CN110724876A - 1100 MPa-level hot-rolled high-strength steel plate and manufacturing method thereof - Google Patents
1100 MPa-level hot-rolled high-strength steel plate and manufacturing method thereof Download PDFInfo
- Publication number
- CN110724876A CN110724876A CN201911006179.0A CN201911006179A CN110724876A CN 110724876 A CN110724876 A CN 110724876A CN 201911006179 A CN201911006179 A CN 201911006179A CN 110724876 A CN110724876 A CN 110724876A
- Authority
- CN
- China
- Prior art keywords
- steel plate
- mpa
- equal
- strength steel
- strength
- 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
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
- 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
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
-
- 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
- C21D8/0247—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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- 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
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
-
- 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
- C21D2211/005—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
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)
- Heat Treatment Of Sheet Steel (AREA)
Abstract
The invention discloses a 1100 MPa-level hot-rolled high-strength steel plate which is characterized by comprising the following chemical components in percentage by weight: c: 0.10-0.20%; si: 0.80-1.50%; mn: 1.20-2.0%; p: less than or equal to 0.015 percent; s: less than or equal to 0.008 percent; cr: 0.20-0.60%; nb: 0.010-0.040%, Ti: 0.010-0.040%; and Als: 0.020-0.060%; the balance of Fe and inevitable impurities; the microstructure of the 1100 MPa-grade hot-rolled high-strength steel plate is ferrite and martensite, wherein the volume fraction of the ferrite is 25-35%, the volume fraction of the martensite is 65-75%, the yield strength of the product is more than or equal to 650MPa, the tensile strength is more than or equal to 1100MPa, the yield ratio is less than or equal to 0.65, the elongation A50 is more than or equal to 16%, the cold bending performance is 180 degrees, and the D is 4a qualified, so that the high-strength hot-rolled high-strength steel plate has higher strength, lower yield ratio and good forming performance.
Description
Technical Field
The invention relates to the technical field of high-strength steel production processes, in particular to an 1100 MPa-level hot-rolled high-strength steel plate and a manufacturing method thereof.
Background
High-strength steel has been widely used in the fields of engineering machinery, automobiles, and the like as one of the most direct and effective means for reducing weight. Along with the rapid development of large-scale engineering machinery, high efficiency and light weight of automobiles, the demand of high-strength steel is gradually increased, and meanwhile, the requirement on the comprehensive performance of the high-strength steel is higher and higher, so that the high-strength steel is required to have higher strength, and the tensile strength is required to be not lower than 1100 MPa; and the alloy is required to have good forming performance and no crack when bent at 180 degrees.
According to the delivery state of products, the high-strength steel can be divided into hot-rolled high-strength steel and cold-rolled high-strength steel, wherein the hot-rolled high-strength steel is mainly used in the fields of engineering machinery, commercial vehicles and the like, and the tensile strength of the hot-rolled high-strength steel is mainly concentrated at 700-1100 MPa at present. The patents reported about 1100 MPa-level hot-rolled high-strength steel include 'a quenched and tempered high-strength steel with yield strength of 900-1000 MPa and a production method thereof' disclosed in patent CN 104532157A, 'a manufacturing method of 1100 MPa-level high-strength steel with yield strength' disclosed in patent CN 106498296A 'and' ultra-high-strength steel with yield strength of 1000MPa and low yield ratio 'and a preparation method thereof' disclosed in patent CN 108315671A, wherein the production process comprises hot rolling, quenching and tempering; the patent publication No. CN 102618800A discloses a steel plate with 1150MPa grade yield strength and a manufacturing method thereof, and the production process comprises hot rolling and tempering. On one hand, the chemical composition design concept is low C, low Si, high Mn, high Cr, high Mo and high Ni, and a proper amount of microalloy elements Nb, V, Ti and B are added, so that the chemical composition design is complex, the content of noble alloy elements is high, and the alloy cost is high; on the other hand, the production process flow of the product comprises hot rolling, quenching and tempering or hot rolling and tempering, a heat treatment process is needed, the process flow is long, the energy consumption is high, the structure is martensite or martensite and residual austenite, the yield ratio is high, the yield ratio is more than 0.80, the residual internal stress is large, and the cold bending forming performance is limited.
The above patents all realize the production of 1100 MPa-grade hot-rolled high-strength steel through hot rolling and heat treatment processes, so that the 1100 MPa-grade hot-rolled high-strength steel without the heat treatment process is developed, and the method has important significance for reducing the production cost of iron and steel enterprises, promoting the light weight of downstream engineering machinery and automobiles, saving energy, reducing emission and the like.
Disclosure of Invention
In order to solve the problems, the invention provides an 1100 MPa-grade hot-rolled high-strength steel plate and a manufacturing method thereof, a quenching and tempering heat treatment or tempering process is not needed, the tensile strength of the hot-rolled high-strength steel can reach 1100MPa through the optimization of reasonable alloying component design, smelting, continuous casting, heating, hot rolling, cooling and coiling processes, and the hot-rolled high-strength steel has good forming performance, and is mainly used for manufacturing structural thinning parts of engineering machinery, automobiles and the like.
The technical scheme of the invention is as follows:
the 1100 MPa-grade hot-rolled high-strength steel plate comprises the following chemical components in percentage by weight: c: 0.10-0.20%; si: 0.80-1.50%; mn: 1.20-2.0%; p: less than or equal to 0.015 percent; s: less than or equal to 0.008 percent; cr: 0.20-0.60%; nb: 0.010-0.040%, Ti: 0.010-0.040%; and Als: 0.020-0.060%; the balance of Fe and inevitable impurities.
Furthermore, the microstructure of the 1100 MPa-grade hot-rolled high-strength steel plate is ferrite and martensite, wherein the volume fraction of the ferrite is 25-35%, the volume fraction of the martensite is 65-75%, the yield strength of the product is more than or equal to 650MPa, the tensile strength is more than or equal to 1100MPa, the yield ratio is less than or equal to 0.65, and the elongation A is50Not less than 16%, cold bending performance of 180 deg. and D being 4 a.
A manufacturing method of 1100 MPa-level hot-rolled high-strength steel plates comprises the following steps:
1) smelting, refining and continuous casting;
2) heating, namely, heating the casting blank in a heating furnace;
3) rolling, wherein a two-stage rolling process is adopted;
4) and (3) cooling: three-stage controlled cooling process is adopted.
Further, in the step 2), the heating temperature is 1150-1200 ℃, and the heat preservation time is 1.5-2 h.
Further, in the step 3), the rough rolling accumulated reduction rate is more than or equal to 70 percent, and the finish rolling accumulated reduction rate is more than or equal to 80 percent; the initial rolling temperature of rough rolling is 1100-1150 ℃, and the final rolling temperature of finish rolling is 800-850 ℃.
Further, in the step 4), the rolled steel plate is cooled to 650-700 ℃ at a cooling speed of more than or equal to 50 ℃/s for air cooling, is cooled to 600-650 ℃ for air cooling for 6-10s, is cooled to less than or equal to 250 ℃ at a cooling speed of more than or equal to 100 ℃/s for coiling, and is air-cooled to room temperature after coiling.
The invention adds high content Si and Mn into the chemical components, combines with proper amount of Cr, Nb and Ti alloy elements, and strictly controls the content of P, S and other impurity elements.
C: 0.10-0.20%, wherein C is used as a basic element in the steel and plays a very important role in improving the strength of the steel, in order to obtain higher strength, the content of C must be ensured to be more than 0.10%, but the content of C cannot be higher than 0.20%, otherwise, a certain proportion of soft phase structure ferrite is difficult to obtain in the cooling process after hot rolling, and the plastic and forming performance of the steel is poor.
Si: 0.80-1.50%, and the addition of a proper amount of Si can not only achieve the effects of deoxidation and solid solution strengthening, increase the strength of steel, but also enlarge the process window of ferrite formation and promote the formation of ferrite. Relevant researches show that the effect of Si is shown when the content of Si reaches more than 0.80 percent, but the content of Si cannot be too high, and a large amount of red iron scales are easily generated on the surface of steel due to too high content of Si, so that the difficulty in removing the iron scales is increased, and the surface quality of a product is influenced.
Mn: 1.20-2.0%, Mn is used as a reinforcing element of the steel, the strength and the hardenability of the steel can be improved, the Mn content is controlled to be more than 1.20% in order to ensure the strength of the steel, but the Mn content cannot be too high, the possibility of casting blank segregation caused by the too high Mn content is obviously increased, ferrite with required quantity is not easily formed after rolling, and the forming performance of the steel is adversely affected.
Cr: 0.20-0.60%, Cr is used as a medium-strength carbide forming element, the hardenability of steel can be obviously improved, the supercooling capability of austenite is increased, the phase transformation of pearlite and ferrite is delayed, the phase transformation of bainite is delayed, a metastable austenite region between a ferrite transformation region and a bainite transformation region is obtained, and the cooling process window is expanded.
P, S as impurity elements, which have adverse effects on the plasticity, forming, toughness and other properties of steel, should be strictly controlled, the lower the content, the better, considering the production cost factor, and the actual production control P: less than or equal to 0.015 percent, S: less than or equal to 0.008 percent.
Nb: the steel is a strong carbon and nitrogen compound forming element, and the strength of the steel is improved mainly by refining grains; on one hand, the solid-dissolved Nb plays a role in solute dragging on the growth of austenite grains and plays a role in preventing the growth of the austenite grains; on the other hand, undissolved Nb (C, N) formed by Nb and C, N can obviously pin austenite grain boundaries, refine austenite grains, and refine the structure of a final product, thereby being beneficial to improving the strength and the cold-bending forming performance of the product.
Ti: 0.010-0.040%, and the Ti mainly plays three roles in the steel, namely, the austenite grains are refined, the strength of the steel is improved, the Nb is matched with the steel, and the optimal refining effect is played on the finally transformed ferrite and martensite structures; secondly, the nitrogen-fixing agent is combined with N element to form TiN, thereby playing a role in nitrogen fixation; thirdly, the welding performance of the material is improved, and TiN formed by combining Ti and N has obvious inhibiting effect on austenite grain coarsening in the welding process.
And Als: 0.020-0.060%, wherein Als mainly plays a role in deoxidation in the steel, but Als cannot be too high, and the too high Als can react with N in the steel to precipitate coarse AlN particles, so that the grain refining effect is not facilitated.
According to the invention, on the design of a hot rolling process, the heating temperature is controlled to 1150-1200 ℃, and the main purpose is to prevent the heating temperature from being too high, and Si reacts with FeO under the high-temperature condition to generate fayalite Fe2SiO4The fayalite can nail-roll the iron scale, so that the adhesiveness of the fayalite with a matrix is increased, the iron scale is difficult to remove, red rust generated on the surface of the strip steel is increased, and the surface quality of the strip steel is influenced; the finishing temperature is controlled to be 800-850 ℃, and the lower finishing temperature is beneficial to refining the original austenite grain size and rapidly entering a ferrite transformation area after finishing rolling to obtain a ferrite structure.
After rolling, a three-section type cooling control process is adopted: the first stage cooling speed is controlled to be more than 50 ℃/s, the final cooling temperature is controlled to be 650-700 ℃, and the purpose is to enable the material to rapidly enter a ferrite phase transformation area and refine ferrite grains; the second stage air cooling time is controlled to be 6-10s, and the final cooling temperature is controlled to be 600-650 ℃, so as to obtain a ferrite structure with a certain proportion; the third stage cooling rate is controlled to be more than 100 ℃/s, and the coiling temperature is controlled to be less than 250 ℃, so that the untransformed austenite structure is rapidly transformed into a martensite structure, and the steel material finally obtains a ferrite and martensite structure.
The hot rolled steel plate produced by the method has a microstructure of ferrite and martensite, wherein the volume fraction of the ferrite is 25-35%, the volume fraction of the martensite is 65-75%, the yield strength of the product is more than or equal to 650MPa, the tensile strength is more than or equal to 1100MPa, the yield ratio is less than or equal to 0.65, and the elongation A is50Not less than 16 percent, cold bending performance of 180 degrees, qualified D-4 a, higher strength, lower yield ratio and good formabilityCan be used.
Drawings
FIG. 1 is a metallographic structure diagram of a 1100MPa hot-rolled high-strength steel plate produced by the present invention.
Detailed Description
The technical solution of the present invention will be described below by way of specific examples.
The chemical components and the weight percentage content provided by the invention are as follows: 0.10-0.20%; si: 0.80-1.50%; mn: 1.20-2.0%; p: less than or equal to 0.015 percent; s: less than or equal to 0.008 percent; cr: 0.20-0.60%; nb: 0.010-0.040%, Ti: 0.010-0.040%; and Als: 0.020-0.060%; the balance of Fe and inevitable impurities.
The manufacturing method of the 1100 MPa-level hot-rolled high-strength steel plate comprises converter smelting, refining, continuous casting, heating, rolling, cooling and coiling processes.
As shown in figure 1, the metallographic structure of the 1100 MPa-grade hot-rolled high-strength steel plate produced by the invention is ferrite and martensite, wherein the volume fraction of the ferrite is 25-35%, and the volume fraction of the martensite is 65-75%.
The chemical composition of each example is shown in table 1, the rolling process parameters are shown in table 2, and the mechanical properties are shown in table 3.
Table 1 measured chemical composition of examples (mass%,% by weight)
| Numbering | C | Si | Mn | P | S | Cr | Nb | Ti | Als |
| Example 1 | 0.16 | 1.45 | 1.58 | 0.013 | 0.006 | 0.35 | 0.015 | 0.025 | 0.025 |
| Example 2 | 0.19 | 0.90 | 1.75 | 0.012 | 0.005 | 0.28 | 0.020 | 0.015 | 0.036 |
| Example 3 | 0.15 | 1.25 | 1.82 | 0.009 | 0.004 | 0.45 | 0.030 | 0.026 | 0.055 |
| Example 4 | 0.13 | 1.35 | 2.40 | 0.008 | 0.006 | 0.50 | 0.035 | 0.030 | 0.045 |
TABLE 2 Main Rolling Process parameters of the examples
TABLE 3 mechanical properties of the examples
It can be seen from the above examples that the hot-rolled steel plate with high strength, low yield ratio and good formability can be obtained by selecting the raw materials according to the given chemical component weight percentage of the 1100 MPa-grade hot-rolled high-strength steel plate of the invention and then producing the hot-rolled high-strength steel plate according to the manufacturing method provided by the invention, and the hot-rolled high-strength steel is mainly used for manufacturing structural thinning parts of engineering machinery, automobiles and the like.
Claims (6)
1. The 1100 MPa-level hot-rolled high-strength steel plate is characterized by comprising the following chemical components in percentage by weight: c: 0.10-0.20%; si: 0.80-1.50%; mn: 1.20-2.0%; p: less than or equal to 0.015 percent; s: less than or equal to 0.008 percent; cr: 0.20-0.60%; nb: 0.010-0.040%, Ti: 0.010-0.040%; and Als: 0.020-0.060%; the balance of Fe and inevitable impurities.
2. The 1100 MPa-grade hot-rolled high-strength steel plate as claimed in claim 1, is characterized in that the microstructure of the 1100 MPa-grade hot-rolled high-strength steel plate is ferrite and martensite, wherein the volume fraction of ferrite is 25-35%, the volume fraction of martensite is 65-75%, the yield strength of a product is more than or equal to 650MPa, the tensile strength is more than or equal to 1100MPa, the yield ratio is less than or equal to 0.65, the elongation A50 is more than or equal to 16%, the cold bending performance is 180%, and D is 4a qualified.
3. The method for manufacturing a 1100 MPa-grade hot-rolled high-strength steel plate according to any one of claims 1 to 2, comprising the steps of:
1) smelting, refining and continuous casting;
2) heating, namely, heating the casting blank in a heating furnace;
3) rolling, wherein a two-stage rolling process is adopted;
4) and (3) cooling: three-stage controlled cooling process is adopted.
4. The method for manufacturing the 1100 MPa-grade hot-rolled high-strength steel plate according to claim 3, wherein in the step 2), the heating temperature is 1150-1200 ℃, and the holding time is 1.5-2 h.
5. The method for manufacturing the 1100 MPa-grade hot-rolled high-strength steel plate according to claim 3, wherein in the step 3), the rough rolling cumulative reduction rate is not less than 70%, and the finish rolling cumulative reduction rate is not less than 80%; the initial rolling temperature of rough rolling is 1100-1150 ℃, and the final rolling temperature of finish rolling is 800-850 ℃.
6. The method for manufacturing the 1100 MPa-level hot-rolled high-strength steel plate as claimed in claim 3, wherein in the step 4), the rolled steel plate is cooled to 650-700 ℃ at a cooling speed of not less than 50 ℃/s for air cooling, is cooled to 600-650 ℃ for air cooling for 6-10s, is cooled to not more than 250 ℃ at a cooling speed of not less than 100 ℃/s for coiling, and is air-cooled to room temperature after coiling.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201911006179.0A CN110724876A (en) | 2019-10-22 | 2019-10-22 | 1100 MPa-level hot-rolled high-strength steel plate and manufacturing method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN201911006179.0A CN110724876A (en) | 2019-10-22 | 2019-10-22 | 1100 MPa-level hot-rolled high-strength steel plate and manufacturing method thereof |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN110724876A true CN110724876A (en) | 2020-01-24 |
Family
ID=69222768
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201911006179.0A Pending CN110724876A (en) | 2019-10-22 | 2019-10-22 | 1100 MPa-level hot-rolled high-strength steel plate and manufacturing method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN110724876A (en) |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN113215490A (en) * | 2021-05-07 | 2021-08-06 | 马鞍山钢铁股份有限公司 | Thin HB 300-grade wear-resistant steel plate and manufacturing method thereof |
| CN114250413A (en) * | 2021-11-24 | 2022-03-29 | 邯郸钢铁集团有限责任公司 | Tempering-free hot-rolled Gepa-grade high-strength steel and production method thereof |
| 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 |
| CN116162860A (en) * | 2023-03-22 | 2023-05-26 | 鞍钢股份有限公司 | Ultrahigh-strength hot rolled Q & P steel with good surface quality and production method thereof |
| CN116240462A (en) * | 2023-03-22 | 2023-06-09 | 鞍钢股份有限公司 | 800 MPa-grade hot-rolled pickled Q & P steel and production method thereof |
Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN105803334A (en) * | 2016-05-06 | 2016-07-27 | 武汉钢铁股份有限公司 | Hot-rolled complex phase steel with tensile strength of 700 MPa and production method thereof |
| CN110331326A (en) * | 2019-07-30 | 2019-10-15 | 马鞍山钢铁股份有限公司 | High-strength dual phase sheet steel of a kind of 1000MPa grades of thin gauge hot rolling and preparation method thereof |
-
2019
- 2019-10-22 CN CN201911006179.0A patent/CN110724876A/en active Pending
Patent Citations (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN105803334A (en) * | 2016-05-06 | 2016-07-27 | 武汉钢铁股份有限公司 | Hot-rolled complex phase steel with tensile strength of 700 MPa and production method thereof |
| CN110331326A (en) * | 2019-07-30 | 2019-10-15 | 马鞍山钢铁股份有限公司 | High-strength dual phase sheet steel of a kind of 1000MPa grades of thin gauge hot rolling and preparation method thereof |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN113215490A (en) * | 2021-05-07 | 2021-08-06 | 马鞍山钢铁股份有限公司 | Thin HB 300-grade wear-resistant steel plate and manufacturing method thereof |
| CN114250413A (en) * | 2021-11-24 | 2022-03-29 | 邯郸钢铁集团有限责任公司 | Tempering-free hot-rolled Gepa-grade high-strength steel and production method thereof |
| 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 |
| CN116162860A (en) * | 2023-03-22 | 2023-05-26 | 鞍钢股份有限公司 | Ultrahigh-strength hot rolled Q & P steel with good surface quality and production method thereof |
| CN116240462A (en) * | 2023-03-22 | 2023-06-09 | 鞍钢股份有限公司 | 800 MPa-grade hot-rolled pickled Q & P steel and production method thereof |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| JP7238129B2 (en) | 980 MPa class cold-rolled steel sheet with high hole expansion ratio and high elongation and method for producing the same | |
| CN110724876A (en) | 1100 MPa-level hot-rolled high-strength steel plate and manufacturing method thereof | |
| CN112095046B (en) | Ultrahigh-strength cold-rolled DH1180 steel and preparation method thereof | |
| CN113549823B (en) | 900 MPa-grade hot-rolled and pickled multiphase steel with low yield ratio and high hole expansion rate and production method thereof | |
| CN110578095A (en) | 1200 MPa-level hot-rolled ultrahigh-strength steel plate and manufacturing method thereof | |
| CN113388779B (en) | 1.5 GPa-grade ultrahigh-strength high-plasticity high-hole-expansion DH steel plate and preparation method thereof | |
| CN110629003A (en) | Heat treatment-free hot continuous rolling ultrahigh-strength steel plate and manufacturing method thereof | |
| CN113416890A (en) | High-hole-expansion high-plasticity 980 MPa-grade cold-rolled continuous annealing steel plate and preparation method thereof | |
| CN108396225B (en) | A kind of 700MPa grades of titaniferous hot rolling biphase plate and its manufacturing method | |
| CN111118403B (en) | Ti microalloyed high-strength high-toughness bainite non-quenched and tempered steel and forging and cooling control process and production process thereof | |
| CN101633996B (en) | 700MPa-grade high strength and high toughness hardened and tempered steel plate with low cost and manufacturing method thereof | |
| CN103320701B (en) | A kind of ferrite-bainite AHSS plate and manufacture method thereof | |
| CN111979490A (en) | High-ductility and high-formability cold-rolled DH590 steel and production method thereof | |
| CN110643800A (en) | 1200 MPa-level hot-rolled high-strength dual-phase steel plate and manufacturing method thereof | |
| CN110331326A (en) | High-strength dual phase sheet steel of a kind of 1000MPa grades of thin gauge hot rolling and preparation method thereof | |
| CN104278194A (en) | Automobile cold-rolled steel plate with high strength and high plasticity and production method thereof | |
| CN112210727B (en) | Hot-rolled complex phase steel with tensile strength of 850MPa and production method thereof | |
| CN101161843A (en) | Method for improving utilization ratio of V-N micro-alloying high-strength steel vanadium alloy | |
| CN114411059A (en) | Bridge steel and manufacturing method thereof | |
| CN102260824A (en) | Hot-rolled steel plate with yield strength of 550 MPa for hot forming and manufacturing method thereof | |
| CN105063311A (en) | Processing method for improving surface quality of TRIP steel | |
| CN114293098A (en) | High-strength and high-toughness bainite non-quenched and tempered steel suitable for large-specification forge piece | |
| CN113481436A (en) | 800 MPa-grade hot-rolled complex phase steel and production method thereof | |
| CN108277434B (en) | Precipitation strengthening ferritic steel with yield strength of 900MPa and production method thereof | |
| CN113584378A (en) | HB400 grade hot continuous rolling wear-resistant steel containing ferrite 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 | ||
| RJ01 | Rejection of invention patent application after publication |
Application publication date: 20200124 |
|
| RJ01 | Rejection of invention patent application after publication |