CN103866204A - Large-strain X80 dual-phase steel plate produced by virtue of process at low temperature and under high pressure - Google Patents
Large-strain X80 dual-phase steel plate produced by virtue of process at low temperature and under high pressure Download PDFInfo
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Abstract
The invention belongs to the field of the low-alloy high-strength pipeline steel and more specifically relates to a large-strain X80 dual-phase steel plate produced by virtue of a process at a low temperature and under a high pressure. The large-strain X80 dual-phase steel plate is composed of the following components in percentage by weight: 0.05-0.07% of C, 0.25-0.35% of Si, 1.40-1.80% of Mn, less than or equal to 0.01% of P, less than or equal to 0.003% of S, 0.01-0.04% of Nb, 0.01-0.02% of Ti, less than or equal to 0.035% of Mo, less than or equal to 0.30% of Cu, less than or equal to 0.035% of Cr, less than or equal to 0.030% of Ni, less than or equal to 40ppm of N, less than or equal to 20ppm of O, less than or equal to 1.2ppm of H and the balance of Fe and inevitable impurities. The large-strain X80 dual-phase steel plate has the beneficial effects that the steel plate is subjected to accelerated cooling by virtue of high-pressure water in the adopted rolling process so that the crystalline grain are effectively refined and the production efficiency is improved, and multi-pass cooling and rolling at a low temperature and under high pressure are not carried out in a non-recrystallization zone, and finally, a proeutectoid ferrite-lath bainite structure is obtained, the obtained steel plate has the yield strength Rt0.5 of 480-560MPa, the tensile strength Rm of 770-800MPa, the yield ratio Rt0.5/Rm being less than or equal to 0.75, the Charpy impact energy at -20 DEG C being greater than or equal to 350J, the drop shear area at -15 DEG C being greater than or equal to 95% and the Uniform elongation UEL being greater than or equal to 12, and the steel plate is high in anti-deforming capability, and furthermore, the stress ratios of the steel plate are as follows: Rt2.0/Rt1.0 is greater than or equal to 1.09 and Rt1.5/Rt0.5 is greater than or equal to 1.15.
Description
Technical field
The invention belongs to low-alloy high-strength pipe line steel manufacturing technology field, the large strain X80 dual phase sheet steel that the large soft reduction process of a kind of low temperature is produced more specifically.
Background technology
Along with the fast development of China's oil petrochemical industry, within one period from now on, country is by newly-built a large amount of pipe laying, to meet the development need of national economy, increasing pipeline service condition is more harsh from now on, geologic media becomes increasingly complex, also more and more higher to the specification of quality of pipe line steel.Because pipe-line constantly extends to permafrost or seismic region, in the time laying the line in these regions, stratum is moved and may be caused the larger strain of steel pipe, and therefore, pipe line steel used must have the deformability of the local bending of preventing and the fracture of pipeline butt girth welding seam.Improving the transportation pipe line method of steel pipe non-deformability is the wall thickness that increases steel pipe, but this certainly will increase the construction cost of pipe, and employing has high deformability steel pipe and can under the prerequisite that does not increase wall thickness, obtain high steel pipe non-deformability.
The tissue of high-performance pipe line steel has experienced the transformation of the types of tissue such as ferrite-pearlite type, acicular ferrite type, granular bainite type and lower bainite type.Research both at home and abroad shows, dual phase microstructure by hard phase and relative soft phase composite can obtain larger strain hardening performance, Japan and other countries iron and steel enterprise has developed ferrite+bainite and bainite+martensite (MA) two class large-deformation-resistance pipeline steels, current domestic steel mill and pipe factory have successfully developed X70 grade of steel large-deformation-resistance pipeline steel, and be successfully applied to middle remote Sweet natural gas/crude oil pipeline engineering, realize large-deformation-resistance pipeline steel production domesticization.
In recent years, particularly Central Asia pipe line steel is laid, for improving the safety performance of air input efficiency and petroleum transport, the over-all propertieies such as higher category, thicker, toughness index require higher based on the X80 large-strain pipeline steel of stress design principle favored, increasing experts and scholars research and analyse
For meeting the requirements such as X80 pipeline steel strength, toughness, anti-strain property, weldability, even intensity, must at the beginning of production technique and Composition Design, just formulate according to large-deformation-resistance pipeline steel standard, adopt these technology that safe and reliable system can be provided, guarantee economic solution, the novelty design based on stress design has solved the practical problems of high-strength line-pipe steel application in engineering is carried simultaneously.The present invention is directed to many difficult problems of producing in large-deformation-resistance pipeline steel project, in conjunction with on-the-spot production practice and tooling, adopt suitable controlled rolling, Controlled cooling process (TMCP technique), steel plate is finally obtained soft, hard duplex structure type, and strictly control soft, hard phase constitution ratio, by soft, hard dual phase microstructure obtains larger strain hardening performance, form the efficient and rational process control technology of advanced person of depressing greatly rolling and laminar flow cooling technology process control from Composition Design to low temperature, realize the stable of large-deformation-resistance pipeline steel plate, produce in enormous quantities.For advancing production domesticization, the large-scale industrial production of large-deformation-resistance pipeline steel to play the effect of positive important.
The research of the distortion X80 of the relevant Chinese People's Anti-Japanese Military and Political College of JFE company of Japan hot-rolled steel sheet, but the tissue of the Japanese distortion X80/X100 of Chinese People's Anti-Japanese Military and Political College steel plate is designed to bainite+Ma Ao island (B+M/A) duplex structure, technological design is TMCP+HOP technique, therefore Chinese People's Anti-Japanese Military and Political College's distortion X80/X100 Pipeline Steel Plate that they are produced obtains by HOP technique, their tissue is to be made up of bainite+Ma Ao island (B+M/A) dual phase microstructure, HOP process characteristic is steel plate carrying out corresponding thermal treatment process through directly entering equipment for Heating Processing after finish rolling system, the armor plate strength of producing under this processing condition is stable, performance inconsistency little but processability and poor toughness, and the domestic this duplex structure filing an application can obtain by the multicomponent microalloying design of low C and the large Reduction Technology of low temperature, duplex structure is made up of ferrite+ferrite bainite dual phase microstructure, can realize the matched well of armor plate strength and toughness.
The patent of invention comparatively close with the present invention has: 1) Chinese patent, application (patent) number: CN200910076066.8, a kind of method of producing X80 level large-deformation resistance pipe line steel plate of moderate thickness; 2) Chinese patent, application (patent) number: 201310022403.1, a kind of method of obtaining X80 steel-grade duplex structure gross distortion pipe line steel; 3) Chinese patent, application (patent) number: 20121003018.8, a kind of low-cost and high-performance X80 pipe line steel and production method thereof; 4) Chinese patent, application (patent) number: 201010530202.9, a kind of low cost, high tenacity X80 large-deformation-resistance pipeline steel and production method; 5) Chinese patent, application (patent) number: 200910048140.5, Wide and Thick Slab and manufacture method thereof for a kind of X80 pipe line steel; 6) Chinese patent, application (patent) number: 201310230259.0, a kind of production method of X80 pipe line steel; 7) Chinese patent, application (patent) number: 200610096513.2, manufacturing technique of low compression ratio high grade pipe line steel.
In above patent documentation 1), 2), 4), 7) be the X80 pipe line steel based on stress design, there is property of resisting large deformation, all the other Jun Shi single organization pipe line steels.1) in the product composition design of announcing, P content maximum value is 0.012%, S content maximum value 0.004%, and carbon content is 0.02 ~ 0.05, and yield tensile ratio is not more than 0.80, uniform elongation >=10%, and thickness of strand is 230mm, rolling adopts conventional two stage rolling; 2) the products production parameter process of announcing is mainly to obtain in laboratory simulation experiment; 4) recrystallization zone rolling pass rate >=60% in the Product Process of announcing, finish rolling start rolling temperature is 880 ℃ ~ 950 ℃, product performance yield tensile ratio is not more than 0.80, and uniform elongation >=10% is above or all have certain defect in the performance of steel plate purity, steel plate or in production technique.
Summary of the invention
Goal of the invention of the present invention is for above deficiency, a kind of low temperature large strain X80 dual phase sheet steel that large soft reduction process is produced is provided, improving situ production efficiency and reducing under the prerequisite of cost of alloy, produce and there is excellent block hammer performance, low yield tensile ratio, the X80 two-phase Pipeline Steel Plate of the high over-all properties such as stress ratio and uniform elongation, P content maximum value 0.010% in product composition design of the present invention, S content maximum value 0.003%, steel is purer, more than after technology implementation ,-20 of steel plate ℃ of Charpy-V impact powers reach 350J,-15 ℃ of shear area >=95% that drop hammer, uniform elongation UEL >=12, in Composition Design, adopt low niobium chromatize Composition Design simultaneously, guaranteeing under the prerequisite of plate property, effectively save adding of precious alloy molybdenum, on rolling technology, the ingenious high pressure water that utilizes is to laminar cooling process, effectively crystal grain thinning and enhancing productivity, adopt super thick intermediate blank, effectively alleviate roughing mill burden, non-recrystallization district adopts low temperature to depress greatly multi-pass cold rolling, take into account plate property and rhythm of production, large-scale industrial production preferably.
The present invention is achieved by the following technical solutions:
The large strain X80 dual phase sheet steel that the large soft reduction process of low temperature is produced, it is made up of following component by weight percentage, C:0.05 ~ 0.07%, Si:0.25 ~ 0.35%, Mn:1.40 ~ 1.80%, P≤0.01%, S≤0.003%, Nb:0.01 ~ 0.04%, Ti:0.01 ~ 0.02%, Mo≤0.35%, Cu≤030%:Cr≤0.35%, Ni≤0.030%, N≤40ppm, O≤20ppm, H≤1.2ppm rest part comprises Fe and inevitable impurity.
The chemical composition of described steel plate meets: Pcm=C+Si/30+Ni/60+ (Mn+Cr+Cu)/20+Mo/15+V/10+5B≤0.20%.
In its Composition Design, the effect of each element is as follows:
C: carbon is that improving intensity main is also the most cheap element, along with the increase of carbon content, the strength increase of steel, but welding property and the plasticity and toughness variation of while steel plate, therefore the present invention selects low-carbon (LC) Composition Design, makes steel plate have good plasticity and toughness and good welding property.
Mn: manganese is the effective element that improves intensity and toughness, and it is weak carbide forming element, its effect in smelting is deoxidation and the impact of eliminating sulphur, can also reduce austenite transformation temperature, refinement ferrite crystal grain is useful to improving armor plate strength and toughness; Simultaneously can also solution strengthening ferrite and increase the hardening capacity of steel; Under low-carbon (LC) condition, it has significant promoter action to bainite transformation; But when Mn too high levels, hardening of steel and ductility degenerates; Mn is because of its successful, with low costly in quality plate is produced, becomes one of main interpolation element.
Si: silicon plays the effect of reductor has solution strengthening effect simultaneously, can also delay greatly the formation of carbide, and growing up of hysteresis cementite, has increased stabilization of austenite; But Si content is high, and steel grade is prone to inclusion, and steel easily get rusty, in hot rolling production, iron rust is easily rolled into steel plate top layer, pot galvanize poor performance, and Si demonstrates local brittle zone when multithreading is welded simultaneously hazardness.
Cu: the precipitation strength of copper is to improve the important means of intensity of steel, in addition, the solidity to corrosion of Cu to steel, improves weldability, low-temperature flexibility, formability and machinability etc. and is highly profitable; But on the other hand, when Cu content is high, easily crack when continuous casting steel billet heating or hot rolling, worsen surface of steel plate performance, must add appropriate Ni to stop the generation of this crackle according to the difference of intensity rank and steel plate thickness.
Ni: nickel does not have detrimentally affect to welded heat affecting zone hardening and toughness, can make again the intensity of mother metal improve, and low-temperature flexibility is improved greatly; But it is compared with noble element, cause the cost of steel significantly to rise, less economical; The object of adding Ni element in steel is mainly to stop containing Cu to measure high steel billet in heating or the tendency that cracks when hot rolling; According to the content of Cu, Ni content is controlled to 0.7-1 times of Cu content.
Ti: adding micro-titanium, is for the nitrogen element in fixing steel; Ti has strong precipitation strength effect in addition, can improve the intensity of steel, the influence that the hardness at welded heat affecting zone place has also been had in the best condition, the grain coarsening that the existence of the nitride particles of Ti can suppress welded heat affecting zone stops steel billet the growing up of crystal grain in heating, rolling, welding process, improves the toughness of mother metal and welded heat affecting zone; Ti is lower than 0.005% time, Gu N weak effect, while exceeding 0.03%, Gu N effect reaches capacity, superfluous Ti can separately or form carbonitride together with Nb, strengthening steel, but form sometimes the precipitated phase of bulk, will make the toughness deterioration of steel; In the time that the ratio of the Ti in steel, N atom is 1:1, the most tiny and distribution disperse of TiN particle, the strongest to the refining effect of high temperature austenite crystal grain, not only can obtain good toughness, and can realize Large Heat Input Welding more than 30KJ/cm; But too much Ti content can cause the alligatoring of the nitride of titanium, unfavorable to low-temperature flexibility; Therefore, generally by Ti Composition Control in 0.02% left and right.
Cr: the interpolation of chromium can reduce the transformation temperature of steel grade, thinning microstructure, effectively improves intensity, can also improve steel grade oxidation-resistance and high temperature corrosion-resisting performance etc., but Cr crosses and separates out at most thickly, causes the embrittlement of steel, bad to welding property, therefore Cr content be designed to≤0.30%.
Another object of the present invention is to provide the manufacture method of the large strain X80 Pipeline Steel Plate of the large soft reduction process production of a kind of low temperature, the method is on the basis of mentioned component design, by controlling slab heating temperature and heat-up time, adopt the low temperature of brand-new thick intermediate blank to depress greatly multi-pass rolling technique, obtain the hot rolling X80 dual phase sheet steel with good obdurability and property of resisting large deformation.
The production craft step that this invention adopts is: get the raw materials ready → molten iron KR desulfurization processing → converter smelting → CAS Argon → LF+RH duplex practice refining → sheet billet continuous casting → slab reheats → laterally broadening → longitudinally moulding → finish rolling → pre-straightening → ACC pattern laminar flow cooling → aligning → stacking slow cooling → UT (Ultrasonic Testing) operation.
Smelting steel process control alloying element addition sequence of the present invention: Nb, Ti are more valuable alloying elements, after vacuum-treat later stage or vacuum-treat, add again, can greatly improve microalloy element specific absorption on the one hand, also can reduce the content of hydrogen in steel simultaneously.
The manufacture method of the large strain X80 dual phase sheet steel that the large soft reduction process of above-mentioned a kind of low temperature is produced, its concrete steps are:
(1) after raw material molten iron KR pre-treatment, through converter smelting, send into the refining of LF refining furnace after ladle argon-blown again, then in VD stove, carry out vacuum-treat, protect vacuum time 20 minutes, processing finishes rear feeding calcium iron wire 2m/t, soft blow argon 10 minutes after line feeding;
(2) upper continuous caster cast after VD stove vacuum breaker, stacking slow cooling 48 hours after strand rolls off the production line;
(3) strand is through process furnace soaking, strand time inside furnace 4-5 hour, and tapping temperature is 1110-1130 ℃, after coming out of the stove, carries out dephosphorize by high pressure water, removes oxidized iron sheets on surface of casting blank, after dephosphorization, casting blank surface temperature is controlled at 1040 ℃ ~ 1050 ℃;
(4) horizontal-vertical rolling mode is selected in strand rolling, first the continuously cast bloom after dephosphorization is carried out to horizontal broadening and longitudinally moulding, laterally broadening rolling 4 passages, every time draft >=12%, accumulative total draft >=40%, longitudinally formation rolling 1 passage, percentage pass reduction >=16%, longitudinally formation rolling temperature is controlled at 950 ℃～1050 ℃, obtains intermediate blank.
(5) after longitudinally formation rolling finishes, utilize roughing mill high pressure water to carry out continuous de-scaling 3 passages that cool to intermediate blank, prevent that crystal grain time of staying temperature between roughing mill and finishing mill is long, grain growth, before each de-scaling is cooling, guarantee that intermediate blank temperature returns red, after cooling, strand temperature is controlled at 880 ℃～900 ℃, air cooling treats that temperature is to 820 ℃ of finish rolling, finish rolling adopts one-pass roller, rolling 14 passages, last 1 road is the empty passage of crossing, rolling mill speed is set to 1.0m/s, roller table speed 0.5 m/s after machine, finish rolling accumulative total percentage pass reduction >=75%, finishing temperature is controlled at 730 ℃～750 ℃,
(6) in described ACC pattern laminar flow is cooling, 21 ℃/S of the cooling target cooling rate of laminar flow, target final cooling temperature is below 200 ℃, water convexity bias :+15%; Edge part shading OS:40; DS:-40.
Water convexity refers to that water coolant uses than the water yield large in region intermediate in region, edges of plate, and uses the less water yield at center, and current present convex, become water convexity, and bias refers to that edge section is than the water yield of middle portion large 15%.
In above-mentioned steps (2), continuous caster casting process adopts Segment Electromagnetic Stirring and the light soft reduction process of strand.
In upper step (2), gained slab thickness is 250mm.
Described in above-mentioned steps (4), workpiece thickness is 120mm, to guarantee the large accumulative total of non-recrystallization district rolling draft;
The pressure of above-mentioned steps (3) and step (5) mesohigh water is 20Mp.
The invention has the beneficial effects as follows: P content maximum value 0.010% in product composition design of the present invention, S content maximum value 0.003%, steel is purer, in Composition Design, adopt low niobium chromatize Composition Design simultaneously, guaranteeing under the prerequisite of plate property, effectively save adding of precious alloy molybdenum, on rolling technology, the ingenious high pressure water that utilizes is to laminar cooling process, effectively crystal grain thinning and enhancing productivity, adopt super thick intermediate blank, effectively alleviate roughing mill burden, non-recrystallization district adopts low temperature to depress greatly multi-pass cold rolling, take into account plate property and rhythm of production, large-scale industrial production preferably, finally obtain proeutectoid ferrite+ferrite bainite tissue, gained steel plate yield strength Rt0.5 is 480MPa～560MPa, tensile strength Rm is 770MPa～800MPa, yield tensile ratio Rt0.5/Rm≤0.75,-20 ℃ of Charpy-V impact power >=350J,-15 ℃ of shear area >=95% that drop hammer, uniform elongation UEL >=12, steel plate non-deformability is strong, stress ratio is Rt2.0/ Rt1.0 >=1.09, Rt1.5/ Rt0.5 >=1.15.
Accompanying drawing explanation
Fig. 1 is the organization chart of the large strain X80 of the present invention dual phase sheet steel.
Embodiment
Further illustrate the present invention by following specific embodiment:
Embodiment mono-
The large strain X80 dual phase sheet steel that the large soft reduction process of low temperature of the present embodiment is produced is to be prepared from by the component of following mass percent: C:0.05%, Si:0.25%, Mn:1.7%, P:0.008%, S:0.002%, Cr:0.25%, Ni:0.022%, Ti:0.015%, Pcm=0.19, surplus is Fe and inevitable impurity.
The preparation method of the large strain X80 dual phase sheet steel that the large soft reduction process of low temperature of the present embodiment is produced is as follows:
1) smelting technology: after raw material molten iron KR pre-treatment, through 210t top and bottom combined blown converter smelting, send into again the refining of LF refining furnace after ladle argon-blown, then in VD stove, carry out vacuum-treat, protect vacuum time 20 minutes, processing finishes rear feeding calcium iron wire 2m/t, soft blow argon 10 minutes after line feeding;
2) casting process: upper 270mm × 2100mm sectional board billet continuous casting machine cast after VD stove vacuum breaker, in casting process, casting machine adopts Segment Electromagnetic Stirring and the light soft reduction process of strand, stacking slow cooling 48 hours after continuously cast bloom rolls off the production line;
3) heating process: strand time inside furnace 4.5 hours, 1120 ℃ of tapping temperatures, carry out 1 road dephosphorize by high pressure water after coming out of the stove, remove oxidized iron sheets on surface of casting blank, 1045 ℃ of casting blank surface temperatures after dephosphorization.
4) rolling technology: adopt horizontal broadening, longitudinally moulding and finish rolling rolling stage by stage, laterally broadening rolling 4 passages, 4 passages press down rate and are respectively 12.2%, 13.7%, 14.5% and 13.6%, add up draft 54%, longitudinally formation rolling 1 passage, percentage pass reduction 17%; 820 ℃ of finish rolling start rolling temperatures, mill product steel plate specification is 26.4mm, last pass accumulative total draft 76%.
6) after testing, the salient features of this example is as follows: Rt0.5 is 520MPa, and tensile strength Rm is 780MPa, yield tensile ratio Rt0.5/Rm=0.67, and ,-20 ℃ of Charpy-V impact powers are 356J, 380J, 387J;-15 ℃ of shear area=95% that drop hammer, 100%; Uniform elongation UEL=12.5, Rt2.0/ Rt1.0=1.10, Rt1.5/ Rt0.5=1.21.
Embodiment bis-
The large strain X80 dual phase sheet steel that the large soft reduction process of low temperature of embodiment is produced is to be prepared from by the component of following mass percent: C:0.065%, Si:0.23%, Mn:1.70%, P:0.010%, S:0.001%, Cr:0.22%, Ni:0.022%, Ti:0.015%, Pcm=0.18, surplus is Fe and inevitable impurity.
The preparation method of the large strain X80 dual phase sheet steel that the large soft reduction process of low temperature of the present embodiment is produced is with embodiment mono-, difference is that strand time inside furnace is 4 hours, 1048 ℃ of casting blank surface temperatures after dephosphorization, laterally broadening rolling 4 passages, 4 passages press down rate and are respectively 12.8%, 13.8%, 13.9% and 13.4%, accumulative total draft 53.9%, longitudinally formation rolling 1 passage, percentage pass reduction 17.7%, finish rolling accumulative total deformation rate is 77%.
After testing, the salient features of this example is as follows: Rt0.5 is 510MPa, and tensile strength Rm is 770MPa, yield tensile ratio Rt0.5/Rm=0.66, and-20 ℃ of Charpy-V impact powers are 348J, 385J, 365J;-15 ℃ of shear area=100% that drop hammer, 100%; Uniform elongation UEL=13.5, Rt2.0/ Rt1.0=1.12, Rt1.5/ Rt0.5=1.19.
Claims (8)
1. the large strain X80 dual phase sheet steel that the large soft reduction process of low temperature is produced, it is made up of following component by weight percentage: C:0.05 ~ 0.07%, Si:0.25 ~ 0.35%, Mn:1.40 ~ 1.80%, P≤0.01%, S≤0.003%, Nb:0.01 ~ 0.04%, Ti:0.01 ~ 0.02%, Mo≤0.35%, Cu≤030%:Cr≤0.35%, Ni≤0.030%, rest part is Fe and inevitable impurity.
2. the large strain X80 dual phase sheet steel that the large soft reduction process of a kind of low temperature according to claim 1 is produced, is characterized in that: the chemical composition of described steel plate meets: Pcm=C+Si/30+Ni/60+ (Mn+Cr+Cu)/20+Mo/15+V/10+5B≤0.20%.
3. the manufacture method of the large strain X80 dual phase sheet steel that the large soft reduction process of a kind of low temperature according to claim 1 is produced, its processing step comprises: the moulding → finish rolling → pre-straightening → ACC pattern laminar flow of reheat → laterally broadening of get the raw materials ready → molten iron KR desulfurization processing → converter smelting → CAS Argon → LF+RH duplex practice refining → sheet billet continuous casting → strand → is longitudinally cooling → aligning → stacking slow cooling → UT (Ultrasonic Testing) operation.
4. the manufacture method of the large strain X80 dual phase sheet steel that the large soft reduction process of a kind of low temperature according to claim 3 is produced, its concrete steps are:
(1) after raw material molten iron KR pre-treatment, through converter smelting, send into the refining of LF refining furnace after ladle argon-blown again, then in VD stove, carry out vacuum-treat, protect vacuum time 20 minutes, processing finishes rear feeding calcium iron wire 2m/t, soft blow argon 10 minutes after line feeding;
(2) upper continuous caster cast after VD stove vacuum breaker, stacking slow cooling 48 hours after strand rolls off the production line;
(3) strand is through process furnace soaking, strand time inside furnace 4-5 hour, and tapping temperature is 1110-1130 ℃, after coming out of the stove, carries out dephosphorize by high pressure water, removes oxidized iron sheets on surface of casting blank, after dephosphorization, casting blank surface temperature is controlled at 1040 ℃ ~ 1050 ℃;
(4) horizontal-vertical rolling mode is selected in strand rolling, first the continuously cast bloom after dephosphorization is carried out to horizontal broadening and longitudinally moulding, laterally broadening rolling 4 passages, every time draft >=12%, accumulative total draft >=40%, longitudinally formation rolling 1 passage, percentage pass reduction >=16%, longitudinally formation rolling temperature is controlled at 950 ℃～1050 ℃, obtains intermediate blank;
(5) after longitudinally formation rolling finishes, utilize roughing mill high pressure water to carry out continuous de-scaling 3 passages that cool to intermediate blank, before each de-scaling is cooling, guarantee that intermediate blank temperature returns red, after cooling, strand temperature is controlled at 880 ℃～900 ℃, air cooling treats that temperature is to 820 ℃ of finish rolling, finish rolling adopts one-pass roller, rolling 14 passages, last 1 road is the empty passage of crossing, rolling mill speed is set to 1.0m/s, roller table speed 0.5 m/s after machine, finish rolling accumulative total percentage pass reduction >=75%, finishing temperature is controlled at 730 ℃～750 ℃;
(6) ACC pattern laminar flow cooling in, 21 ℃/S of the cooling target cooling rate of laminar flow, target final cooling temperature is below 200 ℃, water convexity bias :+15%; Edge part shading OS:40; DS:-40.
5. the manufacture method of the large strain X80 dual phase sheet steel that the large soft reduction process of a kind of low temperature according to claim 4 is produced, is characterized in that: in described step 2, continuous caster casting process adopts Segment Electromagnetic Stirring and the light soft reduction process of strand.
6. the manufacture method of the large strain X80 dual phase sheet steel that the large soft reduction process of a kind of low temperature according to claim 4 is produced, is characterized in that: in step 2, gained slab thickness is 250mm.
7. the manufacture method of the large strain X80 dual phase sheet steel that the large soft reduction process of a kind of low temperature according to claim 4 is produced, is characterized in that: workpiece thickness described in step 4 is 120mm.
8. a kind of low temperature according to claim 4 is suppressed the manufacture method of the two-way steel plate of large strain X80 of lower explained hereafter, it is characterized in that: the pressure of described step 3 and step 5 mesohigh water is 20MP.
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| WO2021017521A1 (en) * | 2019-08-01 | 2021-02-04 | 江阴兴澄特种钢铁有限公司 | Low yield-to-tensile ratio thin specification pipeline steel manufacturing method |
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| CN104694844A (en) * | 2015-03-27 | 2015-06-10 | 山东钢铁股份有限公司 | Production method of X65M pipeline steel |
| CN106319387A (en) * | 2015-06-16 | 2017-01-11 | 鞍钢股份有限公司 | X80 large deformation resistant pipeline steel and manufacturing method thereof |
| CN105088096A (en) * | 2015-08-31 | 2015-11-25 | 山东钢铁股份有限公司 | X80 pipeline steel with high stress ratio and high arrest toughness and preparation method and application of X80 pipeline steel |
| CN105088096B (en) * | 2015-08-31 | 2017-04-19 | 山东钢铁股份有限公司 | X80 pipeline steel with high stress ratio and high arrest toughness and preparation method and application of X80 pipeline steel |
| CN105886924A (en) * | 2016-04-28 | 2016-08-24 | 山东钢铁股份有限公司 | Low-alloy steel high in strength and toughness performance and preparing method of low-alloy steel |
| CN106040749A (en) * | 2016-06-21 | 2016-10-26 | 首钢京唐钢铁联合有限责任公司 | Rough rolling rhythm control method |
| CN106040749B (en) * | 2016-06-21 | 2018-06-22 | 首钢京唐钢铁联合有限责任公司 | Rough rolling rhythm control method |
| CN106191657A (en) * | 2016-08-18 | 2016-12-07 | 山东钢铁股份有限公司 | Carbon low cost L245 L320 level pipeline pipeline steel and manufacture method thereof in one |
| CN108103407A (en) * | 2018-01-31 | 2018-06-01 | 舞阳钢铁有限责任公司 | Surrender 450MPa grades of sour environment military service Pipeline Steel Plates and its production method |
| CN110369519A (en) * | 2019-07-23 | 2019-10-25 | 唐山中厚板材有限公司 | The operation of rolling method for controlling shape of 500MPa level low alloy high strength steel plate |
| WO2021017521A1 (en) * | 2019-08-01 | 2021-02-04 | 江阴兴澄特种钢铁有限公司 | Low yield-to-tensile ratio thin specification pipeline steel manufacturing method |
| CN110964971A (en) * | 2019-12-25 | 2020-04-07 | 山东钢铁集团日照有限公司 | Production method of X65M-grade pipeline steel plate with thin specification and high crack resistance |
| CN114737133A (en) * | 2022-03-23 | 2022-07-12 | 江阴兴澄特种钢铁有限公司 | Low-yield-ratio high-toughness structural steel plate and manufacturing method thereof |
| CN114737133B (en) * | 2022-03-23 | 2023-10-20 | 江阴兴澄特种钢铁有限公司 | Low-yield-ratio high-toughness structural steel plate and manufacturing method thereof |
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