CN104561486A - Thick-gauge hot continuous rolling steel belt with excellent ultralow temperature CTOD (Crack Tip Opening Displacement) performance and production method of thick-gauge hot continuous rolling steel belt - Google Patents
Thick-gauge hot continuous rolling steel belt with excellent ultralow temperature CTOD (Crack Tip Opening Displacement) performance and production method of thick-gauge hot continuous rolling steel belt Download PDFInfo
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Abstract
The invention relates to the technical field of hot continuous rolling steel belts for use in submarine oil/gas transmission pipelines and provides a thick-gauge hot continuous rolling steel belt with excellent ultralow temperature CTOD (Crack Tip Opening Displacement) performance and a production method of the thick-gauge hot continuous rolling steel belt. According to the thick-gauge hot continuous rolling steel belt and the production method, the technical problem of high technical difficulty in the production of the thick-gauge hot continuous rolling steel belt with the excellent ultralow temperature CTOD performance in the prior art is solved. The production method comprises the following steps: (1) continuously casting a plate blank into a casting blank with the thickness of 230mm-240mm by virtue of 'complete pretreatment' smelting and LF refining; (2) carrying out offline detection on the casting blank; (3) putting the casting blank in a heating furnace, and heating, wherein the heating temperature is 1190-1230 DEG C, and the temperature equalizing time is more than or equal to 30 minutes; (4) carrying out a rough rolling process; (5) carrying out a precision rolling process, wherein the thickness of the rolled steel belt is 16mm-20.2mm; (6) carrying out a laminar flow cooling process; and (7) reeling at the temperature of 480-560 DEG C. The production method can be used for producing the thick-gauge hot continuous rolling steel belt with the excellent ultralow temperature CTOD at relatively low difficulties.
Description
Technical field
The present invention relates to the technical field of submarine oil-transportation/gas pipeline hot continuous rolling steel band, particularly relate to a kind of production method with the think gauge hot continuous rolling steel band of excellent very low temperature CTOD performance.
Background technology
Over nearly 10 years, China increases more than 50% of oil production rate newly from ocean, and offshore and gas development is in major fields, and the demand of Submarine pipeline steel is also increasing.Because environment for use is harsh, Submarine pipeline steel is stricter than the requirement of general buried gas transmission line steel, except general execution DNV (DET NORSKEVERITAS: Veritas) standard, design Fang Junhui proposes harsher requirement and ensures security.As, Submarine pipeline steel requires higher weldability, require comparatively low-carbon-equivalent, X65 levels necessitate carbon equivalent ce≤0.39, user may require CE≤0.38, and the general X65 pipe line steel carbon equivalent upper limit is 0.43, actual product often requires≤low-temperature impact toughness of-30 DEG C, ≤-15 DEG C of drop weight tearing performances, require higher indulging simultaneously, lateral performance, low temperature CTOD (Crack Tip Opening Displacement: crack tip opening displacement) performance is the important evaluation index of Submarine pipeline steel, particularly think gauge product, for evaluating crackle crack arrest ability, this is directly connected to safety in utilization and the service life of subsea pipeline, generally, ERW welds subsea pipeline CTOD and requires it is 0 DEG C of value >=0.20mm, according to different environment for use, user requires-15 DEG C of value >=0.30mm sometimes.The Submarine pipeline steel with good low temperature performance will improve work reliability and the active time of subsea pipeline greatly.
In general, deep-sea pipeline steel wall thickness requires comparatively large, main employing plate of moderate thickness steel plate; And hot continuous rolling roll bending by high frequency resistance welding welding (ERW) or crosscut become steel plate after union-melt weld be connected into pipe, for the environments such as subsea that the degree of depth is relatively shallow, vertical, flat and bend pipe in the pipeline of shallow sea all can adopt hot-rolled coil tubulation, and hot-rolled coil has that production efficiency is high, control accuracy high.Although be all Submarine pipeline steel, hot continuous rolling (strip product) is produced has very big-difference with the physical metallurgy process of plate of moderate thickness Plate Production.Limit by continous hot rolling facility, the compression ratio of hot continuous rolling steel band is limited, treat that warm space is little, hot continuous rolling strip product thickness is larger, Rolling Production and to batch difficulty larger, ensure that the difficulty of every very low temperature performance is also larger, and the requirement of low cost, low-carbon-equivalent, will further improve the production technology difficulty requiring low-temperature performance steel band undoubtedly.Therefore, need to carry out alloy system, smelting and rolling technology design targetedly.
At present, the patent report for the subsea pipeline hot-rolled coil with superior low temperature CTOD performance is less.
The patent of publication number CN 101701315 A provides " manufacture method of submerged pipeline steel pipe ", its feature is to adopt C:0.04-0.08%, Si≤0.25%, Mn≤1.65%, Nb+V+Ti≤0.15%, the hot-rolled coil raw material of Ceq≤0.41 carries out ERW weldprocedure tubulation, and its patent only pays close attention to tube-making process, do not relate to hot continuous rolling steel band production technique, low temperature CTOD performance and low-temperature impact toughness, have larger difference with in this patent.The patent of publication number CN 101082108 A provides " a kind of steel plate for subsea pipeline and rolling scheme thereof ", describe a kind of production decision of subsea pipeline hot-rolled coil, its composition is C:0.030 ~ 0.075%, Si:0.10 ~ 0.30%, Mn:1.40 ~ 1.60%, Cu :≤0.20%, Ni:0.10 ~ 0.25%, Mo:0.07 ~ 0.20%, Nb:0.03 ~ 0.05%, V :≤0.060%, Ti:0.001 ~ 0.02%, Al:0.01 ~ 0.06%, Cr :≤0.20%, but the thickness that this patent relates to hot-rolled sheet coil is only 6-14mm, impact average temperature only at-15 DEG C, value is at 168 ~ 336J, low temperature CTOD only relates to-5 DEG C, value only shows to be greater than 0.25mm, the thickness range of the patented product and low-temperature impact toughness, CTOD value level is relatively low, and the Ni added in its product costly, Cu alloying element, cost is higher, harsher environment is still needed to enhance product performance, larger difference is had with in this patent.Publication number CN 103451536 A patent describes " a kind of low cost think gauge subsea pipeline steel plate and manufacture method thereof ", the chemical composition that steel plate comprises is: C:0.04 ~ 0.06%, Si:0.15 ~ 0.20%, Mn:1.43 ~ 1.47%, P :≤0.008%, S :≤0.003%, Ni:0.10 ~ 0.15%, Nb:0.030 ~ 0.040%, Ti:0.012 ~ 0.023%, Al:0.015 ~ 0.025%, N :≤0.006%, Nb+V+Ti≤0.15%.It is plate of moderate thickness product that this patent relates to product, and its intensity is at below 470MPa, and-30 ° are impacted average at about 300J, do not describe the low temperature CTOD value of steel sheet product, have larger difference with in this patent.The patent " a kind of production decision improving subsea pipeline steel low temperature arrest toughness " of publication number CN 103846277 A is applicable to the production of subsea pipeline steel Wide and Thick Slab product, describe and a kind ofly improve subsea pipeline steel thickness direction heart portion Charpy impact toughness, method that low temperature drops hammer toughness DWTT and crack tip opening displacement CTOD, this patent does not relate to Composition Design, CTOD value probe temperature is-15 DEG C, has larger difference with in this patent.
From analyzing above, in prior art, there is the technical problem that technical difficulty is higher, production cost is higher of the think gauge hot continuous rolling steel band producing very low temperature CTOD performance.
Summary of the invention
The invention provides a kind of think gauge hot continuous rolling steel band and the production method with excellent very low temperature CTOD performance, to solve in prior art to produce, there is the higher technical problem of the technical difficulty of the think gauge hot continuous rolling steel band of excellent very low temperature CTOD performance.
First aspect, the embodiment of the present invention provides a kind of production method with the think gauge hot continuous rolling steel band of excellent very low temperature CTOD performance, comprises the following steps:
(1) " complete three take off " smelting, LF refining, slab continuous casting become thickness to be the strand of 230-240mm;
(2) lower ray examination is carried out to described strand, if inspection of rolling off the production line described in passing through shows that described strand does not satisfy condition, flame cleaning is carried out to described continuously cast bloom;
(3) described strand is loaded process furnace to heat, wherein, Heating temperature is 1190 ~ 1230 DEG C, equal temperature time >=30min;
(4) roughing technique, it is 1020 ~ 980 DEG C that last passes of described roughing technique starts temperature, last reduction in pass 19 ~ 22% described, and workpiece thickness is 50 ~ 58mm;
(5) finish-rolling process, the temperature in of described finish-rolling process is 900 ~ 960 DEG C, and finish rolling end reduction in pass controls 9 ~ 12%, and finishing temperature is 800 ~ 860 DEG C, and after rolling, the thickness of steel band is 16 ~ 20.2mm;
(6) laminar flow cooling technology;
(7) when coiling temperature is 480 ~ 560 DEG C, batch, and then obtain described hot continuous rolling steel band.
Optionally, described " complete three take off " smelting, LF refining, slab continuous casting become thickness to be the strand of 230-240mm, specifically comprise the following steps:
Molten iron is carried out to the pre-treatment of de-S and de-P, make S content≤0.0050% in described molten iron, P content≤0.015%;
Add steel scrap and Mo-Fe alloy at described molten iron, described Mo-Fe alloy is for adjusting the content of Mo in described molten iron, and adding amount of scrap steel accounts for the 8-10% of total molten steel amount; Described molten iron is blended into de-C converter and carries out converter smelting;
Carry out converter tapping, add with the steel stream of described molten steel the deoxidation operation that Al-Fe alloy carries out described molten steel at tapping process; Add Si-Fe alloy, low-carbon Mn-Fe alloy, low-carbon (LC) Cr-Fe alloy subsequently, to carry out the preliminary adjustment of Si, Mn, Cr element;
Carry out the refining of LF stove;
Be cast into by continuous casting process the described continuously cast bloom that thickness is 230 ~ 240mm, in described casting treating processes, carry out dynamic soft-reduction at the solidification end of described molten steel.
Optionally, described in carry out the refining of LF stove, specifically comprise:
Heating makes molten steel to being applicable to teeming temperature, ensures molten steel overheat 15-30 DEG C described in casting process;
Carry out de-S operation, make S content≤0.0030% in described molten steel;
In described molten steel, add Al-Fe, Si-Fe alloy, middle carbon Mn-Fe alloy, low-carbon (LC) Cr-Fe, Ti-Fe alloy and C powder, thus carry out the adjustment of Al, Si, Mn, Cr, Ti, C element;
By feeding Ca-Fe line in described molten steel, denaturing treatment is carried out to inclusion;
Be blown into by the bottom blowing hole of ladle bottom the argon gas that single channel flow is 50 ~ 150L/min, make described inclusion floating.
Optionally, the mass percent of the chemical composition of described hot continuous rolling steel band is: C:0.040-0.080wt%, Si:0.05-0.20wt%, Mn:1.20-1.60wt%, P :≤0.015wt%; S :≤0.0030wt%, Nb :≤0.060wt%, Cr :≤0.20wt%, Ti:0.010-0.025wt%, V :≤0.040wt%, Mo :≤0.15wt%, all the other are Fe and inevitable impurity.
Optionally, carbon equivalent ce≤0.38 of described hot continuous rolling steel band, welding cold cracking Sensitivity rate Pcm≤0.17.
Optionally, the transverse yield strength R of described hot continuous rolling steel band
t0.5>=510MPa, tensile strength R
m>=610MPa, elongation A
50.8mm>=35% ,-35 DEG C of low-temperature impacts absorb merit average>=390J, and-15 DEG C of Drop-Weight Tear Test (DWTT) DWTT averages are 100% ,-15 DEG C of crack tip opening displacement CTOD average>=1.2mm ,-40 DEG C of CTOD average>=0.9mm.
Second aspect, the embodiment of the present invention provides a kind of think gauge hot continuous rolling steel band with excellent very low temperature CTOD performance, its feature functionality is, the production method manufacture with the think gauge hot continuous rolling steel band of excellent very low temperature CTOD performance that described hot continuous rolling steel band is introduced by any embodiment of the present invention forms.
Optionally, the mass percent of the chemical composition of described hot continuous rolling steel band is: C:0.040-0.080wt%, Si:0.05-0.20wt%, Mn:1.20-1.60wt%, P :≤0.015wt%; S :≤0.0030wt%, Nb :≤0.060wt%, Cr :≤0.20wt%, Ti:0.010-0.025wt%, V :≤0.040wt%, Mo :≤0.15wt%, all the other are Fe and inevitable impurity.
Optionally, carbon equivalent ce≤0.38 of described hot continuous rolling steel band, welding cold cracking Sensitivity rate Pcm≤0.17.
Optionally, the transverse yield strength R of described hot continuous rolling steel band
t0.5>=510MPa, tensile strength R
m>=610MPa, elongation A
50.8mm>=35% ,-35 DEG C of low-temperature impacts absorb merit average>=390J, and-15 DEG C of Drop-Weight Tear Test (DWTT) DWTT averages are 100% ,-15 DEG C of crack tip opening displacement CTOD average>=1.2mm ,-40 DEG C of CTOD average>=0.9mm.
Beneficial effect of the present invention is as follows:
Due in embodiments of the present invention, a kind of production method with the think gauge hot continuous rolling steel band of excellent very low temperature CTOD performance is provided, comprise the following steps: (1) " complete three take off " is smelted, LF refining, slab continuous casting becomes thickness to be the strand of 230-240mm, wherein smelted by " complete three take off ", LF refining can obtain comparatively high cleanliness to make molten steel, reduce S, the impurity contents such as P, and then make S content≤0.0030% in continuously cast bloom, P content≤0.015%, (2) lower ray examination is carried out to strand, if inspection shows that strand does not satisfy condition through rolling off the production line, flame cleaning is carried out to continuously cast bloom, thus ensure that strand is loaded process furnace and heats by steel strip surface quality (3), wherein, Heating temperature is 1190 ~ 1230 DEG C, equal temperature time >=30min, to make each regional temperature of strand even, ensure the abundant solid solution of alloying element, prevent again undue and uneven the growing up of austenite, (4) roughing technique, it is 1020 ~ 980 DEG C that last passes of roughing technique starts temperature, last reduction in pass 19 ~ 22%, 3rd workpiece thickness is 50 ~ 58mm, thus ensure that austenite crystal is by the repeatedly full and uniform refinement of Static Recrystallization behavior, ensure the complete Static Recrystallization behavior under lesser temps simultaneously, suppress growing up of recrystal grain with this, obtain tiny austenite crystal, (5) finish-rolling process, the temperature in of finish-rolling process is 900 ~ 960 DEG C, finish rolling end reduction in pass controls 9 ~ 12%, finishing temperature is 800 ~ 860 DEG C, after rolling, the thickness of steel band is 16 ~ 20.2mm, the abundant flattening of austenite crystal is ensured with this, obtain higher strain accumulation by finish rolling simultaneously, ensure the abundant refinement of phase-change organization, reduce effective particle size, ensure the abundant flattening of austenite crystal with this, obtain higher strain accumulation by finish rolling simultaneously, ensure the abundant refinement of phase-change organization, reduce effective particle size, (6) laminar flow cooling technology, (7) carrying out the taking-up activities that coiling temperature is 480 ~ 560 DEG C, is the microstructure of target to obtain with acicular ferrite, thus the think gauge subsea pipeline hot continuous rolling steel band of obtained more than 16mm.So provide a kind of production method with the think gauge hot continuous rolling steel band of excellent very low temperature CTOD performance, the method production difficulty is lower, and then can reduce production cost.
Accompanying drawing explanation
Fig. 1 is the schema of the production method of the think gauge hot continuous rolling steel band in the embodiment of the present invention with excellent very low temperature CTOD performance;
Fig. 2 is that the embodiment of the present invention to have in the production method of the think gauge hot continuous rolling steel band of excellent very low temperature CTOD performance " complete three take off " smelting, LF refining, slab continuous casting become thickness to be the schema of the strand of 230-240mm;
Fig. 3 is the schema carrying out the refining of LF stove in the embodiment of the present invention.
Embodiment
The invention provides a kind of think gauge hot continuous rolling steel band and the production method with excellent very low temperature CTOD performance, to solve in prior art to produce, there is the higher technical problem of the technical difficulty of the think gauge hot continuous rolling steel band of excellent very low temperature CTOD performance.
Technical scheme in the embodiment of the present application is solve above-mentioned technical problem, and general thought is as follows:
A kind of production method with the think gauge hot continuous rolling steel band of excellent very low temperature CTOD performance is provided, comprise the following steps: (1) " complete three take off " is smelted, LF refining, slab continuous casting becomes thickness to be the strand of 230-240mm, wherein smelted by " complete three take off ", LF refining can obtain comparatively high cleanliness to make molten steel, reduce S, the impurity contents such as P, and then make S content≤0.0030% in continuously cast bloom, P content≤0.015%, (2) lower ray examination is carried out to strand, if inspection shows that strand does not satisfy condition through rolling off the production line, flame cleaning is carried out to continuously cast bloom, thus ensure that strand is loaded process furnace and heats by steel strip surface quality (3), wherein, Heating temperature is 1190 ~ 1230 DEG C, equal temperature time >=30min, to make each regional temperature of strand even, ensure the abundant solid solution of alloying element, prevent again undue and uneven the growing up of austenite, (4) roughing technique, it is 1020 ~ 980 DEG C that last passes of roughing technique starts temperature, last reduction in pass 19 ~ 22%, 3rd workpiece thickness is 50 ~ 58mm, thus ensure that austenite crystal is by the repeatedly full and uniform refinement of Static Recrystallization behavior, ensure the complete Static Recrystallization behavior under lesser temps simultaneously, suppress growing up of recrystal grain with this, obtain tiny austenite crystal, (5) finish-rolling process, the temperature in of finish-rolling process is 900 ~ 960 DEG C, finish rolling end reduction in pass controls 9 ~ 12%, finishing temperature is 800 ~ 860 DEG C, after rolling, the thickness of steel band is 16 ~ 20.2mm, the abundant flattening of austenite crystal is ensured with this, obtain higher strain accumulation by finish rolling simultaneously, ensure the abundant refinement of phase-change organization, reduce effective particle size, ensure the abundant flattening of austenite crystal with this, obtain higher strain accumulation by finish rolling simultaneously, ensure the abundant refinement of phase-change organization, reduce effective particle size, (6) laminar flow cooling technology, (7) carrying out the taking-up activities that coiling temperature is 480 ~ 560 DEG C, is the microstructure of target to obtain with acicular ferrite, thus the think gauge subsea pipeline hot continuous rolling steel band of obtained more than 16mm.To provide a kind of production method with the think gauge hot continuous rolling steel band of excellent very low temperature CTOD performance, the method production difficulty is lower, and then can reduce production cost.
In order to better understand technique scheme, below by accompanying drawing and specific embodiment, technical solution of the present invention is described in detail, the specific features being to be understood that in the embodiment of the present invention and embodiment is the detailed description to technical solution of the present invention, instead of the restriction to technical solution of the present invention, when not conflicting, the technical characteristic in the embodiment of the present invention and embodiment can combine mutually.
First aspect, the embodiment of the present invention provides a kind of production method with the think gauge hot continuous rolling steel band of excellent very low temperature CTOD performance, please refer to Fig. 1, comprises the following steps:
Step S101: " complete three take off " smelting, LF (Ladle Furnace: ladle refining furnace) refining, slab continuous casting become thickness to be the strand of 230-240mm;
In above-mentioned steps, first carry out complete three and take off " smelt, then carry out LF refining, finally slab continuous casting become thickness to be the strand of 230-240mm.
Step S102: carry out lower ray examination to strand, if show that strand does not satisfy condition through inspection of rolling off the production line, carries out flame cleaning to continuously cast bloom;
Wherein, lower ray examination mainly checks surface quality and the quality of edges of strand, if there is problem, flame cleaning and chamfered need be carried out, thus these ensure surface quality (as without sticking up skin, bubble) and the quality of edges (without edge cracks, fine rule) of the hot-rolled sheet coil of final rolling, because all can affect surface quality and the welding of later stage tubulation steel pipe.
Wherein, flame cleaning utilizes the gas cutting of thermal-flame and molten removing to act on steel billet surface defect burn off.It is the important procedure ensureing billet quality.
Steel band quality can be ensured by above-mentioned steps.
Step S103: strand is loaded process furnace and heats, wherein, Heating temperature is 1190 ~ 1230 DEG C, equal temperature time >=30min, wherein be in cold conditions at strand to be loaded process furnace to heat, after cold conditions refers to that strand cools down completely, then send into process furnace.
By the control of above-mentioned heating parameters, each regional temperature of strand can be made even, ensure the abundant solid solution of alloying element, prevent again undue and uneven the growing up of austenite.
Step S104: roughing technique, it is 1020 ~ 980 DEG C that last passes of roughing technique starts temperature, and last reduction in pass 19 ~ 22%, workpiece thickness is 50 ~ 58mm.
By the control of above-mentioned roughing parameter, can ensure that austenite crystal passes through the repeatedly full and uniform refinement of Static Recrystallization behavior, ensure the complete Static Recrystallization behavior under lesser temps simultaneously, suppress growing up of recrystal grain with this, obtain tiny austenite crystal.
Step S105: finish-rolling process, the temperature in of finish-rolling process is 900 ~ 960 DEG C, and finish rolling end reduction in pass controls 9 ~ 12%, and finishing temperature is 800 ~ 860 DEG C, and after rolling, the thickness of steel band is 16 ~ 20.2mm;
By the control of above-mentioned finish rolling parameter, the abundant flattening of austenite crystal can be ensured, obtain higher strain accumulation by finish rolling simultaneously, ensure the abundant refinement of phase-change organization, reduce effective particle size, ensure the abundant flattening of austenite crystal with this, obtain higher strain accumulation by finish rolling simultaneously, ensure the abundant refinement of phase-change organization, reduce effective particle size.
In specific implementation process, if the steel band that thickness specification is 16 ~ 18mm will be obtained, then finish rolling 7 passage; If obtain the steel band that thickness specification is more than 18mm, then finish rolling 6 passage.
Step S106: laminar flow cooling technology;
Step S107: when coiling temperature is 480 ~ 560 DEG C, batch, and then obtain hot continuous rolling steel band.
Under normal circumstances, can obtain by such scheme the think gauge subsea pipeline hot continuous rolling steel band that thickness specification is more than 16mm.
As further preferred embodiment, in step S101, " complete three take off " smelting, LF refining, slab continuous casting become thickness to be the strand of 230-240mm, please refer to Fig. 2, specifically comprise the following steps:
Step S201: pre-treatment molten iron being carried out to de-S and de-P, makes S content≤0.0050% in molten iron, P content≤0.015%;
Wherein, S can be taken off by the de-S device of KR (Kanbara reactor), make molten steel S content≤0.0050%; Utilize independent converter of laying to take off P and de-Si, make molten steel P content≤0.015%;
Step S202: add steel scrap and Mo-Fe alloy at molten iron, Mo-Fe alloy is for adjusting the content of Mo in molten iron, and adding amount of scrap steel accounts for the 8-10% of total molten steel amount; Molten iron is blended into de-C converter and carries out converter smelting;
Step S203: carry out converter tapping, adds with the steel stream of molten steel the deoxidation operation that Al-Fe alloy carries out molten steel at tapping process; Add Si-Fe alloy, low-carbon Mn-Fe alloy, low-carbon (LC) Cr-Fe alloy subsequently, to carry out the preliminary adjustment of Si, Mn, Cr element;
Step S204: carry out the refining of LF stove;
Step S205: be cast into the continuously cast bloom that thickness is 230 ~ 240mm by continuous casting process, in casting treating processes, carries out dynamic soft-reduction at the solidification end of molten steel.
In specific implementation process, solidification end just refers to molten steel by liquid state to solid state crystallization process of setting, the position before solidifying,
As further preferred embodiment, carry out the refining of LF stove in step S205, please refer to Fig. 3, specifically comprise:
Step S301: heating makes molten steel to being applicable to teeming temperature, ensures casting process molten steel overheat 15-30 DEG C;
Step S302: carry out de-S operation, make S content≤0.0030% in molten steel;
Wherein, mainly de-S operation is carried out by adding the material such as synthetic slag, fluorite.
Step S303: add Al-Fe, Si-Fe alloy, middle carbon Mn-Fe alloy, low-carbon (LC) Cr-Fe, Ti-Fe alloy and C powder in molten steel, thus carry out the adjustment of Al, Si, Mn, Cr, Ti, C element;
Step S304: by feeding Ca-Fe line in molten steel, denaturing treatment is carried out to inclusion;
Step S305: the argon gas (single channel flow 50 ~ 150L/min) being blown into little tolerance by the bottom blowing hole of ladle bottom, makes inclusion floating.
In such scheme, the Composition Design of employing low cost, low-carbon-equivalent produces a kind of think gauge hot continuous rolling steel band with excellent very low temperature CTOD performance, the production method of invention is: " complete three take off " smelting, LF refining, slab continuous casting become thickness to be the strand of 230-240mm, to make molten steel obtain comparatively high cleanliness, reduce the impurity contents such as S, P.Under strand, ray examination, cleaning ensure steel strip surface quality.The temperature that reheats of rolling is 1190 ~ 1230 DEG C, equal temperature time >=30min, to make each regional temperature of strand even, ensures the abundant solid solution of alloying element, prevents again undue and uneven the growing up of austenite; In hot continuous rolling, roughing divides 8 passes, control last passes of roughing and start temperature, 1020 ~ 980 DEG C, last reduction in pass 19 ~ 22%, ensure that austenite crystal is by the repeatedly full and uniform refinement of Static Recrystallization behavior, ensure the complete Static Recrystallization behavior under lesser temps simultaneously, suppress growing up of recrystal grain with this, obtain tiny austenite crystal.Workpiece thickness controls at 50 ~ 58mm, entry temperature at finishing is 900 ~ 960 DEG C, 16 ~ 18mm thickness specification, finish rolling 7 passage, more than 18mm specification, finish rolling 6 passage, finish rolling end reduction in pass controls 9 ~ 12%, and finishing temperature is 800 ~ 860 DEG C, the abundant flattening of austenite crystal is ensured with this, obtain higher strain accumulation by finish rolling simultaneously, ensure the abundant refinement of phase-change organization, reduce effective particle size.Steel band after rolling, adopt laminar flow to cool fast, coiling temperature is 480 ~ 560 DEG C, and obtaining with acicular ferrite is the microstructure of target, thus the think gauge hot continuous rolling steel band with excellent very low temperature CTOD performance of obtained more than 16mm.
As further preferred embodiment, the mass percent of the chemical composition of hot continuous rolling steel band is: C:0.040-0.080wt%, Si:0.05-0.20wt%, Mn:1.20-1.60wt%, P :≤0.015wt%; S :≤0.0030wt%, Nb :≤0.060wt%, Cr :≤0.20wt%, Ti:0.010-0.025wt%, V :≤0.040wt%, Mo :≤0.15wt%, all the other are Fe and inevitable impurity.
In subsea pipeline hot continuous rolling steel band provided by the invention, each alloy element action is as follows:
C: strengthening element most economical, the most basic in steel, but the increase of C content will reduce the toughness of steel and can weld, and for ensureing lower carbon equivalent level, improves low-temperature impact toughness and low temperature CTOD performance simultaneously.Patent C addition of the present invention is 0.04-0.08wt%.
Si: the intensity improving steel with solution strengthening form, but more Si content is unfavorable for that the low-carbon-equivalent of steel controls and welding property, and too high Si may cause more serious scale on surface simultaneously.This patent Si addition is 0.05-0.25wt%.
Mn: solution strengthening element, can effective proof strength, but Mn is too high will significantly improve carbon equivalent, produce simultaneously serious in the middle of segregation, affect the low-temperature performance of product.Patent Mn addition of the present invention is 1.20-1.60wt%.
P, S are detrimental impurity element, will increase material fragility, and comparatively obvious on low-temperature flexibility impact, therefore, its content is more low better, and this patent takes off smelting, LF refinery practice by complete three, and P :≤0.015wt%; S :≤0.0030wt%.
Nb: thin brilliant successful, can significantly improve obdurability, adds the grain growth that a certain amount of Nb microalloy can suppress welded heat affecting zone.Patent Nb addition of the present invention is Nb:0.020-0.060wt%.
Ti: microalloy element, it is mainly solid N that trace adds, and tiny precipitation simultaneously plays in the heat stage and suppresses austenite to be grown up, and is conducive to the raising of low-temperature flexibility.Patent Ti addition of the present invention is 0.010 ~ 0.020wt%.
Mo, Cr: there is stronger solid solution strengthening effect, effectively can improve hardening capacity, strength-enhancing effect is obvious, Mo can suppress ferrite transformation, reduce starting temperature of transformation, especially under hot continuous rolling condition, under the condition that strain is accumulative higher, Mo effectively can suppress the generation of high-temperature phase-change tissue, makes up hot continuous rolling cooling power not enough.But too high Mo, Cr will improve carbon equivalent greatly, do not reach the requirement being less than 0.38, also there is disadvantageous effect to ERW welding in too high Cr in addition, and the price of Mo own is higher, will improve material cost.Patent Cr of the present invention :≤0.25wt%, Mo :≤0.15wt%.
V: microalloy element, about having solid solution and precipitation strength, the precipitation particularly in ferrite, can effective proof strength level, this patent V≤0.050wt%.
As further preferred embodiment, carbon equivalent ce≤0.38 of hot continuous rolling steel band, welding cold cracking Sensitivity rate Pcm≤0.17.
As further preferred embodiment, the transverse yield strength R of hot continuous rolling steel band
t0.5>=510MPa, tensile strength R
m>=610MPa, elongation A
50.8mm>=35% ,-35 DEG C of low-temperature impacts absorb merit average>=390J, and-15 DEG C of Drop-Weight Tear Test (DWTT) DWTT averages are 100% ,-15 DEG C of crack tip opening displacement CTOD average>=1.2mm ,-40 DEG C of CTOD average>=0.9mm.
The production method of the subsea pipeline hot rolled strip that the embodiment of the present invention is introduced will be introduced below with four specific exampless (example 1 to example 4).
The thickness specification of the subsea pipeline hot continuous rolling steel band of example 1,2,3,4 is respectively 16.2mm, 17.3mm, 18mm, 20.2mm;
The chemical composition of the subsea pipeline hot continuous rolling steel band of the example of the present invention 1,2,3,4 produced is as shown in table 1.
As shown in table 1, be the chemical composition (wt%) of hot continuous rolling steel band example 1,2,3,4 of the present invention.
Table 1
| C | Si | Mn | P | S | Alt | Nb | V | |
| Example 1 | 0.07 | 0.11 | 1.50 | 0.010 | 0.0017 | 0.04 | 0.047 | 0.03 |
| Example 2 | 0.06 | 0.10 | 1.40 | 0.010 | 0.0013 | 0.04 | 0.045 | 0.03 |
| Example 3 | 0.065 | 0.11 | 1.45 | 0.010 | 0.0020 | 0.04 | 0.047 | 0.03 |
| Example 4 | 0.06 | 0.10 | 1.44 | 0.007 | 0.0011 | 0.04 | 0.050 | 0.04 |
| Cr | Ti | Mo | N | B | Ceq | Pcm | ||
| Example 1 | 0.14 | 0.017 | 0.08 | 0.0034 | 0.0002 | 0.36 | 0.16 | |
| Example 2 | 0.15 | 0.017 | 0.08 | 0.0035 | 0.0002 | 0.35 | 0.15 |
| Example 3 | 0.16 | 0.020 | 0.08 | 0.0044 | 0.0003 | 0.36 | 0.16 | |
| Example 4 | 0.10 | 0.015 | 0.10 | 0.0036 | 0.0002 | 0.35 | 0.15 |
As shown in table 2 to table 5, it is every test result of the subsea pipeline hot continuous rolling steel band of example 1,2,3,4.
The tensile property of the subsea pipeline hot continuous rolling steel band of table 2 example 1,2,3,4.
Table 2
Table 3 represents low-temperature impact toughness and the low temperature DWTT performance of the subsea pipeline hot continuous rolling steel band of example 1,2,3,4.
Table 3
Table 4 is the serial low-temperature impact toughness of the subsea pipeline hot continuous rolling steel band of example 4 and serial low temperature DWTT performance.
Table 4
Table 5 is the series of CT OD performance of the subsea pipeline hot continuous rolling steel band of example 4.
Table 5
The subsea pipeline hot continuous rolling steel strip substrate tissue generated, based on acicular ferrite, contains a small amount of Ma-Ao constituent element tissue simultaneously.EBSD (Electron Back-Scattered Diffraction) analyzes and shows, CTOD crack propagation region, grain orientation differs greatly, and big angle grain boundary density is high.
Second aspect, based on same inventive concept, the embodiment of the present invention provides a kind of think gauge hot continuous rolling steel band with excellent very low temperature CTOD performance, and hot continuous rolling steel band forms based on the production method manufacture of the subsea pipeline hot rolled strip that any embodiment of the present invention is introduced.
Optionally, the mass percent of the chemical composition of subsea pipeline hot rolled strip is: C:0.040-0.080wt%, Si:0.05-0.20wt%, Mn:1.20-1.60wt%, P :≤0.015wt%; S :≤0.0030wt%, Nb :≤0.060wt%, Cr :≤0.20wt%, Ti:0.010-0.025wt%, V :≤0.040wt%, Mo :≤0.15wt%, all the other are Fe and inevitable impurity.
Optionally, carbon equivalent ce≤0.38 of subsea pipeline hot rolled strip, welding cold cracking Sensitivity rate Pcm≤0.17.
Optionally, the transverse yield strength R of hot continuous rolling steel band
t0.5>=510MPa, tensile strength R
m>=610MPa, elongation A
50.8mm>=35% ,-35 DEG C of low-temperature impacts absorb merit average>=390J, and-15 DEG C of Drop-Weight Tear Test (DWTT) DWTT averages are 100% ,-15 DEG C of crack tip opening displacement CTOD average>=1.2mm ,-40 DEG C of CTOD average>=0.9mm.
One or more embodiment of the present invention, at least has following beneficial effect:
A kind of production method with the think gauge hot continuous rolling steel band of excellent very low temperature CTOD performance is provided, comprise the following steps: (1) " complete three take off " is smelted, LF refining, slab continuous casting becomes thickness to be the strand of 230-240mm, wherein smelted by " complete three take off ", LF refining can obtain comparatively high cleanliness to make molten steel, reduce S, the impurity contents such as P, and then make S content≤0.0030% in continuously cast bloom, P content≤0.015%, (2) lower ray examination is carried out to strand, if inspection shows that strand does not satisfy condition through rolling off the production line, flame cleaning is carried out to continuously cast bloom, thus ensure that strand is loaded process furnace and heats by steel strip surface quality (3), wherein, Heating temperature is 1190 ~ 1230 DEG C, equal temperature time >=30min, to make each regional temperature of strand even, ensure the abundant solid solution of alloying element, prevent again undue and uneven the growing up of austenite, (4) roughing technique, it is 1020 ~ 980 DEG C that last passes of roughing technique starts temperature, last reduction in pass 19 ~ 22%, 3rd workpiece thickness is 50 ~ 58mm, thus ensure that austenite crystal is by the repeatedly full and uniform refinement of Static Recrystallization behavior, ensure the complete Static Recrystallization behavior under lesser temps simultaneously, suppress growing up of recrystal grain with this, obtain tiny austenite crystal, (5) finish-rolling process, the temperature in of finish-rolling process is 900 ~ 960 DEG C, finish rolling end reduction in pass controls 9 ~ 12%, finishing temperature is 800 ~ 860 DEG C, after rolling, the thickness of steel band is 16 ~ 20.2mm, the abundant flattening of austenite crystal is ensured with this, obtain higher strain accumulation by finish rolling simultaneously, ensure the abundant refinement of phase-change organization, reduce effective particle size, ensure the abundant flattening of austenite crystal with this, obtain higher strain accumulation by finish rolling simultaneously, ensure the abundant refinement of phase-change organization, reduce effective particle size, (6) laminar flow cooling technology, (7) carrying out the taking-up activities that coiling temperature is 480 ~ 560 DEG C, is the microstructure of target to obtain with acicular ferrite, thus the think gauge subsea pipeline hot continuous rolling steel band of obtained more than 16mm.To provide a kind of production method with the think gauge hot continuous rolling steel band of excellent very low temperature CTOD performance, the method production difficulty is lower, and then can reduce production cost.
Although describe the preferred embodiments of the present invention, those skilled in the art once obtain the basic creative concept of cicada, then can make other change and amendment to these embodiments.So claims are intended to be interpreted as comprising preferred embodiment and falling into all changes and the amendment of the scope of the invention.
Obviously, those skilled in the art can carry out various change and modification to the embodiment of the present invention and not depart from the spirit and scope of the embodiment of the present invention.Like this, if these amendments of the embodiment of the present invention and modification belong within the scope of the claims in the present invention and equivalent technologies thereof, then the present invention is also intended to comprise these change and modification.
Claims (10)
1. there is a production method for the think gauge hot continuous rolling steel band of excellent very low temperature CTOD performance, it is characterized in that, comprise the following steps:
(1) complete three de-smeltings, ladle refining furnace LF refining, slab continuous casting become thickness to be the strand of 230-240mm;
(2) lower ray examination is carried out to described strand, if inspection of rolling off the production line described in passing through shows that described strand does not satisfy condition, flame cleaning is carried out to described continuously cast bloom;
(3) described strand is loaded process furnace to heat, wherein, Heating temperature is 1190 ~ 1230 DEG C, equal temperature time >=30min;
(4) roughing technique, it is 1020 ~ 980 DEG C that last passes of described roughing technique starts temperature, last reduction in pass 19 ~ 22% described, and workpiece thickness is 50 ~ 58mm;
(5) finish-rolling process, the temperature in of described finish-rolling process is 900 ~ 960 DEG C, and finish rolling end reduction in pass controls 9 ~ 12%, and finishing temperature is 800 ~ 860 DEG C, and after rolling, the thickness of steel band is 16 ~ 20.2mm;
(6) laminar flow cooling technology;
(7) when coiling temperature is 480 ~ 560 DEG C, batch, and then obtain described hot continuous rolling steel band.
2. smelting that the method for claim 1, is characterized in that, described " complete three take off ", LF refining, slab continuous casting become thickness to be the strand of 230-240mm, specifically comprise the following steps:
Molten iron is carried out to the pre-treatment of de-S and de-P, make S content≤0.0050% in described molten iron, P content≤0.015%;
Add steel scrap and Mo-Fe alloy at described molten iron, described Mo-Fe alloy is for adjusting the content of Mo in described molten iron, and adding amount of scrap steel accounts for the 8-10% of total molten steel amount; Described molten iron is blended into de-C converter and carries out converter smelting;
Carry out converter tapping, add with the steel stream of described molten steel the deoxidation operation that Al-Fe alloy carries out described molten steel at tapping process; Add Si-Fe alloy, low-carbon Mn-Fe alloy, low-carbon (LC) Cr-Fe alloy subsequently, to carry out the preliminary adjustment of Si, Mn, Cr element;
Carry out the refining of LF stove;
Be cast into by continuous casting process the described continuously cast bloom that thickness is 230 ~ 240mm, in described casting treating processes, carry out dynamic soft-reduction at the solidification end of described molten steel.
3. method as claimed in claim 2, is characterized in that, described in carry out the refining of LF stove, specifically comprise:
Heating makes molten steel to being applicable to teeming temperature, ensures molten steel overheat 15-30 DEG C described in casting process;
Carry out de-S operation, make S content≤0.0030% in described molten steel;
In described molten steel, add Al-Fe, Si-Fe alloy, middle carbon Mn-Fe alloy, low-carbon (LC) Cr-Fe, Ti-Fe alloy and C powder, thus carry out the adjustment of Al, Si, Mn, Cr, Ti, C element;
By feeding Ca-Fe line in described molten steel, denaturing treatment is carried out to inclusion;
Be blown into by the bottom blowing hole of ladle bottom the argon gas that single channel flow is 50 ~ 150L/min, make described inclusion floating.
4. the method as described in as arbitrary in claim 1-3, it is characterized in that, the mass percent of the chemical composition of described hot continuous rolling steel band is: C:0.040-0.080wt%, Si:0.05-0.20wt%, Mn:1.20-1.60wt%, P :≤0.015wt%; S :≤0.0030wt%, Nb :≤0.060wt%, Cr :≤0.20wt%, Ti:0.010-0.025wt%, V :≤0.040wt%, Mo :≤0.15wt%, all the other are Fe and inevitable impurity.
5. the method as described in as arbitrary in claim 1-3, is characterized in that, carbon equivalent ce≤0.38 of described hot continuous rolling steel band, welding cold cracking Sensitivity rate Pcm≤0.17.
6. the method as described in as arbitrary in claim 1-3, is characterized in that, the transverse yield strength R of described hot continuous rolling steel band
t0.5>=510MPa, tensile strength R
m>=610MPa, elongation A
50.8mm>=35% ,-35 DEG C of low-temperature impacts absorb merit average>=390J, and-15 DEG C of Drop-Weight Tear Test (DWTT) DWTT averages are 100% ,-15 DEG C of crack tip opening displacement CTOD average>=1.2mm ,-40 DEG C of CTOD average>=0.9mm.
7. have a think gauge hot continuous rolling steel band for excellent very low temperature CTOD performance, it is characterized in that, described hot continuous rolling steel band forms based on the method manufacture described in the arbitrary claim of claim 1-3.
8. hot continuous rolling steel band as claimed in claim 7, it is characterized in that, the mass percent of the chemical composition of described hot continuous rolling steel band is: C:0.040-0.080wt%, Si:0.05-0.20wt%, Mn:1.20-1.60wt%, P :≤0.015wt%; S :≤0.0030wt%, Nb :≤0.060wt%, Cr :≤0.20wt%, Ti:0.010-0.025wt%, V :≤0.040wt%, Mo :≤0.15wt%, all the other are Fe and inevitable impurity.
9. hot continuous rolling steel band as claimed in claim 7, is characterized in that, carbon equivalent ce≤0.38 of described hot continuous rolling steel band, welding cold cracking Sensitivity rate Pcm≤0.17.
10. hot continuous rolling steel band as claimed in claim 7, is characterized in that, the transverse yield strength R of described hot continuous rolling steel band
t0.5>=510MPa, tensile strength R
m>=610MPa, elongation A
50.8mm>=35% ,-35 DEG C of low-temperature impacts absorb merit average>=390J, and-15 DEG C of Drop-Weight Tear Test (DWTT) DWTT averages are 100% ,-15 DEG C of crack tip opening displacement CTOD average>=1.2mm ,-40 DEG C of CTOD average>=0.9mm.
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