CN101717886A - Hot rolled dual phase steel plate with 650MPa of tensile strength and manufacturing method thereof - Google Patents

Hot rolled dual phase steel plate with 650MPa of tensile strength and manufacturing method thereof Download PDF

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Publication number
CN101717886A
CN101717886A CN200910222583A CN200910222583A CN101717886A CN 101717886 A CN101717886 A CN 101717886A CN 200910222583 A CN200910222583 A CN 200910222583A CN 200910222583 A CN200910222583 A CN 200910222583A CN 101717886 A CN101717886 A CN 101717886A
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dual phase
steel plate
tensile strength
cooling
steel
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Pending
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CN200910222583A
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杨瑞青
季长恩
许振刚
李化龙
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Jiangsu Shagang Iron and Steel Research Institute Co Ltd
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Jiangsu Shagang Iron and Steel Research Institute Co Ltd
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Priority to CN200910222583A priority Critical patent/CN101717886A/en
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Abstract

The invention relates to a hot rolled dual phase steel plate with 650MPa of the tensile strength and a manufacturing method thereof. The dual phase steel plate contains the ingredients by weight percent of: 0.05-0.12% of C, 0.5-1.2% of Si, 1.0-1.6% of Mn and the balance of Fe and impurities. The manufacturing method of the dual phase steel plate comprises the step: a steel billet containing the same ingredients as the hot rolled dual phase steel plate is sequentially subject to heating, heat insulation, hot rolling and continuous laminar cooling, followed by take-up. The dual phase steel plate according to the invention is designed by adopting common low carbon-silcomanganese steel, has the characteristics of low alloy cost, excellent performance, simple manufacturing process, high production efficiency and great controllability, and is liable to be implemented on traditional continuous hot rolling production line.

Description

Hot rolled dual phase steel plate with 650 MPa of tensile strength and manufacture method thereof
Technical field
The present invention relates to a kind of steel of technical field of metal material manufacture and preparation method thereof, particularly a kind of low-carbon (LC) of tensile strength 650MPa level can cool off low temperature continuously and batch hot rolling biphase plate and manufacture method thereof.
Background technology
At present, the advanced high-strength steel (AHSS) of widespread use on automobile structure with raising travel safety, fuel economy and environment friendly, and is saved manufacturing cost.Therefore, high-strength vehicle is one of focus of material area research with the exploitation of hot-rolled steel sheet always.Yet, the maximum tensile strength of general ferritic-pearlitic steel plate is about 500MPa, though adding Cu, Ni, Cr or Nb, V, behind the alloying elements such as Ti, its tensile strength can increase, but simultaneously yield strength and yield tensile ratio (yield strength/tensile strength) is significantly improved, thereby makes the impact briquetting of part very difficult.
For this reason, people attempt using dual phase steel.Dual phase steel is meant by soft steel or low alloy steel and obtains through critical zone thermal treatment or controlled rolling, mainly, be characterized in the island martensite body that disperse is distributing hard on soft ferrite matrix by ferrite (about more than 70%) and a small amount of (about<30%) a kind of high-strength steel that martensite is formed.Martensite gives material enough tensile strength, and ferrite then makes the easy yield deformation of material have good plasticity and toughness.Therefore, dual phase steel has low yield strength, surrender continuously, and initial manufacture cementation index height, the tensile strength advantages of higher can overcome general advanced high-strength steel and be difficult to stamping forming contradiction.It is the punching press of automobile loss of weight, high tough structural part and simplifies Sheet Metal Forming Technology, has opened up a brand-new approach.
The application for a patent for invention of publication number CN1807670A and CN1807669A has proposed a kind of tensile strength 540MPa level dual phase sheet steel and a kind of tensile strength 600MPa level dual phase sheet steel and manufacture method thereof respectively, but the tensile strength of these two kinds of dual phase sheet steels is all on the low side.And the patent of invention of publication number CN1566389A proposes a kind of superfine crystal particle low-carbon and low-alloy dual phase sheet steel and manufacture method thereof, but this kind steel plate is when producing, the rolling easy generation mixed crystal of its two-phase region, and under low rolling temperature, need powerful mill capacity, general steel mill is difficult to reach.High-strength thin-crystal two-phase steel that patent of invention proposed of publication number CN1566389A and preparation method thereof also has similar defective.
The traditional hot rolling method is produced dual phase steel, because alloying element content is many, the ferrite formation speed is slow.In order to guarantee good intensity and moulding cooperation.Roll the back steel plate and need adopt 3 segmentation technology for controlled cooling usually.A kind of hot-rolled dual-phase steel board fabrication method of tensile strength 700MPa level has been proposed as the patent of invention of publication number CN101279330A, the type of cooling of this steel plate after rolling is: the 1st section is adopted the more weak water spray type of cooling of intensity to make the cooling of band steel enter the ferrite zone, and cooling rate is 25~45 ℃; The 2nd section is adopted the air cooling mode, makes the band steel finish major part (>75%) ferritic transformation, and the air cooling time is 10~15s; The 3rd section is adopted the strong cold water spray type of cooling, and cooling rate is 25~50 ℃, and making the austenitic transformation that does not have enough time to change is martensite, thereby obtains a certain proportion of duplex structure.Equally, the patent of invention of publication number CN1789467A, publication number CN1793400A has also all proposed a kind of high-tensile dual phase sheet steel and manufacture method.But, though the foregoing invention patent all discloses the preparation method with high-tensile dual phase sheet steel, but the segmentation type of cooling that it adopts has following defective usually, promptly, the beginning of air cooling, end temp are difficult to accurate control, the fast pace of big plant produced also is difficult to guarantee the so long air cooling time, and vertical ununiformity of cooling back product is also very outstanding.
Summary of the invention
The objective of the invention is to propose a kind ofly have high-tensile and good plasticity, and preparation technology is simple, low-carbon (LC) hot rolling biphase plate and manufacture method thereof that controllability is high, thus overcome deficiency of the prior art.
For achieving the above object, the present invention has adopted following technical scheme:
A kind of hot rolled dual phase steel plate with 650 MPa of tensile strength is characterized in that, composition that this dual phase sheet steel comprises and weight percent thereof are: the Fe and the impurity of C 0.05~0.12%, Si 0.5~1.2%, Mn 1.0~1.6% and surplus.
Further, described dual phase sheet steel thickness is at 1.5~12mm.
Described dual phase sheet steel has ferrite and martensite duplex structure.
Described dual phase sheet steel prepares by the following method:
The steel billet identical with described hot rolling biphase plate component heated, is incubated processing successively, carry out hot rolling again, carry out the cooling of successive layers stream after the hot rolling, controlled chilling speed is 18~50 ℃/s, batches after the cooling.
The preparation method of above-mentioned hot rolled dual phase steel plate with 650 MPa of tensile strength is characterized in that, this method is:
The steel billet identical with described hot rolling biphase plate component heated, is incubated processing successively, carry out hot rolling again, carry out the cooling of successive layers stream after the hot rolling, batch after the cooling.
Particularly, in this method, be that described steel billet is heated to 1150~1250 ℃, then be incubated processing.
The process that described insulation is handled continues 120~180min.
In this method, when carrying out hot rolling, the control start rolling temperature is 1050~1150 ℃, and finishing temperature is 820~880 ℃.
In this method, it is 18~50 ℃/s that the steel plate after rolling is carried out speed of cooling, and final cooling temperature is identical with coiling temperature, is 100~300 ℃.
This method comprises following concrete steps:
(1) by described dual phase sheet steel component configuration steelmaking feed, obtain molten steel with converter or electrosmelting, and continuous casting becomes steel billet;
(2) above-mentioned steel billet is heated to 1150~1250 ℃, soaking time 120~180 minutes;
(3) carry out hot rolling after the insulation, the control start rolling temperature is 1050~1150 ℃, and finishing temperature is controlled to be 820~880 ℃;
(4) carry out the cooling of successive layers stream after the hot rolling, controlled chilling speed is 18~50 ℃/s, and final cooling temperature is that coiling temperature is 100~300 ℃;
(5) batch after the cooling.
The present invention is a composition of steel based on common C-Mn, by adding an amount of Si element and adopting suitable cooling controlling and rolling controlling process, the hot rolling biphase plate that exploitation can be used in automobile structure, its microtexture is ferrite and martensite duplex structure, yield strength is 410~480MPa, and tensile strength is 670~750MPa, and yield tensile ratio is 0.59~0.70, the percentage of total elongation of having no progeny is 18.0~27.0%, and plasticity is good.
The effect of each alloying element that chemical ingredients of the present invention relates to is as follows:
C is a topmost solution strengthening element in the steel, also is to form martensitic bioelement.Traditional general carbon containing of thermal treatment type dual phase steel higher (0.1~0.2%).But related experiment shows, carbon content is too high to tend to cause martensite island or martensite/ferrite interface cracking in the moulding process, and it is moulding to influence material.Carbon content is crossed at least can not generate enough martensite.The present invention adopts 0.05~0.12% carbon content, and it can generate the martensite about 20%, and martensite is dislocation type martensite, and hardness is moderate.
The Si element is a ferrite former, and the diffusion of C element in austenite in the time of can promoting ferritic transformation promotes the generation of proeutectoid ferrite, simultaneously since Si at Fe 3Solubleness among the C is low, improves the Si constituent content and can stop pearlitic formation, improves the stability of remaining austenite, and the present invention adopts Si0.5~1.2%.
Mn is important solution strengthening element, can improve austenitic stability and reduce the ferritic transformation temperature, helps crystal grain thinning, obtains the low-temperature transformation tissue.Mn content is too low, can not guarantee the intensity of steel plate.Add an amount of Mn element (1.0~1.6) and will increase the intensity of 150MPa at least.But the Mn too high levels easily produces tangible banded segregation in steel, influences the homogeneity of hot rolling microstructure.Consider above-mentioned factor, the present invention has adopted Mn content 1.0~1.6%, and it can effectively promote steel performance.
Compared with prior art, beneficial effect of the present invention is: 650MPa level hot rolling biphase plate of the present invention adopts the composition design of common low carbon-silicon manganese steel, and cost of alloy is cheap, and is functional; And among the preparation technology of the present invention, when hot rolling, adopt the austenite one phase district rolling, it is even to roll back product microtexture, and adopts the continuous laminar flow type of cooling and suitable speed of cooling in process of cooling, and its production process realizes on the traditional hot continuous rolling production line easily.
Description of drawings
Fig. 1 is the engineering stress-strain curve figure of hot rolling biphase plate among the embodiment 2;
Fig. 2 is the structural representation of microtexture in the hot rolling biphase plate among the embodiment 2.
Embodiment
Below in conjunction with the drawings and the specific embodiments content of the present invention is described further.
Embodiment 1
Chemical ingredients that this hot rolling biphase plate comprises and weight percent thereof are: C 0.08%, and Si 0.69%, and Mn 1.43%, and P 0.009%, and S 0.0041%, and all the other are Fe and other unavoidable impurities.
This steel plate carries out the analog rolling experiment on Gleeble3800 thermal analogy machine, its process is:
By described dual phase sheet steel component configuration steelmaking feed, obtain molten steel with converter or electrosmelting, and continuous casting becomes the experiment bloom of 10 * 15 * 20mm;
To test bloom and carry out austenitizing at 1200 ℃ of insulation 10min;
After the insulation, carry out hot rolling, it is 1050 ℃ that roughing begins temperature, deflection is 0.45, implements finish rolling at 900 ℃, 875 ℃, 850 ℃ and 825 ℃ respectively then, and the finish rolling deflection is respectively 0.28,0.2,0.18 and 0.15, rate of deformation is 1/s, and finishing temperature is 825 ℃;
Cool off continuously after rolling, and be cooled to 250 ℃ with the speed of 19.5 ℃/s, be incubated 10min subsequently, last slow cooling is to room temperature.
This hot rolling biphase plate is organized as ferrite and martensite duplex structure, and wherein the ferrite volume fraction is about 85%, and average grain size is 8 μ m.
Embodiment 2
Chemical ingredients that this hot rolling biphase plate comprises and weight percent thereof are identical with embodiment 1, and its thickness specification is at 10mm, and mechanical property and weave construction see Table 1 and Fig. 1~2.This hot rolling biphase plate preparation process is:
By described dual phase sheet steel component configuration steelmaking feed, obtain molten steel with converter or electrosmelting, and continuous casting becomes slab;
Slab is through 1200 ℃ of heat tracing 2h;
Be rolled after the insulation, 1078 ℃ of roughing start rolling temperatures, roughing draught are 0.15,0.20 and 0.20, and the finish rolling start rolling temperature is 963 ℃, and the finish rolling draught is respectively 0.28,0.28,0.26,0.18,0.18 and 0.13, and finishing temperature is 874 ℃;
Roll after continuously laminar flow be cooled to 200 ℃ and batch, speed of cooling is 43.9 ℃/s.
Embodiment 3
Chemical ingredients that this hot rolling biphase plate comprises and weight percent thereof are identical with embodiment 1, its preparation technology is close with embodiment 2, but its finish rolling start rolling temperature is 971 ℃, and finishing temperature is 880 ℃, roll after continuously laminar flow be cooled to 150 ℃ and batch, speed of cooling is 47.6 ℃/s.The mechanical property of this hot rolling biphase plate is as shown in table 1.
Comparative Examples
Chemical ingredients that this steel plate comprises and weight percent thereof are identical with embodiment 1, and its preparation technology is:
Steel billet slab that will be identical with embodiment 1 described hot rolling biphase plate component adopts and rolls into coiled sheet with embodiment 2 identical rolling procedures after 1200 ℃ of heating and being incubated 2 hours, and finishing temperature is 856 ℃; The segmentation cooling system is adopted in the laminar flow cooling, and leading portion and back segment water-cooled cooling rate are 65.6 ℃/s, and air cooling begins temperature and is about 720 ℃, air cooling time 5s.Be chilled to 200 ℃ eventually and batch, the mechanical property of the steel plate that obtains is as shown in table 1.
The mechanical property of hot rolling biphase plate and Comparative Examples steel plate contrast among table 1. embodiment 2,3
Yield strength, MPa Tensile strength, MPa Yield tensile ratio Unit elongation A 80,%
Embodiment 2 ?462 ?675 ??0.68 ??26.6
Embodiment 3 ?412 ?701 ??0.59 ??25.0
Comparative Examples 1 ?347 ?614 ??0.57 ??24.4
Can see obviously that by the foregoing description and Comparative Examples hot rolling biphase plate mechanical property of the present invention is far superior to existing various hot-rolled steel sheet, and its preparation technology is simple, the production efficiency height, controllability is good.

Claims (10)

1. a hot rolled dual phase steel plate with 650 MPa of tensile strength is characterized in that, composition that this dual phase sheet steel comprises and weight percent thereof are: the Fe and the impurity of C 0.05~0.12%, Si 0.5~1.2%, Mn 1.0~1.6% and surplus.
2. hot rolled dual phase steel plate with 650 MPa of tensile strength according to claim 1 is characterized in that, described dual phase sheet steel thickness is at 1.5~12mm.
3. hot rolled dual phase steel plate with 650 MPa of tensile strength according to claim 1 and 2 is characterized in that, described dual phase sheet steel has ferrite and martensite duplex structure.
4. hot rolled dual phase steel plate with 650 MPa of tensile strength according to claim 1 and 2 is characterized in that, described dual phase sheet steel prepares by the following method:
The steel billet identical with described hot rolling biphase plate component heated, is incubated processing successively, carry out hot rolling again, carry out the cooling of successive layers stream after the hot rolling, controlled chilling speed is 18~50 ℃/s, batches after the cooling.
5. the preparation method of hot rolled dual phase steel plate with 650 MPa of tensile strength according to claim 1 is characterized in that this method is:
The steel billet identical with described hot rolling biphase plate component heated, is incubated processing successively, carry out hot rolling again, carry out the cooling of successive layers stream after the hot rolling, batch after the cooling.
6. the preparation method of hot rolled dual phase steel plate with 650 MPa of tensile strength according to claim 1 according to claim 5 is characterized in that, in this method, is that described steel billet is heated to 1150~1250 ℃, then is incubated processing.
7. according to the preparation method of claim 5 or 6 described hot rolled dual phase steel plate with 650 MPa of tensile strength according to claim 1, it is characterized in that the process that described insulation is handled continues 120~180min.
8. the preparation method of hot rolled dual phase steel plate with 650 MPa of tensile strength according to claim 1 according to claim 5 is characterized in that, in this method, when carrying out hot rolling, the control start rolling temperature is 1050~1150 ℃, and finishing temperature is 820~880 ℃.
9. the preparation method of hot rolled dual phase steel plate with 650 MPa of tensile strength according to claim 1 according to claim 5, it is characterized in that in this method, it is 18~50 ℃/s that the steel plate after rolling is carried out speed of cooling, and final cooling temperature is identical with coiling temperature, is 100~300 ℃.
10. the preparation method of hot rolled dual phase steel plate with 650 MPa of tensile strength according to claim 1 according to claim 5 is characterized in that, this method comprises following concrete steps:
(1) by described dual phase sheet steel component configuration steelmaking feed, obtain molten steel with converter or electrosmelting, and continuous casting becomes steel billet;
(2) above-mentioned steel billet is heated to 1150~1250 ℃, soaking time 120~180 minutes;
(3) carry out hot rolling after the insulation, the control start rolling temperature is 1050~1150 ℃, and finishing temperature is controlled to be 820~880 ℃;
(4) carry out the cooling of successive layers stream after the hot rolling, controlled chilling speed is 18~50 ℃/s, and final cooling temperature is that coiling temperature is 100~300 ℃;
(5) batch after the cooling.
CN200910222583A 2009-11-20 2009-11-20 Hot rolled dual phase steel plate with 650MPa of tensile strength and manufacturing method thereof Pending CN101717886A (en)

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Cited By (16)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN102286700A (en) * 2011-09-13 2011-12-21 江苏省沙钢钢铁研究院有限公司 Sulfuric-acid-resistant dew point corrosion steel with tensile strength greater than or equal to 800Mpa grade and preparation method thereof
CN102517496A (en) * 2011-12-23 2012-06-27 首钢总公司 Hot rolled ferrite/martensite double phase steel and production method thereof
CN102605254A (en) * 2012-04-18 2012-07-25 江苏省沙钢钢铁研究院有限公司 Hot-rolled dual-phase steel medium plate for building structure, and production method thereof
CN102912244A (en) * 2012-10-23 2013-02-06 鞍钢股份有限公司 780MPa-grade tensile strength hot rolling double-phase steel plate and manufacture method thereof
CN103031493A (en) * 2011-09-29 2013-04-10 鞍钢股份有限公司 650MPa-level low-Si Cr-containing hot-rolled dual phase steel plate and manufacturing method thereof
CN104593677A (en) * 2015-01-19 2015-05-06 唐山钢铁集团有限责任公司 Production process of heavy gauge hot-rolled dual-phase steel DP600
CN105483545A (en) * 2014-09-19 2016-04-13 鞍钢股份有限公司 800MPa level hot-rolling high broaching steel plate and manufacturing method thereof
CN105506476A (en) * 2014-09-26 2016-04-20 鞍钢股份有限公司 600 MPa-grade highly-chambered steel plate for automotive chassis and manufacturing method thereof
CN105543674A (en) * 2015-12-18 2016-05-04 东北大学 Method for manufacturing cold-rolled ultrahigh-strength dual-phase steel with high local forming performance
CN106119703A (en) * 2016-06-21 2016-11-16 宝山钢铁股份有限公司 A kind of 980MPa level hot-rolled dual-phase steel and manufacture method thereof
CN106834915A (en) * 2016-12-06 2017-06-13 内蒙古包钢钢联股份有限公司 800MPa grades of hot-rolled dual-phase steel of 2 ~ 4mm thickness and its processing 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
CN111982956A (en) * 2020-08-27 2020-11-24 广东韶钢松山股份有限公司 Method for determining elimination of ultra-low carbon steel mixed crystal structure based on thermal simulation testing machine
CN112246868A (en) * 2020-08-20 2021-01-22 唐山钢铁集团有限责任公司 Production method of substrate for cold rolling of 700 Mpa-level high-strength checkered plate
CN112375979A (en) * 2020-10-31 2021-02-19 日照钢铁控股集团有限公司 Process for hot rolling thin steel plate with 800 MPa-level tensile strength, high plasticity and low cost
CN114086084A (en) * 2021-11-04 2022-02-25 湖南华菱涟钢特种新材料有限公司 Hot-rolled dual-phase steel and preparation method thereof

Cited By (21)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN102286700A (en) * 2011-09-13 2011-12-21 江苏省沙钢钢铁研究院有限公司 Sulfuric-acid-resistant dew point corrosion steel with tensile strength greater than or equal to 800Mpa grade and preparation method thereof
CN103031493A (en) * 2011-09-29 2013-04-10 鞍钢股份有限公司 650MPa-level low-Si Cr-containing hot-rolled dual phase steel plate and manufacturing method thereof
CN103031493B (en) * 2011-09-29 2015-05-06 鞍钢股份有限公司 650MPa-level low-Si Cr-containing hot-rolled dual phase steel plate and manufacturing method thereof
CN102517496A (en) * 2011-12-23 2012-06-27 首钢总公司 Hot rolled ferrite/martensite double phase steel and production method thereof
CN102605254A (en) * 2012-04-18 2012-07-25 江苏省沙钢钢铁研究院有限公司 Hot-rolled dual-phase steel medium plate for building structure, and production method thereof
CN102912244A (en) * 2012-10-23 2013-02-06 鞍钢股份有限公司 780MPa-grade tensile strength hot rolling double-phase steel plate and manufacture method thereof
CN105483545A (en) * 2014-09-19 2016-04-13 鞍钢股份有限公司 800MPa level hot-rolling high broaching steel plate and manufacturing method thereof
CN105506476A (en) * 2014-09-26 2016-04-20 鞍钢股份有限公司 600 MPa-grade highly-chambered steel plate for automotive chassis and manufacturing method thereof
CN104593677B (en) * 2015-01-19 2017-10-10 唐山钢铁集团有限责任公司 Think gauge hot-rolled dual-phase steel DP600 production technology
CN104593677A (en) * 2015-01-19 2015-05-06 唐山钢铁集团有限责任公司 Production process of heavy gauge hot-rolled dual-phase steel DP600
CN105543674A (en) * 2015-12-18 2016-05-04 东北大学 Method for manufacturing cold-rolled ultrahigh-strength dual-phase steel with high local forming performance
CN106119703A (en) * 2016-06-21 2016-11-16 宝山钢铁股份有限公司 A kind of 980MPa level hot-rolled dual-phase steel and manufacture method thereof
CN106119703B (en) * 2016-06-21 2018-01-30 宝山钢铁股份有限公司 A kind of 980MPa levels hot-rolled dual-phase steel and its manufacture method
CN106834915A (en) * 2016-12-06 2017-06-13 内蒙古包钢钢联股份有限公司 800MPa grades of hot-rolled dual-phase steel of 2 ~ 4mm thickness and its processing 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
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
CN112246868A (en) * 2020-08-20 2021-01-22 唐山钢铁集团有限责任公司 Production method of substrate for cold rolling of 700 Mpa-level high-strength checkered plate
CN111982956A (en) * 2020-08-27 2020-11-24 广东韶钢松山股份有限公司 Method for determining elimination of ultra-low carbon steel mixed crystal structure based on thermal simulation testing machine
CN111982956B (en) * 2020-08-27 2023-09-05 广东韶钢松山股份有限公司 Method for determining ultra-low carbon steel mixed crystal structure elimination based on thermal simulation testing machine
CN112375979A (en) * 2020-10-31 2021-02-19 日照钢铁控股集团有限公司 Process for hot rolling thin steel plate with 800 MPa-level tensile strength, high plasticity and low cost
CN114086084A (en) * 2021-11-04 2022-02-25 湖南华菱涟钢特种新材料有限公司 Hot-rolled dual-phase steel and preparation method thereof

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Application publication date: 20100602