CN102560250A - Ultralow-carbon bainite steel plate and manufacturing method thereof - Google Patents

Ultralow-carbon bainite steel plate and manufacturing method thereof Download PDF

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CN102560250A
CN102560250A CN2011103834783A CN201110383478A CN102560250A CN 102560250 A CN102560250 A CN 102560250A CN 2011103834783 A CN2011103834783 A CN 2011103834783A CN 201110383478 A CN201110383478 A CN 201110383478A CN 102560250 A CN102560250 A CN 102560250A
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张爱文
焦四海
白岩
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Baoshan Iron and Steel Co Ltd
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Abstract

The invention relates to an ultralow-carbon high-strength high-toughness bainite steel plate with yield strength of 690MPa or more, which comprises the following components in percentage by weight: less than or equal to 0.03 percent of C, less than or equal to 0.15 percent of Si, 1.2-1.6 percent of Mn, less than or equal to 0.015 percent of P, less than or equal to 0.010 percent of S, 0.02-0.05 percent of Al, 0.02-0.04 percent of Nb, 0.005-0.020 percent of Ti, 0.04-0.06 percent of V, 0.45-0.70 percent of Cu, 0.30-0.50 percent of Ni, 0.0008-0.003 percent of B, less than or equal to 0.006 percent of N, and the balance of iron and inevitable impurities. The method for manufacturing the ultralow-carbon bainite steel plate comprises the following steps of: heating a continuous casting billet or a steel billet to a temperature of between 1,100 and 1,250 DEG C, rolling the continuous casting billet or the steel billet in an austenite re-crystallization area and a non-re-crystallization area, wherein the overall reduction rate is more than or equal to 70 percent, and the final rolling temperature is more than or equal to 860 DEG C; cooling to a temperature of between 250 and 350 DEG C with water in 15-50 DGE C/s, and performing air-cooling for 5 to 60 seconds; feeding the cooled steel plate into an online induction heat furnace, heating the steel plate in 1-10 DEG C/s to a temperature of between 500 and 600 DEG C, and tempering for 30 to 60 seconds; and discharging the steel plate from the furnace, and performing air-cooling on the steel plate. The prepared steel plate microstructure comprises the tempered ultralow-carbon bainite and a disperse precipitate. In the steel plate with thickness of between 6 and 25mm, the transverse yield strength is more than or equal to 690MPa, and the elongation A5 is more than or equal to 15 percent, longitudinal minus 40-DEG C Akv is more than or equal to 150J, the cold bending performance is excellent, and higher requirements on a high-strength high-toughness steel plate in the industries of bridges, pipelines, vessels, ships and the like are met.

Description

A kind of ultra-low-carbon bainite steel plate and method of manufacture thereof
Technical field
The present invention relates to a kind of high-intensity high-tenacity steel plate, relate to ultra-low-carbon bainite steel plate and the method for manufacture thereof of a kind of ys particularly more than or equal to 690MPa.Steel plate has good low-temperature toughness and large-line energy welding property, relates to the impact-resistant structural steel and iron of high-intensity high-tenacity that is used for bridge, pressurized vessel, boats and ships, automobile and other industries requirement, and the method for producing the high-intensity high-tenacity steel plate.
Background technology
ULCB is the good new steel grade of HS, H.T., welding property that gets up of development in recent years in the world; But be mainly used in the impact-resistant welded construction steel plate of high-intensity high-tenacity of bridge, pressurized vessel, boats and ships, automobile and other industries requirement; Traditional technology is added valuable alloying elements such as more Cu, Ni, Cr and Mo more when producing this steel grade, remedy the loss of strength because of adopting the Ultra-low carbon technological line to cause; Cost is higher, produces difficulty.Can adopt an amount of microalloy element to add controlled rolling during smaller or equal to the low-carbon bainite steel of 590MPa intensity rank and the suitable postcooling speed of rolling realizes target in the production ys; But when production high intensity levels and exigent welding property; Must adopt very low carbon content in order to reduce the Pcm index; Make carbon reach the ultralow-carbon rank; Usually smaller or equal to 0.03%, reduce by carbon that the loss of strength that causes must be added suitable Cu, Ni, Cr, the valuable alloying element precipitation strength of Mo remedies and suitable microalloy element Nb, V, Ti and controlled rolling and controlled cooling technology crystal grain thinning and precipitation strength remedies.In order in very wide transformetion range and speed of cooling scope, to obtain bainite structure, B becomes element indispensable in this type of steel.What deserves to be mentioned is all have the document of some low-carbon bainites or ultra-low-carbon bainite steel or patent to deliver in recent years both at home and abroad.China's Anshan iron and steel plant, Wuhan Iron and Steel Plant being all in technical the possessing some special knowledge in (surpassing) low-carbon bainite steel field, and have some patented technologies open, but produce with controlled rolling+accelerations cooling mostly, perhaps rolls the quick cooling+off-line tempering process production in back.
Development along with art such as bridge structure, pressurized vessel, boats and ships; Its requirement to the steel plate weldableness also significantly improves; Need steel plate can stand large-line energy welding, the welding heat input reaches more than the 20kJ/mm, and is high even will reach 200kJ/mm; Under high like this welding heat input condition, the impelling strength of the heat affected zone of steel plate must worsen.Traditional bridge, ship hull structure use plow-steel all are through adopting technologies such as controlled rolling, modified thermal treatment to obtain the cooperation that tissues such as acicular ferrite, bainite, tempered martensite reach high-intensity high-tenacity on the basis of low-carbon alloy steel.In order to ensure having enough hardening capacity than thick steel plates, need to add the alloying elements such as Ni, Cr, Mo of high level in the steel usually, the ys rank of steel is generally between 570-690MPa.At present, in the world about more existing documents of the method for manufacture of ys ULCB high-intensity high-tenacity steel plate and patent in the 690MPa left and right sides.
CN101787489A discloses a kind of easy-welding low-carbon bainitic steel and method of manufacture, and its chemical component weight percentage ratio is: C:0.02-0.08, Si:0.10-0.50, Mn:1.20-1.80; P≤0.015, S≤0.010, Al≤0.035, Mo:0.10-0.30; Nb:0.020-0.050, V:0.03-0.10, Ti:0.005-0.030, B:0.0005-0.002; N:0.005-0.010,0.005≤3N-10B≤0.015, Ti+V+10B>=8.525N.Adopt the production technique of electric furnace or converter smelting, external refining, continuous casting, controlled rolling and controlled cooling.550-600 ℃ of tempering, soaking time is 1min/mm * thickness of slab+30min, obtains ys >=550MPa, tensile strength >=670MPa, unit elongation >=20% ,-40 ℃ of Akv >=200J, nearly seam-40 ℃ of Akv >=100J in district during the 20-100kJ/cm welding.The ys and the tensile strength of this patent steel plate are on the low side, and adopt the off-line tempering, and tempering time is long, and the production cycle is long.
Still need ULCB high-intensity high-tenacity steel plate at present.
Summary of the invention
The object of the present invention is to provide the ULCB high-intensity high-tenacity steel plate, particularly 6-25mm Plate Steel of a kind of ys >=690MPa.
For realizing above-mentioned purpose; The ULCB high-intensity high-tenacity steel plate of ys>=690MPa of the present invention; Its composition (weight %) is: C≤0.03%, Si≤0.15%, Mn:1.2-1.6%, P≤0.015%, S≤0.010%, Al:0.02-0.05%, Nb:0.02-0.04%, Ti:0.005-0.020%, V:0.04-0.06%, Cu:0.45-0.70%, Ni:0.30-0.50%, B:0.0008-0.003%, N≤0.006%, surplus are iron and inevitable impurity.
Said steel plate be organized as tempering ULCB and disperse precipitate.
Another object of the present invention is to provide the method for manufacture of said ULCB high-intensity high-tenacity steel plate.
The method of manufacture of said ys 690MPa grade high-strength steel plate of the present invention may further comprise the steps:
(1) molten steel carries out continuous casting or die casting after vacuum outgas is handled, and need roll into steel billet through just after the die casting;
(2) continuously cast bloom or steel billet are rolling in carrying out more than three passages in austenite recrystallization district and non-recrystallization district after the 1100-1250 ℃ of heating, total draft >=70%, finishing temperature >=860 ℃;
(3) roll the back steel plate with the quick water-cooled of 15-50 ℃/s to 250-350 ℃ of temperature range air cooling 5-60s;
(4) the refrigerative steel plate gets into online induction heater and quickly heats up to 500-600 ℃ of tempering 30-60s with 1-10 ℃/s, the air cooling of coming out of the stove then.
The present invention obtains to be organized as the high-intensity high-tenacity steel plate of tempering ULCB+disperse precipitate through appropriate ingredients design and heating, rolling and roll back cooling and online short period of time tempering process fast.6-25mm Plate Steel ys >=690MPa, unit elongation A5 >=15% ,-40 ℃ of Akv >=150J, cold-bending property is good, has satisfied the high requirement of industries such as bridge, pipeline, container, boats and ships to the high-intensity high-tenacity steel plate.
Description of drawings
Fig. 1 is the metallographic structure photo of the embodiment of the invention 1 steel plate.
Fig. 2, the 3rd, the metallographic structure photo of the embodiment of the invention 3 steel plates.
Fig. 4 is the metallographic structure photo of the embodiment of the invention 5 steel plates.
Embodiment
Below the present invention is carried out comparatively detailed explanation.
Among the present invention, unless otherwise, content all refers to weight percent content.
For realizing the ULCB high-intensity high-tenacity steel plate that a kind of ys >=690MPa is provided of the present invention; The purpose of 6-25mm Plate Steel particularly; Be not subject to any theory, the selection of main chemical compositions of the present invention and control reason are described below:
Carbon: guarantee the key element of armor plate strength, it can significantly improve the hardening capacity of steel plate.But for the steel plate that will obtain to be organized as ULCB, carbon needs significantly to reduce.Carbon equivalent and welding crack Sensitivity Index Pcm that carbon reduces the back steel plate will correspondingly reduce, and toughness also can correspondingly significantly improve.Loss of strength after carbon reduces need be leaned on other alloying element to add and remedied.After carbon significantly reduced, steel plate was fit to the large-line energy welding.For ys 690MPa intensity rank of the present invention,, adopt low-down carbon content≤0.03% in order to obtain higher low-temperature impact toughness.Preferably, carbon content is 0.015-0.030%.
Silicon: add silicon in the steel and can improve purity of steel and deoxidation.Silicon plays the solution strengthening effect in steel.But the oxide debris viscosity when the too high meeting of silicone content makes the steel plate heating is bigger, the back de-scaling difficulty of coming out of the stove, and the red oxide debris of surface of steel plate is serious after causing rolling, and surface quality is relatively poor.And high silicon is unfavorable for welding property.Take all factors into consideration the influence of silicon each side, silicone content of the present invention is smaller or equal to 0.15%.Preferably, silicone content is 0.03-0.15%.
Manganese: manganese stable austenite tissue, its ability is only second to alloying element nickel, is cheap stable austenite and reinforced alloys element, and manganese increases the hardening capacity of steel simultaneously, reduces the critical cooling rate that martensite forms.But manganese has higher segregation tendency, so its content can not be too high, manganese content is no more than 2.0% in the general low-carbon micro steel-alloy.The add-on of manganese depends primarily on the intensity rank of steel.The content of manganese of the present invention should be controlled at 1.2-1.6%.Manganese in steel also and aluminium play the effect of deoxidation together jointly.Preferably, manganese content is 1.21-1.60%.
Sulphur and phosphorus: sulphur forms the plastic occluded foreignsubstance manganese sulfide with chemical combination such as manganese in steel, especially unfavorable to the horizontal plastic property and the toughness of steel, so the content of sulphur should be low as much as possible.Phosphorus also is the harmful element in the steel, the plasticity of heavy damage steel plate and toughness.For the present invention, sulphur and phosphorus all are unavoidable impurities elements, should be low more good more, consider the steel-making level that steel mill is actual, and the present invention requires P≤0.015%, S≤0.010%.Preferably, P≤0.011%, S≤0.005%.
Aluminium: strong deoxidant element.Low as best one can in order to guarantee the oxygen level in the steel, the content of aluminium is controlled at 0.02-0.05%.Unnecessary aluminium and the nitrogen element in the steel can form the AlN precipitate after the deoxidation, improve intensity and the element autstenitic grain size of ability refinement steel when thermal treatment heat.Preferably, aluminium content is 0.02-0.045%.
Titanium: titanium is the strong carbide forming element, and the Ti that adds trace in the steel helps the N in the fixing steel, and austenite crystal was within reason when the TiN of formation can make the steel billet heating rises greatly by refinement original austenite grains degree.Titanium also can become TiC, TiS, Ti with carbon with the sulfuration symphysis respectively in steel 4C 2S 2Deng, they with inclusion with second mutually the form of particle exist.These carbonitride precipitates of titanium also can stop the heat affected zone grain growth when welding, improve welding property.At present, little titanium is handled the common process that has become most of HSLA.Titanium content of the present invention is controlled at 0.005-0.020%.Preferably, titanium content is 0.012-0.018%.
Niobium and vanadium: niobium and vanadium all are the strong carbide forming elements, and the niobium that adds trace in the steel can significantly improve the recrystallization temperature of steel, cooperates the interpolation of B, and recrystallization temperature can improve again, and the tissue of refine austenite crystal grain and phase transformation subsequently improves toughness and intensity.Niobium can be separated out tiny carbide in the operation of rolling He in the subsequent cooling process, improve intensity.But vanadium is precipitation strength also, add in this steel niobium and vanadium syllabus be to remedy the very low loss of strength that causes of carbon, and be beneficial to crystal grain thinning, raising impelling strength.Content of niobium of the present invention is controlled at 0.02-0.04%, and content of vanadium is controlled at 0.04-0.06%.Preferably, content of niobium is 0.031-0.040%; Content of vanadium is 0.045-0.058%.
Copper: Cu can play the precipitation strength effect in steel, and can not worsen the toughness of steel, so the present invention adds the copper of 0.45-0.70%.Preferably, copper content is 0.46-0.69%.
Nickel: add nickel in the steel and especially in quenched and tempered steel, add especially low-temperature flexibility of toughness that nickel can significantly improve steel; Simultaneously owing to added Cu in the steel; In order to prevent to heat or hot cracking tendency when rolling; The nickel that need to add a certain amount of (more than or equal to copper content half the) is so the present invention adds the nickel element of 0.30-0.50%.Preferably, nickel content 0.30-0.49%.
Boron: improve the hardening capacity of steel, suppress austenite, make steel in very big speed of cooling scope, all can form bainite structure to ferritic and pearlitic transformation.The interpolation of the boron combination niobium of trace is that the recrystallization temperature of steel significantly improves, and the content of boron is 0.0008-0.003% in this steel.Preferably, the content of boron is 0.0015-0.0025%.
Nitrogen: the present invention has added minor N b, V, Ti microalloy element, and is main schedule of reinforcement with phase transformation strengthening and the precipitation strength of tempering carbide mainly.The titanium that can stablize 0.005-0.02% smaller or equal to the nitrogen of 60ppm content forms TiN, and the austenite crystal of slab was within reason thick when this TiN can guarantee heating.Nb, the main formation carbide precipitation strength that combines with C of V.Control nitrogen content≤0.006% among the present invention.Preferably, nitrogen content is 0.0036-0.0045%.
Process for making is to the influence of product of the present invention:
Bessemerize and vacuum-treat: purpose is to guarantee the basal component requirement of molten steel, obnoxious flavoures such as the oxygen in the removal steel, hydrogen, and add necessary alloying element such as manganese, titanium, carry out the adjustment of alloying element.
Continuous casting or die casting: guarantee that all even surface quality of strand internal component is good, the steel ingot of die casting need be rolled into steel billet.
Heating and rolling: continuously cast bloom or steel billet heat under 1100-1250 ℃ temperature, obtain uniform austenitizing tissue on the one hand, and the compound of alloying elements such as niobium, vanadium, titanium is partly dissolved.Carry out more than three passages in austenite recrystallization district and non-recrystallization district rolling, total draft >=70%, finishing temperature >=860 ℃ (preferred 860-890 ℃);
Fast cooling: roll the back steel plate with the cooling rate water-cooled of 15-50 ℃/s to 250-350 ℃ of air cooling 5-60s; In quick process of cooling, most alloying element is solidly soluted in the bainite.
Online tempering: the refrigerative steel plate gets into online induction heater and quickly heats up to 500-600 ℃ of tempering 30-60s with 1-10 ℃/s, the air cooling of coming out of the stove then.Tempering help to eliminate the internal stress that produces when quenching and eliminate in the lath of bainite or between tiny crack, part copper particle and carbide reinforced is separated out in disperse, improves strong plastotype, toughness and cold-bending property.
The present invention through appropriate ingredients design, heating, controlled rolling, roll back fast cooling and online induction heating tempering; Make steel plate realize refined crystalline strengthening, phase transformation strengthening, precipitation strength; Intensity, the hardness of steel plate have been improved; Have very high low-temperature flexibility, tissue is rendered as tempering ULCB+disperse precipitate.6-25mm Plate Steel ys >=690MPa, unit elongation A5 >=15%, vertical-60 ℃ of Akv >=200J, cold-bending property is good, can be used for the high requirement of industries such as bridge, pipeline, container, boats and ships to the high-intensity high-tenacity steel plate.
Embodiment
Below with embodiment the present invention is made more detailed description.These embodiment only are the descriptions to best mode for carrying out the invention, scope of the present invention are not had any restriction.
Embodiment 1
To smelt the molten steel of accomplishing by table 1 proportioning and after vacuum outgas is handled, carry out continuous casting or die casting, slab thickness 80mm, the gained blank is after 1200 ℃ of heating; Rolling through multi-pass in the austenite recrystallization temperature scope; Be rolled into the steel plate that thickness is 6mm, total draft 94%, finishing temperature is 880 ℃; Quickly heat up to 500 ℃ of tempering so that 50 ℃/s water-cooled to 250 is ℃ online more then, air cooling is to room temperature then;
Detailed composition and the processing parameter of embodiment 2-5 are seen table 1 and 2, and embodiment gained plate property is seen table 3.
The chemical ingredients of table 1 embodiment of the invention 1-5, Ceq (wt%) and welding crack Sensitivity Index
Pcm
Figure BDA0000112481490000071
*Ceq=C+Mn/6+(Cr+Mo+V)/5+(Ni+Cu)/14
P CM=C+Si/30+Mn/20+Cu/20+Ni/60+Cr/20+Mo/15+V/10+5B
The heating of table 2 embodiment of the invention 1-5, rolling, cooling, tempering related process parameter and steel plate thickness
Figure BDA0000112481490000072
Test Example 1: the mechanical property of steel plate
According to ys, tensile strength, unit elongation ,-40 ℃ of mechanical properties such as impelling strength of GB/T228-2002 metallic substance tensile test at room temperature method, GB 2106-1980 metal Charpy V test method mensuration embodiment of the invention 1-5 steel plate, its result sees table 3.According to GB/T232-2010 metallic substance bend test method, embodiment of the invention 1-5 steel plate is carried out horizontal clod wash d=2a, 180 ° of tests, its result sees table 3.
The mechanical property of table 3 steel plate of the present invention and tissue
Figure BDA0000112481490000073
Test Example 2: metallographic structure
Utilize the metallographic structure of light microscope determining embodiment of the invention steel plate, its result sees table 3, is tempering ULCB and disperse precipitate.
Fig. 1 is the metallographic structure photo of the embodiment of the invention 1 steel plate.
Fig. 2, the 3rd, the metallographic structure photo of the embodiment of the invention 3 steel plates.
Fig. 4 is the metallographic structure photo of the embodiment of the invention 5 steel plates.
Other embodiment also can obtain similar metallographic structure photo.
Visible from figure, steel plate of the present invention be organized as tempering ULCB and disperse precipitate.
Can find out from above embodiment, adopt above-mentioned composition and processing parameter to process, the ys >=690MPa of the thick finished product steel plate of 6-25mm; Unit elongation A5 >=15%;-40 ℃ of Akv >=150J, cold-bending property is good, and tissue is rendered as tempering ULCB+disperse precipitate.Steel plate has satisfied the high requirement of relevant industries to the high-intensity high-tenacity steel plate.Product is applicable to industries such as bridge, pipeline, container, boats and ships, is with a wide range of applications and market outlook.

Claims (20)

1. steel plate; Its weight percent composition is: C≤0.03%, Si≤0.15%, Mn:1.2-1.6%, P≤0.015%, S≤0.010%, Al:0.02-0.05%, Nb:0.02-0.04%, Ti:0.005-0.020%, V:0.04-0.06%, Cu:0.45-0.70%, Ni:0.30-0.50%, B:0.0008-0.003%, N≤0.006%, surplus are iron and inevitable impurity.
2. steel plate as claimed in claim 1 is characterized in that carbon equivalent Ceq:0.30-0.40.
3. according to claim 1 or claim 2 steel plate is characterized in that, said steel plate be organized as tempering ULCB and disperse precipitate.
4. like the arbitrary described steel plate of claim 1-3, it is characterized in that steel plate thickness is 6-25mm.
5. like the arbitrary described steel plate of claim 1-4, it is characterized in that the ys >=690MPa of steel plate, unit elongation A5 >=15% ,-40 ℃ of Akv >=150J.
6. like the arbitrary described steel plate of claim 1-5, it is characterized in that C:0.015-0.030%.
7. like the arbitrary described steel plate of claim 1-6, it is characterized in that Si:0.03-0.15%.
8. like the arbitrary described steel plate of claim 1-7, it is characterized in that Mn:1.21-1.60%.
9. like the arbitrary described steel plate of claim 1-8, it is characterized in that P≤0.011%.
10. like the arbitrary described steel plate of claim 1-9, it is characterized in that S≤0.005%.
11., it is characterized in that Al:0.02-0.45% like the arbitrary described steel plate of claim 1-10.
12., it is characterized in that Nb:0.031-0.04% like the arbitrary described steel plate of claim 1-11.
13., it is characterized in that Ti:0.012-0.018% like the arbitrary described steel plate of claim 1-12.
14., it is characterized in that V:0.045-0.58% like the arbitrary described steel plate of claim 1-13.
15., it is characterized in that Cu:0.46-0.69% like the arbitrary described steel plate of claim 1-14.
16., it is characterized in that Ni:0.30-0.49% like the arbitrary described steel plate of claim 1-15.
17., it is characterized in that B:0.0015-0.0025% like the arbitrary described steel plate of claim 1-16.
18., it is characterized in that N:0.0036-0.0045% like the arbitrary described steel plate of claim 1-17.
19. the method for manufacture like the arbitrary said steel plate of claim 1-18 comprises:
Molten steel carries out continuous casting or die casting after vacuum outgas is handled, need roll into steel billet through just after the die casting;
Continuously cast bloom or steel billet are rolling in carrying out more than three passages in austenite recrystallization district and non-recrystallization district after the 1100-1250 ℃ of heating, total draft >=70%, finishing temperature >=860 ℃;
Roll the back steel plate with 15-50 ℃/s water-cooled to 250-350 ℃ of temperature range air cooling 5-60s;
The refrigerative steel plate gets into online induction heater and is heated to 500-600 ℃ of tempering 30-60s with 1-10 ℃/s, the air cooling of coming out of the stove then.
20. method as claimed in claim 19 is characterized in that, finishing temperature is 860-890 ℃.
CN2011103834783A 2011-11-25 2011-11-25 Ultralow-carbon bainite steel plate and manufacturing method thereof Pending CN102560250A (en)

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Cited By (3)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN103695783A (en) * 2013-12-23 2014-04-02 钢铁研究总院 Ultra-low carbon bainite high-strength steel bar and production method thereof
WO2017206419A1 (en) * 2016-05-31 2017-12-07 江阴兴澄特种钢铁有限公司 Low-compression-ratio ultra-thick eh36 ship plate steel and method for preparing same
CN108296285A (en) * 2018-02-01 2018-07-20 湖南华菱湘潭钢铁有限公司 A kind of milling method of ultralow-carbon bainite steel plate

Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN1330166A (en) * 2001-06-26 2002-01-09 宝山钢铁股份有限公司 Microalloyed low-carbon bainite ferrite steel and its preparing process
CN101163807A (en) * 2005-03-17 2008-04-16 住友金属工业株式会社 High tension steel plate, welded steel pipe and method for production thereof
CN101255528A (en) * 2007-02-26 2008-09-03 宝山钢铁股份有限公司 Niobium-containing steel plate with excellent ultralow-temperature flexibility and rolling method thereof
CN101622370A (en) * 2007-03-05 2010-01-06 新日本制铁株式会社 Thick high-strength steel plate and process for producing the same

Patent Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN1330166A (en) * 2001-06-26 2002-01-09 宝山钢铁股份有限公司 Microalloyed low-carbon bainite ferrite steel and its preparing process
CN101163807A (en) * 2005-03-17 2008-04-16 住友金属工业株式会社 High tension steel plate, welded steel pipe and method for production thereof
CN101255528A (en) * 2007-02-26 2008-09-03 宝山钢铁股份有限公司 Niobium-containing steel plate with excellent ultralow-temperature flexibility and rolling method thereof
CN101622370A (en) * 2007-03-05 2010-01-06 新日本制铁株式会社 Thick high-strength steel plate and process for producing the same

Cited By (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN103695783A (en) * 2013-12-23 2014-04-02 钢铁研究总院 Ultra-low carbon bainite high-strength steel bar and production method thereof
WO2017206419A1 (en) * 2016-05-31 2017-12-07 江阴兴澄特种钢铁有限公司 Low-compression-ratio ultra-thick eh36 ship plate steel and method for preparing same
CN108296285A (en) * 2018-02-01 2018-07-20 湖南华菱湘潭钢铁有限公司 A kind of milling method of ultralow-carbon bainite steel plate
CN108296285B (en) * 2018-02-01 2019-07-30 湖南华菱湘潭钢铁有限公司 A kind of milling method of ultralow-carbon bainite steel plate

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Application publication date: 20120711