CN103305762A - Cold-rolled dual-phase sheet steel with 400MPa-level tensile strength and preparation method thereof - Google Patents
Cold-rolled dual-phase sheet steel with 400MPa-level tensile strength and preparation method thereof Download PDFInfo
- Publication number
- CN103305762A CN103305762A CN2013102510451A CN201310251045A CN103305762A CN 103305762 A CN103305762 A CN 103305762A CN 2013102510451 A CN2013102510451 A CN 2013102510451A CN 201310251045 A CN201310251045 A CN 201310251045A CN 103305762 A CN103305762 A CN 103305762A
- Authority
- CN
- China
- Prior art keywords
- cold
- sheet steel
- phase sheet
- dual phase
- steel
- 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
Abstract
The invention discloses a cold-rolled high-strength dual-phase sheet steel with 400MPa-level tensile strength for a car and a preparation method thereof, and belongs to the field of steel materials. The double-phase sheet steel adopts a ferrite-martensite dual-phase structure serving as the main structure and contains 4 to 9% of martensite and comprises the following chemical components by mass percent: 0.01 to 0.05% of C, 0.1 to 0.4% of Si, 1.2 to 1.6% of Mn, 0.1 to 0.4% of Cr, 0.02 to 0.05% of Als, not greater than 0.005% of N, not greater than 0.02% of P, not greater than 0.01% of S, and the balance of Fe and inevitable residual impurity elements. The preparation method comprises the steps of hot rolling, acid pickling, cold rolling and heat treating. The produced cold-rolled double-phase sheet steel has the yield strength of 200 to 250MPa, tensile strength of 400 to 450MPa and percentage of elongation of 30 to 35%.
Description
Technical field
The invention belongs to field of iron and steel, is a kind of automobile cold-rolled dual phase steel, particularly a kind of tensile strength 400MPa level cold-rolled biphase steel plate and preparation method thereof.
Background technology
Alleviate tare by improving armor plate strength, reach energy-saving and cost-reducing, reducing environmental pollution is the important topic of current automotive industry research.Since dual phase steel have low yield tensile ratio, high initial manufacture cementation index, ageing resistance stability better, higher collision energy absorption capability, high baking hardening value, excellent welding property, good intensity and the excellent comprehensive performances such as coupling of extension property, in the ULSAB project, application facet at body in white has represented wide prospect, it accounts for about 80% of whole tare, is the development trend of automotive sheet in future.
At present, people mainly concentrate on high intensity levels more than the 500MPa level to the research work of dual phase steel.But owing to be subjected to the restriction of high-strength steel stamping resilience and pressing equipment tonnage, ultrahigh-strength steel also is not widely used in automobile industry at present.For the high-strength steel about common structural part and a spot of Abdeckteil widespread use 400MPa rank.Its steel grade classification comprises common C-Mn structure iron, Hi-Stren steel, baking hardened steel, adds phosphor intensified gapless atomic steel etc., however the C-Mn structure iron has defectives such as work hardening rate is low, aging resistance is poor, plasticity is poor, the baking hardening value is low; Hi-Stren steel makes that the mechanical property fluctuation range is bigger owing to be subjected to hot rolling, influence cold rolling, each operation of annealing bigger, has defectives such as work hardening rate is low, aging resistance is poor, the baking hardening value is low, plasticity difference simultaneously; Baking hardened steel has that aging resistance is poor, being shaped occurs defectives such as tension strain trace and stamping cracking easily; Add phosphor intensified gapless atomic steel because crystal boundary gap-free atom and P to influences such as grain boundary segregations, have weakened the crystal boundary bonding force, be easy to generate defectives such as secondary processing brittleness.Therefore in order to satisfy automobile industry to the active demand of 400MPa grade high-strength steel, other cold-rolled biphase steel of 400MPa level that Development and Production has excellent over-all properties is quite necessary.For 400MPa rank cold-rolled biphase steel, except Chinese patent CN102286696A and CN102002639A have related, do not see other relevant report data.
The Chinese invention patent of Granted publication CN102286696A, a kind of preparation method of super deep-draw dual phase steel of high-ductility strain ratio is disclosed, the tension rank of its cold-rolled biphase steel is 400～500MPa level, wherein the chemical component weight per-cent of steel is: C:0.01～0.05%, Mn:1.0～2.0%, P:0.01～0.06%, S≤0.015%, Al:0.2～0.8%, N≤0.003%, Cr:0.1～0.5%, Mo:0.3～0.8%, all the other are Fe and impurity element.Its hot rolling finishing temperature is that 850～950 ℃, coiling temperature are that 680～750 ℃, continuous annealing temperature are that 800～850 ℃, annealing insulation back are chilled to room temperature soon with the speed of 30～60 ℃/s.This patent of invention has been added precious metal alloys elements such as more Al, Cr, Mo, has increased production cost; Coiling temperature is higher simultaneously, and hot rolling iron scale is thicker, has improved the pickling difficulty relatively.
The Chinese invention patent of application publication number CN102002639A, dual phase sheet steel and manufacture method thereof are disclosed, the tension rank of its cold-rolled biphase steel is 440～590MPa level, this dual phase sheet steel comprises: C:0.05～0.10%, Si:0.03～0.50%, Mn:1.50～2.00%, P≤0.03%, S≤0.003%, Al:0.03～0.50%, Cr:0.1～0.2%, Mo:0.1～0.2%, Nb:0.02～0.04%, B:0～0.005, N:0～0.01%, all the other are that Fe and other must be formed by impurity.Annealing temperature is 780～820 ℃, and adopts hot-dip galvanizing technique production.More precious metal element Al, Mo, Nb etc. have been added in this invention, have increased production cost; Simultaneously C content is higher, and plasticity and the welding property of steel had disadvantageous effect; And from the performance analysis that obtains, its yield tensile ratio is higher, and is unfavorable to drawing.This invention annealing temperature is higher relatively in addition, thereby two-phase region when annealing austenite content increases, and the austenitic alloy constituent content reduces, and has reduced austenitic hardening capacity, makes austenite that perlite or bainite transformation take place easily.
Summary of the invention
The objective of the invention is to overcome the deficiencies in the prior art a kind of 400MPa level cold-rolled biphase steel and preparation method thereof is provided.This dual phase steel tensile strength is greater than 400MPa, and yield tensile ratio is low, work hardening value height, initial manufacture hardening rate height, ageing resistance good stability, intensity and extension matches, punching performance is good, can be used for automobile structure and Abdeckteil etc.
For dual phase steel, its tensile strength depends primarily on the C content in the fraction of martensite volume and martensite in the tissue, and for 400MPa level cold-rolled biphase steel, the composition design is most important with the coupling of annealing process.When alloying element content is higher, the tensile strength of final finished will substantially exceed 400MPa; When alloying element content is low, in process of cooling, can't obtain martensitic stucture again, this also is the low strength rank dual phase steel one of the main reasons difficult than the production of 600～800MPa rank dual phase steel.Therefore under the situation than low-alloy content (especially C content), by the coupling of annealing process, guarantee that it is main contents of the present invention that austenite has excellent hardening capacity.
In order to solve above technical problem, the present invention is achieved by the following technical programs.
The automobile cold-rolled dual phase sheet steel of tensile strength 400MPa level of the present invention, described dual phase sheet steel chemical ingredients mass percent is: C:0.01～0.05%, Si:0.1～0.4%, Mn:1.2～1.6%, Cr:0.1～0.4%, Als:0.02～0.05%, N≤0.005%, P≤0.02%, S≤0.01%, and all the other are Fe and inevitable remaining impurity element; Described dual phase sheet steel has ferrite and martensite duplex structure, and wherein martensitic percent by volume is 4～9%; Described dual phase sheet steel yield strength is 200～250MPa, and tensile strength is 400～450MPa, and unit elongation is 30～35%.
Further, described dual phase sheet steel chemical ingredients mass percent is: C:0.02～0.04%, Si:0.2～0.3%, Mn:1.4～1.6%, Cr:0.2～0.3%, Als:0.02～0.04%, N≤0.003%, P≤0.012%, S≤0.005%, all the other are Fe and inevitable remaining impurity element.
The preparation method of the automobile cold-rolled dual phase sheet steel of tensile strength 400MPa level of the present invention, at first smelt, and refining in the heating ladle, cast slab by continuous casting then, hot rolling routinely again, the pickling cold continuous rolling, heat-treat technology at last, described thermal treatment process adopts continuous annealing process, it heats successively, insulation, slow cooling, cold soon, overaging and naturally cooling step, specifically: be heated to 740～800 ℃ of annealing temperatures earlier, insulation 90～120S, then with speed slow cooling to 640～680 of 5～8 ℃/s ℃, be chilled to 260～320 ℃ soon with the speed greater than 40 ℃/s then and carry out the overaging processing, the overaging treatment time is 400～600s, naturally cools to room temperature at last.
Further, described annealing temperature is 750～770 ℃, and fast cold beginning temperature is 650～670 ℃, and fast cold but speed is 40～60 ℃/s, and the overaging treatment temp is 280～320 ℃.
The reasons are as follows of alloy of the present invention and annealing process design:
C:0.01～0.05% is preferably 0.02～0.04%.The most effective strengthening element is to form martensitic principal element, can improve the hardening capacity of steel, and its content determines martensitic intensity and volume fraction; C content is low excessively, can't obtain martensitic stucture; The C too high levels, the martensitic intensity that forms and volume fraction increase, cause final tensile strength to surpass 450MPa, C content increases simultaneously, its plasticity and welding property will descend.
Si:0.1～0.4% is preferably 0.2～0.3%.Si is ferrite solution strengthening element, improves the intensity of ferrite matrix strongly, promotes carbon enrichment in the austenite, suppresses the forming core of carbide, has " purifications " to act on to ferrite, helps to improve the ductility of dual phase steel.Si content is low excessively, and is less to inhibition and ferritic " purification " effect of carbide, forms carbide and pearlitic structure easily; The Si too high levels, strengthening effect is stronger, makes yield tensile ratio increase, and this element influences surface quality and the phosphorus characteristic of steel plate easily at surface enrichment formation oxide compound simultaneously.
Mn:1.2～1.6% is preferably 1.4～1.6%.Mn belongs to austenite stabilizer element, can improve the hardening capacity of steel, improves the work hardening ability of steel, and can significantly postpone perlite and bainite transformation.Mn content is crossed when hanging down and is caused perlite and bainite transformation easily, is difficult to form martensite in the tissue; During the Mn too high levels, when suppressing perlitic transformation, also can postpone ferritic separating out, make that martensite content is too high in the steel, Mn also easily forms oxide compound and influences subsequently coating performance at surface enrichment simultaneously.
Cr:0.1～0.4% is preferably 0.2～0.3%.Cr is middle strong carbide forming element, can postpone perlite and bainite transformation strongly, austenitic hardening capacity in the time of can improving critical annealing; In addition, Cr can promote that C spreads to austenite, reduces ferritic yield strength.Cr content is low excessively, and its effect is less; But during too high levels, ductility, the plasticity of steel will be destroyed.
Als:0.02～0.05% is preferably 0.02～0.04%.The major function of Al in dual phase steel is reductor, should not be low excessively, but can influence continuous casting production when too high, and form inclusion and influence plasticity.
P :≤0.02%, be preferably≤0.012%.P is a kind of inexpensive solution strengthening element, has to suppress the effect that carbide forms, for dual phase steel, the certain an amount of intensity of P and the formation of duplex structure are useful, but influence weldability when too high, and produce cold shortness to the crystal boundary enrichment, the drawing performance of steel is descended.
S :≤0.01%, be preferably≤0.005%.S easily forms MnS in steel, slivering zonal arrangement after shaping, thus influence the press formability of steel, so more few more good.
N :≤0.005%, be preferably≤0.003%.N causes the ageing of steel easily, and therefore N is more few more good in dual phase steel.
Annealing temperature: 740～800 ℃, be preferably 750～770 ℃.Annealing temperature is in order to obtain a certain amount of austenite structure, and makes the alloying element enrichment in the austenite in the ferrite, improves austenitic stability.Annealing temperature is low excessively, and carbide is dissolving fully not, and austenite content is very few, thereby the martensitic stucture that obtains is less, and intensity is lower; Annealing temperature is too high, and austenite content is too much, and austenitic stability reduces, and easily changes perlite and bainite structure in phase transition process subsequently into.
Fast cold beginning temperature: 640～680 ℃, be preferably 650～670 ℃.Determining for after controlling two-phase region annealing of fast cold beginning temperature, making the part austenitic transformation in the slow cooling section with certain slow speed of cooling is ferritic structure, and make further enrichment in the austenite of alloying element in the ferrite, thereby improve austenitic stability.Fast cold beginning temperature is too high, and stabilization of austenite descends, and fast cold beginning temperature is low excessively, is slowly easily changing pearlitic structure in the process of cooling.
Fast cooling rate rate: 〉=40 ℃/s, be preferably 40～60 ℃/s.The definite of fast cooling rate rate must make it surpass critical cooling rate, and making remaining austenitic transformation is martensitic stucture.Fast cooling rate rate is too high, and the band steel is easy to generate flatness defect; Fast cooling rate rate is low excessively, and bainite transformation easily takes place austenite.
Overaging temperature: 260～320 ℃, be preferably 280～320 ℃.Overaging is for martensite is carried out low-temperaturetempering, and the internal stress of organizing when making phase transformation in the steel discharges, and improves the ductility of steel.The overaging temperature is low excessively, and the ductility of steel is relatively poor, and the overaging temperature is too high, thereby martensite decomposes easily and makes stress-strain(ed) curve yield point elongation occur, worsens the plasticity of steel.
Beneficial effect of the present invention:
The automobile cold-rolled dual phase steel that the present invention produces, yield strength are 200～250MPa, and tensile strength is 400～450MPa, and unit elongation is 30～35%.Compare with low-alloy high-strength steel, stable performance, little to process sensitivity; Compare with low-alloy high-strength steel with common CMn structure iron, yield tensile ratio is low, the work hardening rate height, and baking hardening value height, ductility is good, and press formability is good; Compare with the IF steel, anti-secondary processing brittleness is good; Compare the wrinkling premium properties that waits of piece surface after ageing resistance good stability, no yield extension have been avoided being shaped with the BH steel with common CMn structure iron.Because the designed dual phase steel of the present invention adopts cheap CSiMn composition design, add a spot of relatively cheap Metal Cr on this basis, to improve the hardening capacity of steel, not extra precious metal Mo, the V etc. of adding; And in smelting process, need not to handle as the long vacuum outgas of IF steel, so further reduced production cost.
Description of drawings
Fig. 1 is cold-rolled biphase steel annealing process schematic flow sheet of the present invention.
Fig. 2 is microstructure picture behind the cold-rolled biphase steel annealing process of the present invention.
Embodiment
The present invention is described further below in conjunction with accompanying drawing.
As shown in Figure 1, annealing process flow process of the present invention comprises six stages such as heating zone, holding-zone, slow cooling section, fast cold period, overaging section and naturally cooling section; In heating zone steel plate is quickly heated up to two-phase region, obtain a certain amount of austenite; In the insulating process of holding-zone, carbide further dissolves, and alloying element enrichment in the austenite, improves austenitic stability; Be ferrite at slow cooling section part austenitic transformation, further enrichment in the austenite that does not change of alloying element; Be martensitic stucture at fast cold section austenitic transformation; Martensite obtains low-temperaturetempering in the overaging process, and the internal stress that phase transformation obtains obtains discharging, thereby improves the ductility of steel; Be chilled to room temperature at naturally cooling section steel plate by certain cooling rate.
As shown in Figure 2, the grey matrix is ferritic structure among the figure, and the tiny island of brilliant white is martensitic stucture.Adopting image processing software statistics martensite volume fraction is about 7%, is small and dispersed and is distributed in the ferrite matrix; The martensite that a certain amount of small and dispersed distributes can obtain excellent obdurability coupling, is conducive to further improve the forming property of steel.
The present invention will be further described below in conjunction with specific embodiment, but the present invention is not limited to following embodiment.
Embodiments of the invention chemical ingredients (mass percent) is as shown in table 1.
Table 1 chemical ingredients
| Numbering | C | Si | Mn | Cr | P | S | Als | N |
| DP1 | 0.027 | 0.28 | 1.56 | 0.30 | 0.013 | 0.004 | 0.032 | 0.0052 |
| DP2 | 0.032 | 0.26 | 1.47 | 0.28 | 0.016 | 0.005 | 0.036 | 0.0043 |
Smelt and forge in testing laboratory by table 1 chemical ingredients, forging stock is heated to 1200 ℃ goes into stove insulation 2 hours, carry out hot rolling at 450mm two roller hot rollss, the hot rolling final thickness is 4mm, hot rolling finishing temperature is 860 ℃, water-cooled to 630 ℃ is gone into stove insulation 1 hour, and the furnace cooling simulation is batched then.
Plate after the hot rolling is carried out pickling to remove scale on surface, carry out cold rollingly then, be cold-rolled to 1.2～1.5mm, draft is 60～70%.
Thermal treatment process adopts continuous annealing process, is heated to annealing temperature with the rate of heating of 5 ℃/s.Its concrete processing parameter is as shown in table 2.Table 3 is the mechanical property of specific embodiment.
Table 2 main technologic parameters
Table 3 mechanical property
Claims (4)
1. automobile cold-rolled dual phase sheet steel of tensile strength 400MPa level, it is characterized in that, described dual phase sheet steel chemical ingredients mass percent is: C:0.01～0.05%, Si:0.1～0.4%, Mn:1.2～1.6%, Cr:0.1～0.4%, Als:0.02～0.05%, N≤0.005%, P≤0.02%, S≤0.01%, and all the other are Fe and inevitable remaining impurity element;
Described dual phase sheet steel has ferrite and martensite duplex structure, and wherein martensitic percent by volume is 4～9%;
Described dual phase sheet steel yield strength is 200～250MPa, and tensile strength is 400～450MPa, and unit elongation is 30～35%.
2. the automobile cold-rolled dual phase sheet steel of tensile strength 400MPa level as claimed in claim 1, it is characterized in that, described dual phase sheet steel chemical ingredients mass percent is: C:0.02～0.04%, Si:0.2～0.3%, Mn:1.4～1.6%, Cr:0.2～0.3%, Als:0.02～0.04%, N≤0.003%, P≤0.012%, S≤0.005%, all the other are Fe and inevitable remaining impurity element.
3. the preparation method of the automobile cold-rolled dual phase sheet steel of tensile strength 400MPa level as claimed in claim 1 or 2, at first smelt, and refining in the heating ladle, cast slab by continuous casting then, hot rolling routinely again, the pickling cold continuous rolling, heat-treat technology at last, it is characterized in that, described thermal treatment process adopts continuous annealing process, it heats successively, insulation, slow cooling, cold soon, overaging and naturally cooling step, specifically: be heated to 740～800 ℃ of annealing temperatures earlier, insulation 90～120S then with speed slow cooling to 640～680 of 5～8 ℃/s ℃, is chilled to 260～320 ℃ soon with the speed greater than 40 ℃/s then and carries out overaging and handle, the overaging treatment time is 400～600s, naturally cools to room temperature at last.
4. as the preparation method of the automobile cold-rolled dual phase sheet steel of tensile strength 400MPa level as described in the claim 3, it is characterized in that described annealing temperature is 750～770 ℃, fast cold beginning temperature is 650～670 ℃, fast cold but speed is 40～60 ℃/s, and the overaging treatment temp is 280～320 ℃.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN2013102510451A CN103305762A (en) | 2013-06-21 | 2013-06-21 | Cold-rolled dual-phase sheet steel with 400MPa-level tensile strength and preparation method thereof |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| CN2013102510451A CN103305762A (en) | 2013-06-21 | 2013-06-21 | Cold-rolled dual-phase sheet steel with 400MPa-level tensile strength and preparation method thereof |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN103305762A true CN103305762A (en) | 2013-09-18 |
Family
ID=49131473
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN2013102510451A Pending CN103305762A (en) | 2013-06-21 | 2013-06-21 | Cold-rolled dual-phase sheet steel with 400MPa-level tensile strength and preparation method thereof |
Country Status (1)
| Country | Link |
|---|---|
| CN (1) | CN103305762A (en) |
Cited By (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103938070A (en) * | 2014-04-10 | 2014-07-23 | 马钢(集团)控股有限公司 | Steel plate and preparation method thereof |
| CN103938101A (en) * | 2014-04-10 | 2014-07-23 | 马钢(集团)控股有限公司 | Steel plate and preparation method thereof |
| CN106011644A (en) * | 2016-07-11 | 2016-10-12 | 攀钢集团攀枝花钢铁研究院有限公司 | High-elongation and high-strength cold-rolled steel plate and preparation method thereof |
| CN107267726A (en) * | 2017-06-06 | 2017-10-20 | 武汉钢铁有限公司 | The manufacture method of 450MPa grades of cold-rolled biphase steels of tensile strength |
| CN107338395A (en) * | 2017-07-13 | 2017-11-10 | 武汉钢铁有限公司 | 450MPa levels hot rolling low yield strength ratio paper-thin strip 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 |
| CN110230000A (en) * | 2019-07-10 | 2019-09-13 | 马鞍山钢铁股份有限公司 | A kind of 500MPa grades of galvanizing by dipping high-strength steel and preparation method thereof |
| CN110402298A (en) * | 2017-03-13 | 2019-11-01 | 杰富意钢铁株式会社 | High strength cold rolled steel plate and its manufacturing method |
| CN114107806A (en) * | 2021-10-29 | 2022-03-01 | 马鞍山钢铁股份有限公司 | 450 MPa-grade hot-galvanized dual-phase steel with high work hardening rate and surface quality and production method thereof |
| CN115612934A (en) * | 2022-10-19 | 2023-01-17 | 鞍钢蒂森克虏伯汽车钢有限公司 | 590 MPa-level high-formability hot-dip galvanized dual-phase steel plate and preparation method thereof |
Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102839329A (en) * | 2012-08-06 | 2012-12-26 | 马钢(集团)控股有限公司 | Cold-rolling double-phase-steel steel plate with tensile strength of 450 MPa, and preparation method thereof |
-
2013
- 2013-06-21 CN CN2013102510451A patent/CN103305762A/en active Pending
Patent Citations (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102839329A (en) * | 2012-08-06 | 2012-12-26 | 马钢(集团)控股有限公司 | Cold-rolling double-phase-steel steel plate with tensile strength of 450 MPa, and preparation method thereof |
Cited By (16)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103938101A (en) * | 2014-04-10 | 2014-07-23 | 马钢(集团)控股有限公司 | Steel plate and preparation method thereof |
| CN103938070B (en) * | 2014-04-10 | 2017-04-12 | 马钢(集团)控股有限公司 | Steel plate and preparation method thereof |
| CN103938070A (en) * | 2014-04-10 | 2014-07-23 | 马钢(集团)控股有限公司 | Steel plate and preparation method thereof |
| CN106011644A (en) * | 2016-07-11 | 2016-10-12 | 攀钢集团攀枝花钢铁研究院有限公司 | High-elongation and high-strength cold-rolled steel plate and preparation method thereof |
| 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 |
| CN107619993B (en) * | 2016-07-13 | 2019-12-17 | 上海梅山钢铁股份有限公司 | Cold-rolled martensite steel plate with yield strength of 750MPa and manufacturing method thereof |
| CN110402298A (en) * | 2017-03-13 | 2019-11-01 | 杰富意钢铁株式会社 | High strength cold rolled steel plate and its manufacturing method |
| US11186900B2 (en) | 2017-03-13 | 2021-11-30 | Jfe Steel Corporation | High-strength cold rolled steel sheet and method for manufacturing the same |
| CN110402298B (en) * | 2017-03-13 | 2021-10-15 | 杰富意钢铁株式会社 | High-strength cold-rolled steel sheet and method for producing same |
| CN107267726A (en) * | 2017-06-06 | 2017-10-20 | 武汉钢铁有限公司 | The manufacture method of 450MPa grades of cold-rolled biphase steels of tensile strength |
| CN107338395B (en) * | 2017-07-13 | 2019-06-07 | 武汉钢铁有限公司 | 450MPa grades of hot rolling low yield strength ratio paper-thin strips and its manufacturing method |
| CN107338395A (en) * | 2017-07-13 | 2017-11-10 | 武汉钢铁有限公司 | 450MPa levels hot rolling low yield strength ratio paper-thin strip and its manufacture method |
| CN110230000A (en) * | 2019-07-10 | 2019-09-13 | 马鞍山钢铁股份有限公司 | A kind of 500MPa grades of galvanizing by dipping high-strength steel and preparation method thereof |
| CN114107806A (en) * | 2021-10-29 | 2022-03-01 | 马鞍山钢铁股份有限公司 | 450 MPa-grade hot-galvanized dual-phase steel with high work hardening rate and surface quality and production method thereof |
| CN115612934A (en) * | 2022-10-19 | 2023-01-17 | 鞍钢蒂森克虏伯汽车钢有限公司 | 590 MPa-level high-formability hot-dip galvanized dual-phase steel plate and preparation method thereof |
| CN115612934B (en) * | 2022-10-19 | 2024-02-02 | 鞍钢蒂森克虏伯汽车钢有限公司 | 590 MPa-level high-formability hot dip galvanized dual-phase steel plate and preparation method thereof |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN103805838B (en) | High formability super strength cold-roll steel sheet and manufacture method thereof | |
| CN110029274B (en) | 1600 MPa-grade high-strength high-plasticity steel for hot stamping and preparation method thereof | |
| CN103305762A (en) | Cold-rolled dual-phase sheet steel with 400MPa-level tensile strength and preparation method thereof | |
| CN103556048B (en) | Production method for two-phase automobile steel plate with low yield-strength ratio and high strength | |
| CN101348885B (en) | 1000MPa grade cold rolling hot dip galvanizing two-phase steel and manufacturing method thereof | |
| CN109628846B (en) | 1300 MPa-grade ultrahigh-strength cold-rolled steel plate for automobiles and production method thereof | |
| CN106319368B (en) | A kind of economical thin carrier bar and its manufacture method | |
| CN101487096B (en) | Low-alloy high-strength C-Mn-Al Q & P steel and method of manufacturing the same | |
| CN102839329B (en) | Cold-rolling double-phase-steel steel plate with tensile strength of 450 MPa, and preparation method thereof | |
| CN103509997B (en) | A kind of 440MPa level cold-rolled high-strength automobile structural steel and manufacture method thereof | |
| CN102912219A (en) | High-strength plastic accumulation TRIP (Transformation-Induced Plasticity) steel plate and preparation method thereof | |
| CN103255341B (en) | High-strength and high-toughness hot-rolled wear-resistant steel and preparation method thereof | |
| CN105803321A (en) | 980 MPa-level vanadium-contained ultrafine grain cold rolled dual-phase steel and preparing method thereof | |
| CN104498821B (en) | Medium-manganese high-strength steel for automobiles and production method thereof | |
| CN106350731A (en) | Cold-rolled high-strength steel plate with excellent phosphorization and formability and manufacturing method thereof | |
| CN107502819B (en) | A kind of 600MPa grades of 0.6mm or less thin gauge cold-rolled biphase steel and preparation method thereof | |
| CN103469089B (en) | A kind of cheese crystal grain deep-draw dual phase sheet steel and preparation method thereof | |
| CN105274432A (en) | 600 MPa grade high-yield-ratio high-plasticity cold-rolled steel plate and manufacturing method thereof | |
| CN110863138B (en) | 1800 MPa-grade hot forming steel and manufacturing method thereof | |
| CN111172466B (en) | Plasticity-enhanced cold-rolled dual-phase steel with tensile strength of 590MPa and production method thereof | |
| CN105937011B (en) | Low yield strength cold rolling high strength steel plate and preparation method thereof | |
| CN102021483B (en) | Cold-rolled dual-phase steel plate with 1,200 MPa-level tensile strength and preparation method thereof | |
| CN109694990A (en) | Light phase transition inducing plasticity steel and its production method with good strong plasticity | |
| CN107747039A (en) | A kind of high reaming performance cold-rolled biphase steel and preparation method thereof | |
| CN113403529B (en) | 1470 MPa-level alloyed galvanized steel plate for cold stamping and preparation method thereof |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| C12 | Rejection of a patent application after its publication | ||
| RJ01 | Rejection of invention patent application after publication |
Application publication date: 20130918 |