5-30 min. And (3) performing performance test on the sample after the heat treatment, wherein the tensile strength of the sample after quenching is more than or equal to 2000MPa, and the structure of the sample is full martensite.
The hot-formed strip steel with the zinc-based plating layer of 2000MPa and the production method thereof are also suitable for steel plates.
The design idea of the chemical components of the invention is as follows:
c: is the cheapest solid solution strengthening element and austenite stabilizing element, carbon can stabilize austenite phase by interstitial solid solution strengthening, increase austenite stability, and reduce Ac3The annealing temperature is reduced, and the energy consumption is reduced; the C atoms play a role in interstitial solid solution strengthening in the martensite, and the strengthening effect on the martensite is far greater than that on the martensite and replacement solid solution strengthening alloy elements, so that the carbon content is controlled to be 0.25-0.40%.
Mn: is an austenite stabilizing element and can effectively improve the hardenability of the austenite island, thereby reducing the cooling rate necessary for obtaining a dual-phase structure in the cooling process after the heating of the two-phase region. Mn can also reduce solid solution C in ferrite, promote C to transfer into austenite, improve austenite hardenability and purify a ferrite matrix, thereby improving the ductility of steel, and the content of Mn is controlled to be 1.10-1.70%.
Si: si can enlarge Fe-C phase diagram
A + gamma two-phase region; si solutionized into ferrite can affect the interaction of dislocations, increasing the work hardening rate and uniform elongation at a given strength level. Si and C, Mn, etc. increase the hardenability of steel, and more lath martensite is produced by quenching. Therefore, the Si content of the invention is controlled between 0.10 and 0.30 percent.
V: the V element is added into the steel by utilizing the following characteristics of V: (1) the precipitation strengthening and the fine grain strengthening (Hall-Petch formula) of the VC improve the strength and the plasticity; (2) the elements V and C are combined, so that the content of C in the martensite is reduced, the twin crystal martensite is inhibited, and the plasticity and the toughness are improved; (3) solid-solution V improves hardenability; (4) the V-containing steel contains irreversible hydrogen traps with high binding energy, and the hydrogen brittleness resistance is improved.
More than 0.15 percent of V and more than 0.25 percent of C are added into the components of the hot forming strip steel with 2000MPa zinc-based coating, and a precipitated phase VC or (V, Ti, Nb) C after continuous annealing is obtained, so that the tensile strength can be improved by more than 100MPa by uniform and fine second-phase particles, the size of the precipitated particles is 1-20 nm, and the average particle size is 4.5 nm. According to the precipitation strengthening mechanism, the precipitation strengthening reinforcing quantity can reach 240 MPa. The precipitation of VC or (V, Ti) C consumes carbon in austenite, reduces the carbon content thereof, and reduces the fraction of twin martensite formed in the martensite after the transformation thereof. Therefore, upon VC precipitation in the steel of the present invention, the toughness of martensite itself can be improved, and the strength thereof is reduced due to the reduction of the carbon content in the martensite, but the material strength is improved by VC precipitation strengthening and fine grain strengthening of prior austenite grains.
Adopt the produced beneficial effect of above-mentioned technical scheme to lie in: 1. the V element is added in the component design, so that the tensile strength is increased and the plasticity is improved simultaneously through the precipitation strengthening of VC; 2. according to the invention, through the change of the content of alloy elements and the adjustment of process parameters, the obtained product has ultrahigh strength and excellent welding and forming performances; 3. the strip steel produced by the invention has good corrosion resistance and lower cost than aluminum silicon products.
Detailed Description
The present invention will be described in further detail with reference to specific examples.
The invention relates to a production method of hot-formed strip steel with a zinc-based coating of 2000MPa, which comprises the working procedures of molten iron pretreatment, converter steelmaking, LF refining, RH refining, continuous casting, hot rolling, cold rolling, continuous galvanizing and finishing, and the specific process steps are as follows:
(1) a molten iron pretreatment process: and reducing the S content in the molten iron to be below 30ppm by adopting composite blowing particles Mg.
(2) A steel making process: a100 t top-bottom combined blown converter is adopted, and the end point control of the converter is as follows: c: 0.022-0.040%, P is less than or equal to 0.009%; the temperature is 1660-1690 ℃, and the oxygen level is as follows: 5-20 ppm, pushing off slag in the tapping process, adopting front and back double-shift slag pushing off mode to ensure the phosphorus content of the finished product, adding medium carbon ferromanganese, aluminum particles, low carbon ferrochromium and ferrovanadium in the tapping process, and controlling the content of each element in the converter bale as follows: c: 0.30-0.32%, Mn: 1.20-1.30%, Cr: 0.18 to 0.25%, Als: 0.030-0.050%, V: 0.18-0.20%, and the balance of iron and inevitable impurities. The temperature of the converter ladle is 1620-1640 ℃.
(3) An LF refining procedure: lime and fluorite are adopted for slagging, the contents of C, Cr, Mn, V, Als and the like are adjusted, electrodes are adopted for heating molten steel, and the LF outbound temperature is 1630-1665 ℃.
(4) RH refining process: fine adjustment is carried out on Mn, Als, B and Ti, Ti alloying is carried out, molten steel components are adjusted to a target range, and the outlet temperature is 1575-1610 ℃.
(5) And (3) continuous casting process: the superheat degree of the tundish is 35-45 ℃, and the continuous casting drawing speed is 1.0-1.2 m/min.
(6) A hot rolling procedure: the heating temperature of the casting blank is 1250-1320 ℃, the heating time is 160-240 min, the inlet temperature of finish rolling is 1020-1100 ℃, the finish rolling temperature is 860-900 ℃, and the coiling temperature is 630-670 ℃.
(7) A cold rolling procedure: and the cold rolling reduction rate is 55-70%.
(8) A continuous galvanizing procedure: comprises a preheating section, a heating section 1, a heating section 2 and a soaking section; the dew point of the preheating section is-5 ℃ to +15 ℃, the dew point of the heating section 1 is-5 ℃ to +10 ℃, the dew point of the heating section 2 is-10 ℃ to-40 ℃, and the dew point of the soaking section is-10 ℃ to-40 ℃. The soaking temperature is 770-860 ℃, and the soaking time is 100-200 s; slowly cooling to 660-720 ℃, and then quickly cooling to 420-450 ℃; the slow cooling rate is 10-20 ℃/s, and the fast cooling rate is 35-65 ℃/s; the galvanizing temperature is 458-462 ℃, and the galvanizing time is 5-15 s.
(9) A finishing process: the finishing elongation is 0.2-0.8%, and the rolling force is 5000-8000 kN.
The control parameters of each production procedure of the examples 1 to 10 are shown in tables 1 to 3, and the chemical composition and the mass percentage content of the strip steel are shown in table 4.
Processing the strip steel into a standard tensile sample, and carrying out heat treatment, wherein the method comprises the following specific steps: heating to 870-950 ℃, preserving heat for 3-20 min for austenitizing, then water quenching to room temperature, and then tempering at 120-250 ℃ for 5-30 min. And (3) performing performance test on the sample after the heat treatment, wherein the tensile strength of the sample after quenching is more than or equal to 2000MPa, and the structure of the sample is full martensite.
The mechanical properties of the steel strips of examples 1-10 before and after quenching are shown in Table 5.
TABLE 1 molten iron pretreatment and steelmaking Process control parameters
TABLE 2 LF refining, RH refining, continuous casting, hot rolling, cold rolling and finishing process control parameters
TABLE 3 continuous galvanizing process control parameters
TABLE 4 chemical composition and mass% of the steel strips of examples 1 to 10
TABLE 5 mechanical properties before and after quenching of the steel strips of examples 1 to 10
Claims (10)
1. The hot forming strip steel with the zinc-based coating of 2000MPa is characterized in that a strip steel substrate comprises the following chemical components in percentage by mass: c: 0.25 to 0.40%, Mn: 1.10-1.70%, S is less than or equal to 0.012%, P is less than or equal to 0.020%, and Si: 0.1-0.3%, Als: 0.030-0.050%, Cr: 0.20-0.40%, B: 0.0010-0.0030%, Ti: 0.035-0.050%, V: 0.15-0.30%, N is less than or equal to 0.0030%, and the balance is iron and inevitable impurities.
2. The hot-formed steel strip with a zinc-based coating of 2000MPa level as claimed in claim 1, wherein the tensile strength of the steel strip is not greater than 1000MPa, and after heat treatment, the tensile strength is not less than 2000 MPa.
3. The production method of hot-formed strip steel with 2000 MPa-level zinc-based coating according to claim 1 or 2, characterized in that the production method comprises the working procedures of molten iron pretreatment, converter steelmaking, LF refining, RH refining, continuous casting, hot rolling, cold rolling, continuous galvanizing and finishing;
in the RH refining process, V and Ti are added, the mass percentage of V is adjusted to be 0.15-0.30%, and the mass percentage of Ti is adjusted to be 0.035-0.050%.
4. The production method of hot-formed strip steel with a zinc-based plating layer of 2000MPa according to claim 3, characterized in that in the converter steelmaking process, the end temperature is 1660-1690 ℃, and the oxygen level is 5-20 ppm; the converter end point control is as follows: c: 0.022-0.040%, P is less than or equal to 0.009%; adding medium-carbon ferromanganese, aluminum particles, low-carbon ferrochromium and ferrovanadium in the tapping process, and controlling the weight percentage of each element of the converter ladle to be C: 0.30-0.32%, Mn: 1.20-1.30%, Cr: 0.18 to 0.25%, Als: 0.030-0.050%, V: 0.18-0.20%, and the temperature of the converter ladle is 1620-1640 ℃.
5. The production method of the hot-formed strip steel with the zinc-based coating of 2000MPa according to claim 4, characterized in that in the continuous casting process, the superheat degree of the tundish is 35-45 ℃, and the continuous casting drawing speed is 1.0-1.2 m/min.
6. The production method of the hot-formed strip steel with the zinc-based coating of 2000MPa according to claim 5, wherein in the hot rolling process, the casting blank heating temperature is 1250-1320 ℃, the heating time is 160-240 min, the finish rolling inlet temperature is 1020-1100 ℃, the finish rolling temperature is 860-900 ℃, and the coiling temperature is 630-670 ℃.
7. The production method of hot-formed strip steel with a zinc-based plating layer of 2000MPa according to claim 6, wherein the cold rolling process is performed at a cold rolling reduction of 55-70%.
8. The method for producing hot-formed strip steel with a zinc-based coating of 2000MPa according to claim 7, wherein the continuous galvanizing process comprises a preheating section, a heating 1 section, a heating 2 section and a soaking section; the dew point of the preheating section is-5 ℃ to +15 ℃, the dew point of the heating section 1 is-5 ℃ to +10 ℃, the dew point of the heating section 2 is-10 ℃ to-40 ℃, and the dew point of the soaking section is-10 ℃ to-40 ℃.
9. The production method of hot-formed strip steel with a zinc-based plating layer of 2000MPa according to any one of claims 3 to 8, characterized in that in the continuous galvanizing process, the soaking temperature is 770-860 ℃, and the soaking time is 100-200 s; slowly cooling to 660-720 ℃, and then quickly cooling to 420-450 ℃; the slow cooling rate is 10-20 ℃/s, and the fast cooling rate is 35-65 ℃/s; the galvanizing temperature is 458-462 ℃, and the galvanizing time is 5-15 s.
10. The method for producing hot-formed strip steel with a zinc-based plating layer of 2000MPa according to claim 9, wherein in the finishing step, the finishing elongation is 0.2-0.8%, and the rolling force is 5000-8000 kN.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202011321138.3A CN112779474A (en) | 2020-11-23 | 2020-11-23 | Hot forming strip steel with zinc-based coating at 2000MPa level and production method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN202011321138.3A CN112779474A (en) | 2020-11-23 | 2020-11-23 | Hot forming strip steel with zinc-based coating at 2000MPa level and production method thereof |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN112779474A true CN112779474A (en) | 2021-05-11 |
Family
ID=75750577
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN202011321138.3A Pending CN112779474A (en) | 2020-11-23 | 2020-11-23 | Hot forming strip steel with zinc-based coating at 2000MPa level and production method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN112779474A (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN113957350A (en) * | 2021-10-26 | 2022-01-21 | 江苏沙钢集团有限公司 | 2000 MPa-grade hot forming steel and production method thereof |
| CN115074623A (en) * | 2022-06-16 | 2022-09-20 | 唐山钢铁集团高强汽车板有限公司 | Hydrogen-induced cracking resistant galvanized hot stamping steel and production method thereof |
Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2006307325A (en) * | 2005-03-31 | 2006-11-09 | Jfe Steel Kk | Low yield ratio type high strength alloyed hot-dip galvanized steel sheet having excellent ductility and method for producing same |
| CN108374127A (en) * | 2018-04-28 | 2018-08-07 | 育材堂（苏州）材料科技有限公司 | Hot press-formed steel, hot press-formed technique and hot press-formed component |
| CN109371325A (en) * | 2018-11-30 | 2019-02-22 | 宝山钢铁股份有限公司 | A kind of electrogalvanized thermoforming steel plate that cold-bending property is excellent or steel band and its manufacturing method |
| CN109504930A (en) * | 2018-12-20 | 2019-03-22 | 唐山钢铁集团有限责任公司 | Tensile strength is greater than the hot-dip galvanizing sheet steel and its production method of 1300MPa |
| US20190309385A1 (en) * | 2016-07-08 | 2019-10-10 | Northeastern University | Steel Material For Hot Stamp Forming, Hot Stamp Forming Process And Hot Stamp Formed Member |
| CN110684932A (en) * | 2019-10-12 | 2020-01-14 | 唐山钢铁集团有限责任公司 | 1500 MPa-grade cold-formed strip steel and production method thereof |
-
2020
- 2020-11-23 CN CN202011321138.3A patent/CN112779474A/en active Pending
Patent Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2006307325A (en) * | 2005-03-31 | 2006-11-09 | Jfe Steel Kk | Low yield ratio type high strength alloyed hot-dip galvanized steel sheet having excellent ductility and method for producing same |
| US20190309385A1 (en) * | 2016-07-08 | 2019-10-10 | Northeastern University | Steel Material For Hot Stamp Forming, Hot Stamp Forming Process And Hot Stamp Formed Member |
| CN108374127A (en) * | 2018-04-28 | 2018-08-07 | 育材堂（苏州）材料科技有限公司 | Hot press-formed steel, hot press-formed technique and hot press-formed component |
| CN109371325A (en) * | 2018-11-30 | 2019-02-22 | 宝山钢铁股份有限公司 | A kind of electrogalvanized thermoforming steel plate that cold-bending property is excellent or steel band and its manufacturing method |
| CN109504930A (en) * | 2018-12-20 | 2019-03-22 | 唐山钢铁集团有限责任公司 | Tensile strength is greater than the hot-dip galvanizing sheet steel and its production method of 1300MPa |
| CN110684932A (en) * | 2019-10-12 | 2020-01-14 | 唐山钢铁集团有限责任公司 | 1500 MPa-grade cold-formed strip steel and production method thereof |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN113957350A (en) * | 2021-10-26 | 2022-01-21 | 江苏沙钢集团有限公司 | 2000 MPa-grade hot forming steel and production method thereof |
| CN115074623A (en) * | 2022-06-16 | 2022-09-20 | 唐山钢铁集团高强汽车板有限公司 | Hydrogen-induced cracking resistant galvanized hot stamping steel and production method thereof |
| CN115074623B (en) * | 2022-06-16 | 2023-08-25 | 唐山钢铁集团高强汽车板有限公司 | Zinc-plated hot stamping steel resistant to hydrogen induced cracking and production method thereof |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN110129668B (en) | 1000 MPa-grade alloying hot-dip galvanizing complex-phase steel and preparation method thereof | |
| CN112048681B (en) | 980 MPa-grade high-formability cold-rolled DH steel and preparation method thereof | |
| CN104928568A (en) | Ferrite low-density high-strength steel and manufacturing method thereof | |
| CN110172640B (en) | 500 MPa-grade high-work-hardening-rate hot-dip galvanized dual-phase steel plate and preparation method thereof | |
| CN104928569A (en) | 800MPa grade high-ductility low-density steel and manufacturing method thereof | |
| CN104561812A (en) | 1,000 MPa-level high-aluminum hot-dip-galvanized dual-phase steel and preparation method thereof | |
| CN106498307B (en) | The good high-strength and high ductility lightweight steel of 780MPa grades of cold-forming properties and its manufacturing method | |
| CN111172466B (en) | Plasticity-enhanced cold-rolled dual-phase steel with tensile strength of 590MPa and production method thereof | |
| CN111455285B (en) | Low-cost and easily-produced cold-rolled dual-phase steel with 980 MPa-grade tensile strength and production method thereof | |
| CN110592348A (en) | Ultra-low carbon cold rolled steel performance grading control method | |
| CN108396253A (en) | A kind of zinc-plated diphasic strip steel of the high intensity that buckling performance is excellent and its production method | |
| CN114525452B (en) | Hot-dip galvanized low-alloy high-strength steel with yield strength of 700Mpa level and preparation method thereof | |
| CN110747405B (en) | One-thousand-megapascal-grade cold-rolled bainite steel plate suitable for rolling and preparation method thereof | |
| CN112779474A (en) | Hot forming strip steel with zinc-based coating at 2000MPa level and production method thereof | |
| CN114045441B (en) | Reinforced plastic dual-phase steel for 800 MPa-level continuous annealing and preparation method thereof | |
| CN113416902B (en) | Low-cost thermal-forming axle housing steel plate with yield strength of 460MPa and preparation method thereof | |
| CN110684932B (en) | 1500 MPa-grade cold-formed strip steel and production method thereof | |
| CN114015932B (en) | Preparation method of 800 MPa-grade cold-rolled low-alloy high-strength steel with excellent hole expanding performance | |
| CN113604736B (en) | High-strength medium plate with yield strength of 800MPa and preparation method thereof | |
| CN114000068B (en) | Low-nitrogen ultrahigh-strength hot-rolled steel strip with thickness of 4-10mm and production method thereof | |
| CN114574674A (en) | Preparation method capable of simultaneously producing continuous annealing and galvanized DP780 dual-phase steel | |
| CN108998742B (en) | Steel plate with extremely low yield strength and manufacturing method thereof | |
| CN113061806A (en) | 1180 MPa-grade light high-strength steel and preparation method thereof | |
| CN113046644A (en) | 980 MPa-grade light high-strength steel and preparation method thereof | |
| CN115181894A (en) | 590 MPa-grade high-formability hot-galvanized dual-phase steel and rapid heat treatment hot galvanizing manufacturing method |
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 | ||
| RJ01 | Rejection of invention patent application after publication | ||
| RJ01 | Rejection of invention patent application after publication |
Application publication date: 20210511 |