CN101153369A - Cold-rolled high-strength diphasic strip steel and manufacturing process thereof - Google Patents
Cold-rolled high-strength diphasic strip steel and manufacturing process thereof Download PDFInfo
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Abstract
The invention relates to a cold rolling high strength biphase strip steel and the manufacture process thereof, wherein, the strip steel comprises 0.05wt percent to 0.12wt percent of C, less than or equal to 0.1 wt percent of Si, 1.2wt percent to 1.8wt percent of Mn, 0.15wt percent to 0.35wt percent of Mo, less than or equal to 2.4wt percent of Cr (Mn+Cr+Mo), less than or equal to 0.015wt percent of P, less than or equal to 0.01wt percent of S, less than or equal to 0.005wt percent of N, 0.015wt percent to 0.035wt percent of Nb, 0.015wt percent to 0.065wt percent of Al and the rest, Fe and other inevitable impurities; the manufacture process mainly comprises hot rolling, cold rolling and annealing. With the invention, cold rolling high strength biphase steel with 780MPa tensile strength can be obtained and the common banded structure of the intensity level is eliminated to improve biphase steel phosphorization of the intensity level.
Description
Technical field
The present invention relates to a kind of band steel and manufacturing process thereof, relate in particular to a kind of cold-rolled high-strength diphasic strip steel and manufacturing process thereof.
Background technology
Automotive industry requires to use thinner steel plate for the needs of loss of weight; Simultaneously, for to safe requirement, must use high tensile steel plate, to guarantee enough structural strengths.Therefore, high-strength steel has application promise in clinical practice in automobile industry.Wherein, the high strength dual phase steel consumption maximum of tensile strength about 780Mpa is because the steel of this intensity rank is taken into account better in intensity and plasticity.In order to improve the intensity of dual phase steel, must add higher carbon and alloying element in the steel, have certain hardenability to guarantee steel.But after having added higher alloying element, serious component segregation takes place in the castingprocesses easily, cause follow-up material because uneven components and tissue odds are even, occur mechanical property on the inhomogeneous and different directions of banded structure and mechanical property than big-difference.Just relatively more serious in the high-strength steel of banded structure more than tensile strength 590Mpa, how to eliminate banded structure, obtaining the uniform cold-rolled biphase steel of tissue distribution is the major issue that high-strength steel need solve.Phosphatization is meant the alramenting processing that automotive sheet carries out before japanning, purpose is to improve painted sticking power and surface quality.Usually require the densification of phosphatize phosphate coat homogeneous microstructure.High-strength steel is owing to added more alloying element, and meeting enrichment these alloying elements in surface are sometimes up to tens times.The surface alloy enrichment of element is made the surface and is formed oxide film, is unfavorable for the homogeneous reaction of parkerizing process, easily causes defectives such as phosphatize phosphate coat is thick, loose, does not meet the requirement of automobile making.The phosphorus characteristic difference also is the FAQs of high-strength steel aspect automobile making.
The banded structure of steel mainly is that component segregation causes, segregation then betides in the molten steel solidification process, it is different at first to separate out the molten steel composition and the follow-up component content of separating out that solidify, the alloy element concentration that is dissolved in the molten steel can more and more higher (or more and more lower), finally causes the alloy part constituent content difference of the part of solidifying earlier in the tissue that solidifies and after coagulation very big.The zone of component segregation is deformed elongation in course of hot rolling, finally form banded structure.Banded structure contains high alloying element usually, and because these alloying element diffusion difficulties are difficult to eliminate by heating, the enrichment of alloying element attracts carbon also to be enriched in same zone, form the not only hard but also crisp martensite that is zonal arrangement after causing dual phase steel to quench, bigger to the harm of performance.Phosphorus characteristic is main relevant with the alloying element surface enrichment; under common annealing conditions; alloying element is diffused into the surface; with the oxygen reaction in the protective atmosphere; form oxide film, hindered the normal reaction of phosphatization liquid and iron, cause phosphatize phosphate coat thick or loose; influence follow-up painted adhesion property, make it not meet the requirement of automobile making.
The patent of invention of cold-rolled biphase steel that the intensity of producing to continuous annealing by update search is about 780Mpa is as follows:
The patent No. is that the chemical ingredients of CA2526488 is: 0.05-0.09%C, 0.4-1.3%Si, the Mn of 2.5-3.2% can select to add the Mo of 0.05-0.5% or the Ni of 0.05-2 ,≤0.05%P, S≤0.08*Ti-3.43*N+0.004, ≤ 0.006%N, 0.005-0.10%Al ,≤0.045%Ti, also can add≤0.04%Nb or≤0.0015%B, can add Ca and handle; Other is that Fe and inevitable impurity are formed.Require bainite content greater than 7%, by the above temperature hot rolling of Ar3, batch below 700 ℃ Pcm≤0.3, annealing between cold rolling, 700-900 ℃, and 550-700 ℃ of beginning cooling fast obtains finally that intensity is minimum to be the high-strength steel of 780Mpa.It is strong that this steel has the local deformaton ability, the characteristics that welding region hardness is low.Higher Mn content has been adopted in this steel design, will inevitably cause serious banded structure, thereby cause the ununiformity of mechanical property; In addition, added under the situation of high Mn, added many Si again, put forward high-carbon activity, aggravation C is poly-partially rich Mn district, both has been unfavorable for obtaining uniform tissue, also is unfavorable for phosphorus characteristic.
The patent No. is that EP1659191A1 has introduced the manufacture method of a kind of tensile strength greater than the high-strength steel of 780Mpa, its chemical ingredients is: 0.04-0.13%C, 0.30-1.2%Si, 1.0-3.5%Mn is no more than 0.04% Cu at most, ≤ 0.01%S, ≤ 0.07%Al ,≤0.05%Ti ,≤0.05%Nb, add 0.02-0.5%Cr or 0.05-0.3Mo or 0.05-0.5Ni or 0.0005-0.02%B in addition separately, other is that Fe and inevitable impurity are formed.This invention steel through hot rolling, 450-650 ℃ batch, 770-880 ℃ annealing, 10-50 ℃/s is cooled to below 340 ℃, can obtain the dual phase steel of the above tensile strength of 780Mpa.This steel has the martensite volume content more than 10%, and martensite intensity has good collision shock resistance up to 8Gpa.This invention steel has added more alloy, and the upper limit of Mn is very high, has added many Si again, and aggravation C is poly-partially rich Mn district, both has been unfavorable for obtaining uniform tissue, also is unfavorable for phosphorus characteristic.
The patent No. is the manufacture method that US20040238082A1 has introduced the good high-strength steel of a kind of reaming, its chemical ingredients is: 0.04-0.1%C, 0.5-1.5%Si, 1.8-3%Mn, ≤ 0.020%P ,≤0.01%S, 0.01-0.1%Al, ≤ 0.005%N, other is that Fe and inevitable impurity are formed.The hot rolling between Ar3-870 ℃ of this steel is batched below 620 ℃, 750-870 ℃ of annealing, 550-750 ℃ of beginning is cold soon, fast cooling rate rate 〉=100 ℃/s, and fast cold final temperature is lower than 300 ℃, the final tensile strength that obtains is more than 780Mpa, and hole expansibility is at least 60% cold rolling high-strength steel.Higher Mn content has been adopted in this steel design, easily forms banded structure, thereby causes the ununiformity of mechanical property; In addition, added under the situation of high Mn, added many Si again, aggravation C is poly-partially rich Mn district, both has been unfavorable for obtaining uniform tissue, also is unfavorable for phosphorus characteristic.
The patent No. is the manufacture method that US20050167007A1 has introduced a kind of high tensile steel plate, its chemical ingredients is: 0.05-0.13%C, 0.5-2.5%Si, 0.5-3.5%Mn, 0.05-1%Cr, 0.05-0.6%Mo, ≤ 0.1%Al ,≤0.005%S ,≤0.01%N, ≤ 0.03%P adds 0.005-0.05%Ti or 0.005-0.05%Nb or 0.005-0.2%V.This steel is through the above hot rolling of Ar3 temperature, and 450-700 ℃ is batched, annealing back with the cooling rate of 100 ℃/s from 700-600 ℃ of Cooling Quenching, tempering between 180-450 ℃ then.The hole expansibility that finally obtains tensile strength 780Mpa is higher than 50% high-strength steel.The design of this steel adopt higher Mn content and and the alloying element total amount is not limited, will inevitably cause serious banded structure, can not guarantee homogeneity of structure, thereby cause the inhomogeneous of mechanical property; In addition, added many Si, aggravation C is poly-partially rich Mn district, both has been unfavorable for obtaining uniform tissue, also is unfavorable for phosphorus characteristic.
The composition synopsis (wt%) of table 1 the present invention and existing other invention:
| The patent No. | C | Si | Mn | Cr | Mo | Ni | B |
| CA2526488 | 0.05-0.09 | 0.4-1.3 | 2.5-3.2 | 0.05-0.5 | 0.05-2 | 0.0002-0.0015 | |
| EP1659191A1 | 0.04-0.13 | 0.3-1.2 | 1-3.5 | 0.02-0.5 | 0.05-0.3 | 0.05-0.5 | 0.0005-0.02 |
| US20040238082A1 | 0.04-0.1 | 0.5-1.5 | 1.8-3 | ||||
| US20050167007A1 | 0.05-0.13 | 0.5-2.5 | 0.5-3.5 | 0.05-1 | 0.05-0.6 | ||
| The present invention | 0.05-0.12 | ≤0.1 | 1.2-1.8 | 2.4-Mn-Mo | 0.15-0.35 |
The continuous table of the composition synopsis of table 2 the present invention and existing other invention (wt%):
| The patent No. | P | S | Al | N | Ti | Nb | Ca | V |
| CA2526488 | 0.001-0.05 | ≤0.08*Ti-3.43*N+0.004 | 0.005-0.1 | ≤0.006 | 0.001-0.045 | ≤0.04 | 0.0003-0.01 | |
| EP1659191A1 | ≤0.04 | ≤0.01 | 0.001-0.07 | 0.005-0.05 | ≤0.05 | |||
| US20040238082A1 | ≤0.02 | ≤0.01 | 0.01-0.1 | ≤0.005 | ||||
| US20050167007A1 | ≤0.03 | ≤0.005 | ≤0.1 | ≤0.0 | 0.005-0.05 | 0.005-0.05 | 0.005-0.2 | |
| The present invention | ≤0.015 | ≤0.01 | 0.015-0.065 | ≤0.005 | 0.015-0.035 |
Above patent is not all done any explanation to banded structure in the steel and phosphorus characteristic, and the invention target that shows these patents all is not to solve banded structure and the bad problem of phosphorus characteristic in the high-strength steel.According to metallurgy principle, can not effectively eliminate the problem of banded structure common in the high strength dual phase steel and phosphatization difference according to the design of above patent.
Summary of the invention
Purpose of the present invention, be to design by the reasonable component design and processes, obtain the cold-rolled high-strength dual phase steel of tensile strength 780Mpa, eliminate the common banded structure of this intensity rank, obtain equally distributed martensite and uniform mechanical property, simultaneously, design by composition, improve the phosphatization of this rank dual phase steel, make it meet the requirement of automobile making.
The object of the present invention is achieved like this:
Draw point of the present invention by suitable composition design and processes design, under the situation that does not increase any additional process, is effectively eliminated the problem of banded structure and phosphatization difference to the problem of banded structure in the high strength dual phase steel and phosphorus characteristic difference.Concrete measure is that the control alloying element adds total amount and the compound interpolation of multiple alloying element.At first, control alloying element total amount is selected lower carbon content scope, thereby reduces the enrichment degree of C in steel, reduces the banded structure tendency; Select lower Mn content to add, reduce that main alloy element amount in this dual phase steel can effectively reduce tendency that banded structure occurs and the detrimentally affect of phosphatization; Add a certain amount of Mo, remedy the low hardening capacity that causes of Mn content and descend, simultaneously, surface enrichment does not take place and does not reduce phosphatization in Mo; The interpolation of strictness restriction Si in composition designs reduces because gathering partially of the C atom that Si change C atom activity causes helps reducing banded structure and form tendency.Restriction alloying element total amount, the addition of Cr is looked the addition of Mn, Mo and is increased and decreased; Can reduce the tendency of banded structure generation and the tendency of phosphatization variation greatly by above measure; Many alloying elements add, and can reduce single alloying element addition on the one hand, and on the other hand, the alloying element of interpolation is intended to draw back on the fusing point gap, and the alloying element fusing point height order among the present invention is Mo＞Cr＞Fe＞Mn.In process of setting, rich Mo separates out earlier mutually with rich Cr, and rich Mn separates out after mutually, has avoided separating out simultaneously, has alleviated highly enriched when alloying element is separated out simultaneously, can effectively reduce the tendency that banded structure forms.At process aspect, adopted lower coiling temperature, crystal grain thinning makes in cold-rolled process, because the grain orientation difference, turning direction is different with angle, and banded structure is disperseed; Adopted higher annealing holding temperature, helped the dilution of carbon content, avoided banded structure, be cooled fast to 700-750 ℃ simultaneously and just be cooled to below 300 ℃, effectively avoided the formation of the poly-partially and banded structure of carbon with higher rate of cooling.In the final product, because Si, Mn content are low, the alloying element surface enrichment is significantly less than the situation of high Si, high Mn, obtains good phosphorus characteristic.
Steel of the present invention selects the reason of chemical ingredients scope as follows:
C: improve martensitic intensity, influence martensitic content, very big to intensity effect, simultaneously, it is unfavorable to weldability that carbon content improves, and therefore, selects carbon content between 0.05-0.12wt%, if be lower than 0.05%, insufficient strength; If be higher than 0.12%, weldability descends, and too high in addition carbon can cause banded structure apparent in view.
Si: play the effect that improves unit elongation in steel, Si puies forward high-carbon activity, can promote C poly-partially in rich Mn district, the tendency of increase formation banded structure.In addition, Si forms oxide film at surface enrichment easily, in order to improve phosphatization, the upper limit of si content is controlled requirement≤0.1wt%.
Mn: can improve the hardening capacity of steel, effectively improve the intensity of steel, but unfavorable to welding.Mn is segregation in steel, is rolled into the Mn enrichment region that becomes band and distribute in course of hot rolling easily, forms banded structure, is unfavorable for the homogeneity of structure of final dual phase steel.In addition, Mn forms oxide film easily in the surface of steel plate enrichment, influences phosphatization, and therefore, the content of choosing Mn is 1.2-1.8wt%, is lower than the hardening capacity deficiency of 1.2% steel, insufficient strength; Be higher than 1.8%, easily produce banded structure, unfavorable to phosphatization.
Mo: can improve the hardening capacity of steel, effectively improve the intensity of steel; Mo at the surface enrichment of steel, does not influence phosphatization, so add the Mo of 0.15-0.35%.Be lower than 0.15% Mo, act on not obvious, the price comparison height of Mo, thus on be defined as 0.35%.
Cr: can improve the hardening capacity of steel, in order to guarantee hardening capacity, can add Cr, but require Mn+Cr+Mo≤2.4%, be higher than 2.4% and can cause intensity higher, plasticity descends, obviously banded and phosphatization decline.
P: in steel impurity element, requirement≤0.015wt%.
S: in steel impurity element, requirement≤0.01wt%.
Al: in steel, played the effect of desoxydatoin and crystal grain thinning, required Al:0.015-0.065wt%.
N: in steel impurity element, requirement≤0.005wt%.
Nb: be the precipitation strength element, play the effect of regulating intensity, require to be distributed between the 0.015-0.035wt%, crossing lowly increases not obviously to intensity, and too high then plasticity descends more.
In sum, the chemical ingredients of cold-rolled high-strength diphasic strip steel of the present invention comprises:
C：0.05-0.12wt％ Si：≤0.1wt％
Mn：1.2-1.8wt％ Mo：0.15-0.35wt％
Cr：Mn+Cr+Mo≤2.4wt％
P：≤0.015wt％ S：≤0.01wt％
N：≤0.005wt％ Nb：0.015-0.035wt％
Al：0.015-0.065wt％
Other is Fe and inevitable impurity.
The chemical ingredients preferred version of cold-rolled high-strength diphasic strip steel of the present invention is as follows:
C：0.06-0.10wt％ Si：≤0.03wt％
Mn：1.4-1.6wt％ Mo：0.2-0.3wt％
Cr：Mn+Cr+Mo≤2.0wt％
P：≤0.01wt％ S：≤0.005wt％
N：≤0.003wt％ Nb：0.02-0.03wt％
Al：0.03-0.06wt％
Other is Fe and inevitable impurity.
The manufacturing process of cold-rolled high-strength diphasic strip steel of the present invention is as follows:
Hot rolling:, roll back cooling fast, 500～650 ℃ of coiling temperatures by the above temperature hot rolling of Ar3;
Cold rolling: the 35-80% draft;
Annealing: 780-880 ℃ of insulation, be cooled fast between 750-650 ℃, be cooled to below 300 ℃ to be not less than 30 ℃/s speed, behind 200-300 ℃ of tempering 100-300s, it is smooth to pass through 0-0.6% again.
The preferred version of cold-rolled high-strength diphasic strip steel manufacturing process of the present invention is as follows:
Hot rolling: by the above temperature hot rolling of Ar3, roll back cooling fast, 540～600 ℃ of coiling temperatures,
Cold rolling: the 40-60% draft
Annealing: 800-860 ℃ of insulation, be cooled between 750-700 ℃ to be not less than 10 ℃/s cooling rate, be cooled to below 270 ℃ with 40-100 ℃/s speed again, behind 200-270 ℃ of tempering 100-300s, it is smooth to pass through 0-0.6% again.
The present invention makes it compared with prior art owing to adopted above-mentioned technical scheme, and have following advantage and positively effect: in the tissue of steel of the present invention, martensite is evenly distributed, and does not have obvious banded structure; Can produce intensity according to the present invention and be higher than high strength dual phase steel steel more than the 780Mpa, good percentage elongation, the mechanical property of different directions sampling is very approaching, and mechanical property has good uniformity, and helps the plasticity of dual phase steel; The tiny densification of alramenting film of steel of the present invention can provide good sticking power and corrosion resistance nature.The invention solves the banded structure of high strength dual phase steel and the fatal problem of phosphatization difference, meet fully fields such as automobile making to high strength dual phase steel in the requirement aspect intensity and the formability.
Embodiment
Following form is the specific embodiment of the present invention, wherein: table 3 is the chemical ingredients of steel of the present invention, A1-A5 is a patent steel sequence number of the present invention, and the process condition of steel of the present invention is as shown in table 4, steel of the present invention through smelting, hot rolling, cold rolling, annealing and smooth after the intensity that obtains as shown in table 5.As can be seen from Table 5, can produce intensity according to the present invention and be higher than high strength dual phase steel more than the 780Mpa, its good percentage elongation, the mechanical property of different directions sampling is very approaching, so mechanical property has good uniformity.As seen, by the design of the suitable composition of the present invention, the annealing process for cooling condition of improvement can obtain the high strength dual phase steel steel plate of homogeneous microstructure, and mechanical property is very even, helps the plasticity of dual phase steel.The invention solves the banded structure of high strength dual phase steel and the fatal problem of phosphatization difference, and good mechanical performance, therefore, the present invention is different from existing invention or is better than having now invention with the final each side such as result that obtain in the design of composition design and processes.
The chemical ingredients of table 3 steel of the present invention (wt%)
| Grade of steel | Chemical ingredients, wt% | |||||||||
| C | Si | Mn | Cr | Mo | P | S | Al | N | Nb | |
| A1 | 0.05 | 0.1 | 1.8 | 0.45 | 0.15 | 0.008 | 0.005 | 0.015 | 0.005 | 0.035 |
| A2 | 0.06 | 0.05 | 1.4 | 0.4 | 0.3 | 0.01 | 0.008 | 0.065 | 0.004 | 0.03 |
| A3 | 0.08 | 0.02 | 1.6 | 0.45 | 0.2 | 0.015 | 0.005 | 0.03 | 0.003 | 0.025 |
| A4 | 0.1 | 0.03 | 1.5 | 0.4 | 0.25 | 0.011 | 0.01 | 0.06 | 0.0025 | 0.02 |
| A5 | 0.12 | 0.01 | 1.2 | 0.5 | 0.35 | 0.012 | 0.006 | 0.045 | 0.0034 | 0.015 |
The critical process process parameter of table 4 invention steel and mechanical property contrast
| Grade of steel-technology | Holding temperature | A speed of cooling, ℃/s | Fast cold temperature in | Fast cold temperature out | Fast speed of cooling, ℃/s | Tempering temperature, ℃ | Tempering time, s | Smooth rate, % |
| A1 | 780 | 10 | 750 | 250 | 100 | 250 | 250 | 0 |
| A2-1 | 800 | 15 | 750 | 270 | 80 | 270 | 150 | 0.2 |
| A2-2 | 820 | 12 | 700 | 250 | 60 | 250 | 200 | 0.3 |
| A3 | 840 | 20 | 700 | 275 | 50 | 275 | 100 | 0.5 |
| A4 | 860 | 25 | 650 | 200 | 30 | 200 | 300 | 0.5 |
| A5-1 | 880 | 30 | 650 | 235 | 45 | 235 | 250 | 0.6 |
| A5-2 | 800 | 15 | 700 | 300 | 50 | 300 | 100 | 0.3 |
The performance of table 5 invention steel
| Laterally sampling stretches | Vertically sampling stretches | |||||
| Grade of steel-technology | σ sMpa | σ b，Mpa | δ 5，％ | σ sMpa | σ b，Mpa | δ 50，％ |
| A1 | 495 | 790 | 23 | 480 | 780 | 25 |
| A2-1 | 500 | 823 | 24 | 498 | 815 | 24 |
| A2-2 | 520 | 850 | 21 | 500 | 840 | 23 |
| A3 | 530 | 848 | 20 | 520 | 835 | 22 |
| A4 | 545 | 860 | 19 | 535 | 850 | 20 |
| A5-1 | 576 | 870 | 18 | 570 | 860 | 18 |
| A5-2 | 521 | 840 | 22 | 515 | 830 | 23 |
Claims (4)
1. cold-rolled high-strength diphasic strip steel is characterized in that:
C： 0.05-0.12wt％ Si：≤0.1wt％
Mn： 1.2-1.8wt％ Mo：0.15-0.35wt％
Cr： Mn+Cr+Mo≤2.4wt％
P： ≤0.015wt％ S：≤0.01wt％
N： ≤0.005wt％ Nb：0.015-0.035wt％
Al： 0.015-0.065wt％
Other is Fe and inevitable impurity.
2. cold-rolled high-strength diphasic strip steel as claimed in claim 1 is characterized in that: described
C： 0.06-0.10wt％ Si：≤0.03wt％
Mn：1.4-1.6wt％ Mo：0.2-0.3wt％
Cr：Mn+Cr+Mo≤2.0wt％
P： ≤0.01wt％ S：≤0.005wt％
N： ≤0.003wt％ Nb：0.02-0.03wt％
Al：0.03-0.06wt％
Other is Fe and inevitable impurity.
3. the manufacturing process of cold-rolled high-strength diphasic strip steel as claimed in claim 1 is characterized in that:
Hot rolling:, roll back cooling fast, 500～650 ℃ of coiling temperatures by the above temperature hot rolling of Ar3;
Cold rolling: the 35-80% draft;
Annealing: 780-880 ℃ of insulation, be cooled fast between 750-650 ℃, be cooled to below 300 ℃ to be not less than 30 ℃/s speed, behind 200-300 ℃ of tempering 100-300s, it is smooth to pass through 0-0.6% again.
4. the manufacturing process of cold-rolled high-strength diphasic strip steel as claimed in claim 3 is characterized in that:
Hot rolling:, roll back cooling fast, 540～600 ℃ of coiling temperatures by the above temperature hot rolling of Ar3;
Cold rolling: the 40-60% draft;
Annealing: 800-860 ℃ of insulation is cooled between 750-700 ℃, again to be not less than 10 ℃/s cooling rate
Be cooled to below 270 ℃ with 40-100 ℃/s speed, behind 200-270 ℃ of tempering 100-300s, it is smooth to pass through 0-0.6% again.
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| CN102605240A (en) * | 2011-12-09 | 2012-07-25 | 首钢总公司 | High-strength and high-plasticity dual-phase steel and manufacturing method thereof |
| CN102644021A (en) * | 2012-04-23 | 2012-08-22 | 武汉钢铁(集团)公司 | 600MPa-level cold rolling dual-phase steel with low process sensitivity and production method |
| CN103018271A (en) * | 2012-12-07 | 2013-04-03 | 内蒙古包钢钢联股份有限公司 | Method for determination of C-Mn bainite rail CCT curve |
| CN103060703A (en) * | 2013-01-22 | 2013-04-24 | 宝山钢铁股份有限公司 | 780MPa grade cold rolling biphase strip steel and manufacturing method thereof |
| CN106048391A (en) * | 2016-07-20 | 2016-10-26 | 淮北元力金属制品有限公司 | Production method of cold-rolled bright strip steel |
| CN107190128A (en) * | 2017-06-06 | 2017-09-22 | 武汉钢铁有限公司 | The manufacture method of 780MPa grades of cold-rolled biphase steels of high-yield strength |
Family Cites Families (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| AU677540B2 (en) * | 1995-02-03 | 1997-04-24 | Nippon Steel Corporation | High-strength line-pipe steel having low yield ratio and excellent low-temperature toughness |
| EP1493828A4 (en) * | 2002-03-29 | 2011-01-05 | Nippon Steel Corp | High tensile steel excellent in high temperature strength and method for production thereof |
| JP4235030B2 (en) * | 2003-05-21 | 2009-03-04 | 新日本製鐵株式会社 | High-strength cold-rolled steel sheet and high-strength surface-treated steel sheet having excellent local formability and a tensile strength of 780 MPa or more with suppressed increase in hardness of the weld |
-
2006
- 2006-09-27 CN CN200610116554A patent/CN100584983C/en active Active
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| Publication number | Priority date | Publication date | Assignee | Title |
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| CN102605240A (en) * | 2011-12-09 | 2012-07-25 | 首钢总公司 | High-strength and high-plasticity dual-phase steel and manufacturing method thereof |
| CN102644021A (en) * | 2012-04-23 | 2012-08-22 | 武汉钢铁(集团)公司 | 600MPa-level cold rolling dual-phase steel with low process sensitivity and production method |
| CN102644021B (en) * | 2012-04-23 | 2014-07-23 | 武汉钢铁(集团)公司 | 600MPa-level cold rolling dual-phase steel with low process sensitivity and production method |
| CN103018271A (en) * | 2012-12-07 | 2013-04-03 | 内蒙古包钢钢联股份有限公司 | Method for determination of C-Mn bainite rail CCT curve |
| CN103060703A (en) * | 2013-01-22 | 2013-04-24 | 宝山钢铁股份有限公司 | 780MPa grade cold rolling biphase strip steel and manufacturing method thereof |
| WO2014114041A1 (en) * | 2013-01-22 | 2014-07-31 | 宝山钢铁股份有限公司 | 780 mpa class cold rolled dual-phase strip steel and manufacturing method thereof |
| CN103060703B (en) * | 2013-01-22 | 2015-09-23 | 宝山钢铁股份有限公司 | A kind of cold rolling diphasic strip steel of 780MPa level and manufacture method thereof |
| US11377711B2 (en) | 2013-01-22 | 2022-07-05 | Baoshan Iron & Steel Co., Ltd. | 780MPa cold-rolled duel-phase strip steel and method for manufacturing the same |
| CN106048391A (en) * | 2016-07-20 | 2016-10-26 | 淮北元力金属制品有限公司 | Production method of cold-rolled bright strip steel |
| CN107190128A (en) * | 2017-06-06 | 2017-09-22 | 武汉钢铁有限公司 | The manufacture method of 780MPa grades of cold-rolled biphase steels of high-yield strength |
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