CN101928875A - High-strength cold-rolled plate with favorable forming property and preparation method thereof - Google Patents

High-strength cold-rolled plate with favorable forming property and preparation method thereof Download PDF

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Publication number
CN101928875A
CN101928875A CN2009100122262A CN200910012226A CN101928875A CN 101928875 A CN101928875 A CN 101928875A CN 2009100122262 A CN2009100122262 A CN 2009100122262A CN 200910012226 A CN200910012226 A CN 200910012226A CN 101928875 A CN101928875 A CN 101928875A
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steel plate
strength
strength cold
temperature
rolling
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郭金宇
刘仁东
王衍平
王越
高毅
孙建伦
王旭
林利
王科强
徐鑫
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Angang Steel Co Ltd
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Angang Steel Co Ltd
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Abstract

The invention provides a high-strength cold-rolled plate with favorable forming property and a preparation method thereof. The high-strength cold-rolled plate comprises the following chemical components: 0.05-0.6% of C, being more than or equal to 0.3% and being less than 0.8% of Si, 0.5-4.0% of Mn, being more than ore equal to 0.2% of P, being more than or equal to 0.002% of S, being more than or equal to 0.1% of Al, being more than or equal to 0.01% of N, and the balance of Fe and inevitable impurities. The preparation method comprises the following steps: smelting, continuous-casting, hot-rolling, cold-rolling and continuous-annealing, wherein annealing temperature is higher than that of Ac3, holding time is 3-30 minutes; quickly cooling to 100-600 DEG C at the rate of 30-100 DEG C/s, keeping the temperature for 3-30 minutes, and finally cooling to room temperature at the rate of 5-30 DEG C/s. The invention adopts low-silicon low-aluminum component design and heat treatment technique; the strength level of the produced bainite TRIP steel is greater than 780 MPa; and the produced bainite TRIP steel has favorable strength, plasticity, extensibility, chambering property and coating property.

Description

Has high strength cold rolled steel plate of favorable forming property and preparation method thereof
Technical field
The invention belongs to the steel alloy technical field, relate in particular to a kind of high strength cold rolled steel plate and preparation method thereof with favorable forming property.
Background technology
Along with the rise of oil price and the aggravation of environmental degradation, people have higher requirement to the energy-saving and environmental protection and the security of automobile, and the lightweight of automobile also just becomes the long-term objective of automobile industry, and the application of high-strength steel on automobile is also universal day by day.In the manufacturing processed of automobile component, not only require steel plate to have very high intensity, to reach the purpose that alleviates tare, require steel plate to have good forming property simultaneously, to guarantee that steel plate can be processed into qualified part.
Traditional high-strength low-alloy steel, be the main steel grade that is used to make automobile structure, it is organized as ferrite and perlite, and its strength grade is generally at 400~600MPa, the shortcoming of this steel is that its unit elongation significantly descends along with the increase of intensity, is difficult to satisfy the requirement of automobile industry development.
In order to solve the contradiction of intensity and unit elongation, it is the advanced high-strength steel of representative that people have developed with dual phase steel and transformation induced plasticity steel, wherein the microtexture of dual phase steel is: the martensite of 80~90% ferrite+10~20%, being organized as of transformation induced plasticity steel: 60% ferrite+30% bainite+10% residual austenite tissue, these two kinds of steel have solved the contradiction between intensity and the unit elongation having the high-intensity good unit elongation that has simultaneously.Yet because the matrix of these two kinds of steel all is a ferritic structure, strengthen by second phase constitution, it is bad that structural inequality is given the reaming performance that has caused steel plate between this matrix and the enhanced tissue, limited its application on automobile component.Simultaneously, the intensity rank of these two kinds of steel is mostly at 600~800MPa, in order further to improve its intensity, needs to add alloying element such as Nb, V, Ti and takes measure such as controlled rolling and controlled cooling in process of production, come crystal grain thinning and separate out second particle mutually, to improve armor plate strength.This method not only increases cost, and control is difficult on producing, and the qualification rate of product is low.
In order further to improve the intensity of steel plate, guarantee that simultaneously it has good unit elongation and reaming performance, application number is 200580034205.0, the Chinese patent of " high-strength steel sheet that unit elongation and reaming are good and manufacture method thereof " by name has proposed a kind of solution, promptly producing with the tempered martensite is the steel sheet that matrix contains residual austenite, and this method has solved the contradiction between intensity and unit elongation and the reaming well.But this process using is quenched and is added the method that tempering is handled, and complex manufacturing is difficult to realize on existing continuous annealing production unit.
Application number is 200710091779.2, the Chinese patent of " high tensile steel plate that has excellent stretch flangeability " by name, having proposed a kind of is the high tensile steel plate of matrix with bainite and residual austenite, have high strength, high-elongation and reaming performance, its shortcoming is to take the composition design of high Si, wherein Si content between 0.8-2.5%, higher silicone content, cause plate surface quality to descend, hot-rolled steel plate performance and surface-coated performance are descended greatly.
Summary of the invention
The objective of the invention is to overcome the above-mentioned various defectives of existing in prior technology, providing a kind of is matrix with bainite and residual austenite, has high strength, high-ductility, high reaming and hot coating property, and strength grade is greater than the TRIP steel of 780MPa.
The present invention is achieved in that the chemical ingredients of the high strength cold rolled steel plate that this has favorable forming property is C:0.05%~0.6%, 0.3≤Si<0.8%, Mn:0.5%~4.0%, P≤0.2%, S≤0.002%, Al:0.02~0.1%, N≤0.005% by percentage to the quality, and surplus is Fe and unavoidable impurities.
The microstructure of high strength cold rolled steel plate of the present invention is in area percentage bainite>70%, residual austenite 1%~20%, and all the other are martensite and ferrite.
The chemical ingredients of this high strength cold rolled steel plate also can contain by percentage to the quality among V, Nb, Ti, Mo and the Cr more than a kind or 2 kinds, V:0.005%~2.0% wherein, Nb:0.002%~2.0%, Ti:0.002%~2.0%, Mo:0.002%~2.0%, Cr:0.005%~2.0%.
Composition design reason of the present invention:
C: being the important element that is used for the reinforcement of steel and hardening capacity is improved, is for obtaining bainite and heterogeneous structures such as residual austenite and martensite are indispensable.In order to obtain tensile strength greater than 780MPa and have bainite and the residual austenite tissue, C content is to be necessary more than 0.05%.On the other hand, when content was too much, occurring iron such as cementite easily was thickization of carbide, forming property is descended, and influence the weldability of steel plate, so the upper limit is defined as 0.6%.
Si: can hinder austenite effectively and decompose, reduce separating out of cementite, thereby C effectively is enriched in the austenite.If the content of Si is low excessively, can cause separating out of cementite, reduce the stability of residual austenite, so the following of Si content of the present invention is limited to 0.3%.Too highly then can reduce the surface quality of hot rolling slab, the coating property of cold-rolled steel sheet and the welding property of steel plate, thus the present invention will on be defined as<0.8%.
Mn: be austenite stabilizer element, and reduce cementite and separate out temperature.If the content of Mn is low excessively, can can't obtain residual austenite, so under be limited to 0.5%.Surpass at 4% o'clock at Mn content, can cause serious component segregation, form banded structure, influence the mechanical property of steel plate, thus on be limited to 4%.
P: can suppress the formation of cementite, improve ferritic intensity, so the P of some amount is useful to improving armor plate strength.Yet, if P content surpasses at 0.2% o'clock, during casting solidifying segregation significantly, cause the deterioration of internal fissure and reaming, be limited to 0.2% on therefore.
S: be harmful element, remain in the steel with inclusion forms such as MnS usually, remarkable to the tension intensity effect, so content must be controlled at below 0.002%.
Al: be deoxidant element necessary in the steel, the following of Al is limited to 0.02% among the present invention; The too high levels of Al can influence slab surface quality, thus Al on be limited to 0.1%.
N: the ageing and processibility that surpasses 0.01% o'clock steel plate worsens, so the upper limit is defined as 0.005%.
The explanation of the available element of the present invention:
Nb: play the purpose that improves intensity and welding property.Be lower than at 0.002% o'clock at content, can not play the effect that improves intensity and welding property.If add too much, can form too much carbide, reduce the forming property of material, thus on be limited to 2%.
V: play the effect of precipitation strength, can in 0.005%~2% scope, add.
Ti: the purpose that adds Ti is that Ti (CN) is separated out at high temperature, thereby plays the effect that hinders grain growth in course of hot rolling, and then improves the intensity of steel plate.Be lower than at 0.002% o'clock, be difficult for the effect of performance crystal grain thinning.If but add too much, can cause Ti (CN) thick, influence grain refinement effect, and causes austenitic C density loss in the steel plate, the forming property of reduction steel plate, thus on be defined as 2%.
Mo: the purpose that adds Mo is in order to suppress ferrite and pearlitic separating out, to improve the intensity of sheet material.Be lower than at 0.002% o'clock, do not have the purpose that inhibition ferrite and perlite are separated out, so the lower limit of Mo be made as 0.002%.If add too much, can increase considerably cost, so the upper limit be made as 2%.
Cr: the purpose of interpolation is in order to suppress ferrite and pearlitic separating out, and 0.005% o'clock effect is relatively poor being lower than, and can cause the sheet material forming mis-behave surpassing at 2% o'clock, therefore is defined as 0.005%~2%.
The preparation method that the present invention has the high strength cold rolled steel plate of favorable forming property comprises smelting, continuous casting, hot rolling and cold rolling, be characterized in carrying out continuous annealing after cold rolling, annealing temperature is greater than Ac3, soaking time 3~30 minutes, be quickly cooled to 100~600 ℃ with 30~100 ℃/s then, be incubated 3~30 minutes again, be cooled to room temperature with 5~30 ℃/s speed at last.
The thickness of the described continuously cast bloom of preparation method of the present invention is 70~200mm; Slab heating temperature is 1150~1350 ℃, is incubated 2~4 hours, carries out hot rolling, comprises roughing, finish rolling and laminar flow cooling, 750~900 ℃ of its finishing temperatures, and coiling temperature is 550~700 ℃, hot-rolled sheet thickness is 1.5~8mm; Carry out cold rollingly after the hot-rolled sheet pickling with 30%~80% accumulation draught, its finished product thickness is 0.5~4.0mm.
Technological design reason of the present invention:
The present invention at the process furnace of packing under the condition of high temperature or behind the cool to room temperature, heats the slab of thickness 70~200mm with 1150~1350 ℃ scopes, carry out hot finishing at 750~900 ℃ then.When hot rolling finishing temperature was lower than 750 ℃, crystal grain became thickness crystal grain admixture, and the processing characteristics of steel plate is descended, and when finishing temperature was higher than 900 ℃, resulting crystal grain was too thick, and the forming property of steel plate is descended.Low temperature batches the tissue that helps obtaining refinement, improves the forming property of steel plate, and therefore selecting coiling temperature is 550~700 ℃.Carrying out cold rollingly after the hot-rolled sheet pickling, consider rolling load and material property, is 30~80% with calibration under the cold rolling.
Annealing temperature is the key factor of decision plate property, and annealing temperature is greater than Ac3, to obtain austenitic single phase structure.Soaking time is between 30 seconds to 300 seconds under annealing temperature, and the time is lower than 30 seconds, and all thermal effect is insufficient, and the time is higher than 300 seconds, causes crystal grain too to be grown up, and reduces plate property.Speed of cooling is lower than 30 ℃/s for the first time, easily forms perlite, reduces the amount of the residual austenite in the steel plate, and the cooling power of line is moved back by the company of considering, range of choice is 30~100 ℃/s.Bainite district isothermal, the too high meeting of temperature causes cementite to be separated out, and temperature is crossed low meeting and is reduced bainite transformation speed, so preferred temperature range is 100~600 ℃.Steel plate of the present invention carries out isothermal annealing more than the Ac3 temperature, be quenched to bainite district isothermal processes then, be quenched to room temperature at last, obtain containing bainite, residual austenite, martensite and ferritic metal structure, thereby obtain having the high tensile steel plate of favorable forming property.
The present invention adopts low aluminium component design of special low silicon and thermal treatment process, and the strength grade of the bainite type TRIP steel of producing not only has good intensity, plasticity, unit elongation and reaming performance greater than 780MPa, also has good coating property simultaneously.This steel plate can be a cold-reduced sheet, also can be coated steel sheet, can be common zinc-plated, any plating such as aluminize, also can behind plating, carry out Alloying Treatment or carry out the multilayer plating, and can be that hot dip also can be to electroplate.
Embodiment
The present invention is further described by the following embodiment, but the present invention is not subjected to the restriction of following embodiment, can carry out suitable change in described scope and implement, and this all is included in the technical scope of the present invention.
The chemical ingredients of embodiment of the invention steel grade is as shown in table 1, and surplus is Fe and unavoidable impurities.After steel billet is cast in vacuum metling, implement hot rolling.During hot rolling, with 1250 ℃ of insulations 30 minutes, be rolled, finishing temperature is greater than 880 ℃, with the speed of cooling cooling of 40 ℃/s, with 650 ℃ of insulations after 30 minutes furnace cooling to room temperature.Carry out pickling, cold rolling, cold rolling draft is 70%, and cold-rolled steel sheet thickness is 2mm.
The continuous annealing process of embodiment of the invention steel plate is as shown in table 2.
The tensile property index of embodiment of the invention steel plate, reaming performance and coating property are as shown in table 3.The hot dip process performance of embodiment of the invention steel plate all satisfies the mechanical property of corresponding grade of steel, and its processibility and coating adaptation are good, and hot dip process sample surfaces quality reaches the FB rank.
The composition (weight %) of table 1 embodiment of the invention steel
Grade of steel C Si Mn P S N Al Nb V Ti Cr Mo
1 0.16 0.6 1.60 0.015 0.005 0.002 0.025
2 0.21 0.64 1.60 0.015 0.005 0.002 0.025
3 0.24 0.72 1.60 0.015 0.005 0.002 0.025
4 0.21 0.68 1.60 0.015 0.005 0.002 0.025 0.04
5 0.19 0.54 1.61 0.015 0.005 0.002 0.028 0.06
6 0.20 0.52 1.62 0.015 0.005 0.002 0.022 0.04
7 0.21 0.63 1.58 0.015 0.005 0.002 0.032 0.2
8 0.20 0.67 1.59 0.015 0.005 0.002 0.026 0.08
9 0.20 0.42 1.61 0.015 0.005 0.002 0.028 0.04 0.1
10 0.19 0.64 1.60 0.015 0.005 0.002 0.025 0.04 0.03
11 0.19 0.69 1.60 0.015 0.005 0.002 0.025 0.03 0.02
12 0.21 0.48 1.60 0.015 0.005 0.002 0.025 0.04 0.06
13 0.11 0.57 1.60 0.015 0.005 0.002 0.025 0.04 0.06
14 0.16 0.3 1.60 0.015 0.005 0.002 0.025 0.03 0.02
15 0.16 0.53 1.2 0.015 0.005 0.002 0.025 0.04 0.03
The continuous annealing process of table 2 embodiment of the invention steel plate
Mechanical property, hole expansibility and coating property after the thermal treatment of table 3 embodiment of the invention steel plate
Annotate: zero expression does not have not plating part.

Claims (6)

1. high strength cold rolled steel plate with favorable forming property, the chemical ingredients that it is characterized in that this steel is C:0.05%~0.6%, 0.3≤Si<0.8%, Mn:0.5%~4.0%, P≤0.2%, S≤0.002%, Al≤0.1%, N≤0.01% by percentage to the quality, and surplus is Fe and unavoidable impurities.
2. high strength cold rolled steel plate according to claim 1 is characterized in that its microstructure in area percentage bainite>70%, residual austenite 1%~20%, and all the other are martensite and ferrite.
3. high strength cold rolled steel plate according to claim 1 and 2, it is characterized in that its chemical ingredients also contains V:0.005%~2.0% by percentage to the quality, Nb:0.002%~2.0%, Ti:0.002%~2.0%, Mo:0.002%~2.0%, in Cr:0.005%~2.0% more than a kind or 2 kinds.
4. the preparation method of a claim 1,2 or 3 described high strength cold rolled steel plates, comprise smelting, continuous casting, hot rolling and cold rolling, it is characterized in that carrying out continuous annealing after cold rolling, annealing temperature is greater than Ac3, soaking time 3~30 minutes, be quickly cooled to 100~600 ℃ with 30~100 ℃/s then, be incubated 3~30 minutes again, be cooled to room temperature with 5~30 ℃/s speed at last.
5. according to the preparation method of the described high strength cold rolled steel plate of claim 4, the thickness that it is characterized in that described continuously cast bloom is 70~200mm; Slab heating temperature is 1150~1350 ℃, is incubated 2~4 hours, carries out hot rolling, 750~900 ℃ of finishing temperatures, and coiling temperature is 550~700 ℃, hot-rolled sheet thickness is 1.5~8mm.
6. according to the preparation method of claim 4 or 5 described high strength cold rolled steel plates, it is characterized in that described cold rolling accumulation draught 30%~80%, finished product thickness is 0.5~4.0mm.
CN2009100122262A 2009-06-22 2009-06-22 High-strength cold-rolled plate with favorable forming property and preparation method thereof Pending CN101928875A (en)

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CN102199722A (en) * 2011-05-09 2011-09-28 北京科技大学 Transformation induced plasticity (TRIP) steel plate of bainite substrate and preparation method thereof
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CN103890202B (en) * 2011-10-24 2015-09-30 杰富意钢铁株式会社 The manufacture method of the high tensile steel plate of excellent processability
CN102534375B (en) * 2012-02-27 2014-05-14 中国石油天然气集团公司 Steel for N80-grade Nb bainite oil containing casing pipe and manufacturing method for steel tube product
CN102534375A (en) * 2012-02-27 2012-07-04 中国石油天然气集团公司 Steel for N80-grade Nb bainite oil containing casing pipe and manufacturing method for steel tube product
US10227683B2 (en) 2012-03-30 2019-03-12 Voestalpine Stahl Gmbh High strength cold rolled steel sheet
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US10106874B2 (en) 2012-03-30 2018-10-23 Voestalpine Stahl Gmbh High strength cold rolled steel sheet
CN104204261A (en) * 2012-03-30 2014-12-10 奥钢联钢铁有限责任公司 High strength cold rolled steel sheet and method of producing such steel sheet
JP2015516511A (en) * 2012-03-30 2015-06-11 フォエスタルピネ スタール ゲゼルシャフト ミット ベシュレンクテルハフツングVoestalpinestahl Gmbh High-strength cold-rolled steel sheet and method for producing such a steel sheet
CN102747295A (en) * 2012-07-27 2012-10-24 武汉钢铁(集团)公司 Bainite sheet steel produced by controlled rolling and cooling method and preparation method thereof
CN102747295B (en) * 2012-07-27 2014-06-18 武汉钢铁(集团)公司 Bainite sheet steel produced by controlled rolling and cooling method and preparation method thereof
CN102899561A (en) * 2012-10-23 2013-01-30 鞍钢股份有限公司 High-strength cold forming steel sheet and manufacturing method thereof
CZ304832B6 (en) * 2013-04-13 2014-11-26 Západočeská Univerzita V Plzni Heat treatment process of TRIP steel half-finished products
CN103627887B (en) * 2013-08-28 2015-06-03 内蒙古北方重工业集团有限公司 Thermal processing method for eliminating carbide precipitation of low-carbon low-alloy heat-resisting steel
CN103627887A (en) * 2013-08-28 2014-03-12 内蒙古北方重工业集团有限公司 Thermal processing method for eliminating carbide precipitation of low-carbon low-alloy heat-resisting steel
CN103952635A (en) * 2014-05-13 2014-07-30 东北特钢集团北满特殊钢有限责任公司 Manganese-silicon-based high-strength steel and preparation method thereof
CN104233092A (en) * 2014-09-15 2014-12-24 首钢总公司 Hot-rolled TRIP steel and preparation method thereof
CN107849667A (en) * 2015-07-13 2018-03-27 新日铁住金株式会社 Steel plate, hot-dip galvanized steel sheet and alloyed hot-dip galvanized steel plate and their manufacture method
US10808291B2 (en) 2015-07-13 2020-10-20 Nippon Steel Corporation Steel sheet, hot-dip galvanized steel sheet, galvannealed steel sheet, and manufacturing methods therefor
CN107849667B (en) * 2015-07-13 2020-06-30 日本制铁株式会社 Steel sheet, hot-dip galvanized steel sheet, alloyed hot-dip galvanized steel sheet, and methods for producing same
US10822672B2 (en) 2015-07-13 2020-11-03 Nippon Steel Corporation Steel sheet, hot-dip galvanized steel sheet, galvanized steel sheet, and manufacturing methods therefor
CN105039851A (en) * 2015-08-17 2015-11-11 攀钢集团攀枝花钢铁研究院有限公司 Titanium alloyed TAM steel and manufacturing method thereof
CN105039851B (en) * 2015-08-17 2017-03-01 攀钢集团攀枝花钢铁研究院有限公司 Ti Alloying TAM steel and its manufacture method
CN106811698A (en) * 2015-12-02 2017-06-09 鞍钢股份有限公司 A kind of high strength steel plate and its manufacture method based on tissue precise controlling
CN105665662A (en) * 2016-03-09 2016-06-15 日照宝华新材料有限公司 ESP (endless strip production) line-based method for manufacturing steel for flux-cored wires
CN105734437A (en) * 2016-04-26 2016-07-06 东北大学 Nanoscale rodlike copper precipitated phase strengthening and toughening marine steel plate and preparation method thereof
CN107400834A (en) * 2016-05-18 2017-11-28 鞍钢股份有限公司 A kind of reaming hot rolling complex phase steel plate of good performance and its production method
CN106048176A (en) * 2016-06-06 2016-10-26 日照宝华新材料有限公司 Method for producing low-carbon hot-rolled TRIP steel based on ESP thin slab continuous casting and rolling process
CN105821190A (en) * 2016-06-06 2016-08-03 日照宝华新材料有限公司 Method for producing medium-carbon hot-rolled TRIP steel based on ESP thin-slab casting and rolling process
CN107794453A (en) * 2016-08-30 2018-03-13 宝山钢铁股份有限公司 A kind of thin strap continuous casting medium managese steel and its manufacture method
CN108396237A (en) * 2017-02-05 2018-08-14 鞍钢股份有限公司 A kind of high-ductility cold-reduced sheet and its production method
CN108396259A (en) * 2017-02-05 2018-08-14 鞍钢股份有限公司 A kind of high reaming performance hot rolling galvanized steel plain sheet and its manufacturing method
CN108396237B (en) * 2017-02-05 2020-01-07 鞍钢股份有限公司 High-plasticity cold-rolled sheet and production method thereof
CN107012398B (en) * 2017-04-25 2018-09-11 内蒙古科技大学 A kind of Nb-microalloying TRIP steel and preparation method thereof
CN107012398A (en) * 2017-04-25 2017-08-04 内蒙古科技大学 A kind of Nb-microalloying TRIP steel and preparation method thereof
CN107338351B (en) * 2017-07-27 2018-09-04 燕山大学 Accelerate the method for bainitic transformation in steel using the heterogeneous forming cores of in-situ nano AlN
CN107338351A (en) * 2017-07-27 2017-11-10 燕山大学 Accelerate the method for bainitic transformation in steel using the heterogeneous forming cores of in-situ nano AlN
CN111315908A (en) * 2017-11-10 2020-06-19 安赛乐米塔尔公司 Cold-rolled steel sheet and method for producing same
CN108754307B (en) * 2018-05-24 2020-06-09 山东钢铁集团日照有限公司 Method for producing economical cold-rolled DP780 steel with different yield strength grades
CN108754307A (en) * 2018-05-24 2018-11-06 山东钢铁集团日照有限公司 A method of producing the economical cold rolling DP780 steel of different yield strength ranks
CN108754328A (en) * 2018-06-14 2018-11-06 鞍钢股份有限公司 A kind of anti-room temperature ageing type baking hardening steel plate and its manufacturing method
WO2020001430A1 (en) * 2018-06-27 2020-01-02 宝山钢铁股份有限公司 Ultrahigh-strength hot-rolled steel sheet and steel strip having good fatigue and reaming properties and manufacturing method therefor
CN108950405B (en) * 2018-08-14 2020-02-18 武汉钢铁有限公司 800 MPa-grade multi-phase steel with good flanging performance and production method thereof
CN109504900A (en) * 2018-12-05 2019-03-22 鞍钢股份有限公司 A kind of superhigh intensity cold rolling transformation induced plasticity steel and preparation method thereof
CN110016615A (en) * 2019-04-26 2019-07-16 本钢板材股份有限公司 A kind of cold-rolled biphase steel DP780 and its Flexible Production method
CN110578100A (en) * 2019-10-18 2019-12-17 山东钢铁集团日照有限公司 cold-rolled CP980 steel with different yield strength grades and production method thereof
CN110629115A (en) * 2019-10-21 2019-12-31 山东钢铁集团日照有限公司 Economical cold-rolled CP800 steel with different yield strength grades and production method thereof
CN111534739A (en) * 2020-02-17 2020-08-14 本钢板材股份有限公司 980 MPa-grade high-formability cold-rolled phase-change induced plasticity steel and preparation method thereof
CN111206186A (en) * 2020-02-24 2020-05-29 攀钢集团攀枝花钢铁研究院有限公司 High-hole-expansion-performance cold-rolled dual-phase steel with tensile strength of 780MPa and preparation method thereof
CN111118498A (en) * 2020-03-06 2020-05-08 贵州大学 TRIP steel coating for 304 stainless steel surface laser cladding and cladding method
CN112159931A (en) * 2020-09-28 2021-01-01 首钢集团有限公司 1000 MPa-grade medium manganese TRIP steel with continuous yield and preparation method thereof
CN113528978A (en) * 2021-06-21 2021-10-22 首钢集团有限公司 980 MPa-grade galvanized complex-phase steel and preparation method thereof

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Application publication date: 20101229