CN105779904B - Low-cost X80 straight welded pipe and preparation method thereof - Google Patents
Low-cost X80 straight welded pipe and preparation method thereof Download PDFInfo
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- CN105779904B CN105779904B CN201410820975.9A CN201410820975A CN105779904B CN 105779904 B CN105779904 B CN 105779904B CN 201410820975 A CN201410820975 A CN 201410820975A CN 105779904 B CN105779904 B CN 105779904B
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- 238000005096 rolling process Methods 0.000 claims abstract description 31
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- 229910052742 iron Inorganic materials 0.000 claims description 4
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Abstract
The invention discloses a low-cost X80 straight welded pipe and a preparation method thereof, wherein the chemical components comprise the following components in percentage by weight: 0.039-0.079% of C, 0.16-0.26% of Si, 1.33-1.83% of Mn1, less than or equal to 0.017% of P, less than or equal to 0.0046% of S, 0.14-0.24% of Cr0.019-0.059% of Nb0.019-0.039% of V, 0.0051-0.028% of Ti, 0.011-0.057% of Al, 0.13-0.28% of Ni and the balance of Fe and trace inevitable impurities, and has the process characteristics that the soaking temperature is 1120-1220 ℃, the two-stage controlled rolling is adopted, and the rolling temperature in a recrystallization zone is 950-1200 ℃; the second stage rolling is non-recrystallization area rolling, and the air cooling final temperature is 650-750 ℃; laminar cooling rate: 5-25 ℃/s, adopting JCO or UO to manufacture the pipe, the expanding ratio e is more than or equal to t/D, the maximum expanding ratio is 2.5%, the effect is that the high-grade X80 longitudinal submerged arc welded pipe is prepared by a low-grade steel plate, the strength and plasticity indexes are excellent, and the production cost is reduced.
Description
Technical field
The invention belongs to technical field of pipeline steel, specifically a kind of inexpensive X80 ERWs and preparation method thereof.
Background technology
As the rapid development of economy, the whole world are growing day by day to the demand of oil, natural gas.Pipeline is as over long distances
One of safest mode of oil gas is conveyed, is received much concern.In recent years, X70, X80 line pipe have become the main flow of pipe-line construction
Pipe.Pass through substantial amounts of production practices, it has been found that straight-line joint submerged arc welding tube is acicular ferrite either iron element when its matrix
During body+pearlite, the steel pipe of particularly X80 and its following rank, after homogeneous tube is expanding, the intensity of steel pipe is not always higher than corresponding
The intensity of steel plate.Therefore, for safety, it has to prepare same level welded tube using same level steel plate.This conservative selection plan
Slightly so that the steel plate purchase cost in pipeline engineering process of construction remains high.It is well known that same thickness, same widths
Pipeline hot rolled plate, with the reduction of intensity rank, steel plate manufacturing cost also decreases.Therefore, using low level steel plate system
Standby high-level steel plate will reduce pipeline engineering construction cost, and this is significant to low steel industry.
Currently, the document on X80 steel plates and its steel pipe is a lot, still prepares X80 straight weld without using low level steel plate
The inconsistent open report of pipe.
Patent CN201110213737.8 discloses a kind of large deformation pipeline steel tube control method for fabrication technology, this method from
Theoretical calculation angle is set out, there is provided the technological parameter of suitable tubulation improves tubulation lumber recovery, and its main purpose is optimization
Tube-making process in itself, rather than for tubulation selection provides reference.Patent CN201110247612.7 discloses high-strength line-pipe use
Steel, steel pipe and its manufacture method, the organization type of the patent steel plate is (F+B, F volume fraction 50%-75%), using UOE systems
Pipe, the yield strength scope of steel pipe is 485-690MPa, and tensile strength scope is 570-825MPa, is not directed to the performance of steel plate,
Not embodying low level steel plate and preparing high-level steel pipe and enlarging rate has the core feature of optimal value.Patent JP200515823A
A kind of excellent pipeline high tensile steel tube of deformation performance and its manufacture method are disclosed, its selection strategy is that steel plate is used at heat
Manage state tissue；In addition, also added the elements such as Mo, Mg, Re in steel, production cost is high.Patent JP2004124167A,
The method for manufacturing of high-strength line-pipe steel plate and steel pipe disclosed in JP2006283147A, required steel plate are organized as needle-like iron
Ferritic, expanding measurer is not known in tube-making process optimal value, it is impossible to gives full play to the potentiality of steel.Patent
CN201310090776.2、CN201310039371.6、CN201210327206.6、CN201210152836.4、
The patents such as CN201110179997.8 only disclose the preparation technology of Pipeline Steel Plate, not publicly design tubulation parameter.
The paper that Su Zhi etc. delivers in the annual meeting in 2011 of welded still pipe academic board of steel rolling branch of Chinese Metals Society
《The development of X90 straight-line joint submerged arc welding tubes》In point out the thick steel containing Mo of 22.9mm using yield strength scope in 500MPa-620MPa
During plate trial-production X90 steel pipes, the steel plate yield strength lifting range after tubulation is 10MPa-179MPa, and this steel does not add
The elements such as Mo, Cu, and define that the expanding scope of tubulation, Zhao Bo etc. exist《Welded tube》The paper that the 10th phase of volume 35 delivers《Tubulation
Technique and strain-aging are to X70 high deformability steel pipe performances》Point out the performance and its (F of X70 level Φ 1016mm × 17.5mm steel pipes
+ B) shape steel plate ratio, yield strength excursion is -50~172MPa after tubulation, the horizontal steel plate of influence level prepare steel pipe,
From the point of view of above-mentioned prior art, the steel plate of non-(F+B) organization type, its yield strength might not rise after tubulation is expanding.For
Safety, during tubulation selection, the identical plate property of generally use can not be utilized farthest, unnecessary so as to cause
Waste.
Summary background technology either all exists for X80 ERWs from composition design and preparation method thereof
The problems such as cost is high, preparation technology is complicated, product Potential model is insufficient.
The content of the invention
Based on above-mentioned X80 straight-line joint submerged arc welding tubes production status, the present invention passes through composition design, organization optimization and expanding amount
The measures such as restriction, realize the X80 straight-line joint submerged arc welding tubes for going out low cost using low level Plate Production.
The present invention breaks traditional selection strategy of pipeline engineering construction, uses (F+B) type hot rolled steel plate to substitute traditional (F+
P) or acicular ferrite type hot rolled steel plate, the expanding amount after cooperation optimization, low level steel plate can be used for preparing high-level steel pipe.
Yield strength is used in the present invention as 450-500MPa, tensile strength is 630-700MPa (F+B) type hot-rolled steel
Plate, after UOE or JCOE shapings, steel pipe property indices can meet the performance requirement of API X80 straight-line joint submerged arc welding tubes.
To realize that the object of the invention present invention takes following measures：
The content range of each composition is by weight percentage in designed ERW in the present invention：C0.039%-
0.079%, Si0.16%-0.26%, Mn1.33%-1.83%, P≤0.017%, S≤0.0046%, Cr0.14%-
0.24%, Nb0.019%-0.059%, V0.019%-0.039%, Ti 0.0051%-0.028%, Al0.011%-
0.057%, Ni 0.13%-0.28%, surplus are Fe and micro inevitable impurity.
ERW of the present invention has the tissue signature of (F+B), wherein F volume fractions 35%-55%.
The main function of each alloy constituent element in the present invention.
C：Most economical in steel, most basic intensified element, have by solution strengthening and precipitation strength to the intensity for improving steel
Obvious effect, but improve C content has negative effect to the ductility, toughness and weldability of steel, therefore, the present invention is by C content
Limit is set as 0.079%.The evolution of modern age pipe line steel is the continuous process for reducing C content.C content is reduced on the one hand to help
In the toughness for improving steel, the welding performance of steel on the other hand can be improved.When C content is too low, it is impossible to give full play to the elements such as Nb
Precipitation enhancement, the present invention by C content lower limit set be 0.039%.
Si：Addition Si is the intensity for deoxidation in steelmaking process and raising matrix, while has the ferritic work of purification
With the forming core for reducing pearlite is inclined to.If the Si of excessive addition, the toughness of the welding heat affected zone of mother metal will significantly drop
Low, welding procedure performance in field can also be deteriorated.Therefore, Si contents are set as 0.16-0.26% in the present invention.
Mn：The intensity of steel is improved by solution strengthening, is that compensation causes loss of strength because C content reduces in pipe line steel
Main and most economical intensified element.Mn still expands the element of γ phase regions, can reduce γ → α phase transition temperatures of steel, help
In obtaining tiny phase-change product, the toughness of steel can be improved, reduce ductile-brittle transition temperature.In order to proof strength and low-temperature flexibility it
Between balance, Mn minimum content is set as 1.33%.Mn content, the hardenability characteristic increase of steel are improved, content increases to one
After determining degree, welding performance can be caused to decline the toughness of especially severe exacerbation welding heat affected zone.In addition, too high Mn contents
Continuous casting billet center segregation can also be increased, make the anisotropy of plate property increase.Therefore, Mn upper content limits of the invention are designed as
1.83%.
Nb：It is one of most important element in modern microalloying pipe line steel, the effect to crystal grain refinement is fairly obvious.It is logical
The recovery and recrystallization that NbC strain induced precipitates during hot rolling hinder deformed austeaite is crossed, is cooled down by controlled rolling and control
It is organized in the deformed austeaite of non-recrystallization zone rolling and is changed into tiny phase-change product during phase transformation, so that steel has high intensity
And high tenacity.The present invention is exactly to coordinate C content to add the effect that appropriate Nb plays NbC, and the present invention chooses Nb content ranges
0.019%-0.059%.
Ti：It is strong solid N element, Ti/N stoichiometric proportion is 3.42, and steel can be fixed using 0.01% or so Ti
Middle 30ppm or so N, the TiN precipitated phases of tiny high-temperature stable can be formed in sheet billet continuous casting.This tiny TiN particles
Austenite Grain Growth when slab reheats can effectively be suppressed, be favorably improved solid solubility of the Nb in austenite, improved
The impact flexibility of welding heat affected zone.When Al content is too low (as being less than 0.005%), Ti can form oxide, life in these
Particle can play a part of Intragranular Acicular Ferrite forming core core, refinement welding heat affected zone tissue.In order to obtain this effect, extremely
0.0051%Ti is added less.When Ti additions exceed certain certain value, TiN particles will be roughened, and TiC precipitation enhancement shows
It is existing, cause low-temperature flexibility to deteriorate.Therefore, the present invention chooses Ti content ranges 0.0051%-0.028%.
V：It is one of most important element in modern microalloy steel for pipeline as Nb, Ti, there is good precipitation strength
Effect.With the compound addition of Nb, Ti, 1+1 can be played>2 effect.The present invention chooses V content scope 0.019%-0.039%.
Al：Al presence also plays the role of thinning microstructure typically as the deoxidier in steel.But when Al content
More than 0.057%, the amount of aluminum oxide nonmetal inclusion increases so as to reduce the cleanliness factor of steel.Al content is too low, and deoxidation is not filled
Point, the oxidizable element such as Ti will form oxide, therefore Al content lower limit set is 0.011%.
Cr：It is to expand γ phase regions, postpones and ferrite formation is first separated out during γ → α phase transformations, promotes the main of bainite formation
Element, to control, phase-change organization plays an important role, and is added under certain cooling condition and finishing temperature in Ultra-low carbon pipe line steel,
Obvious bainite structure is achieved with, while because phase transformation is to the transformation of low temperature direction, tissue can be made further to refine, structure refinement
Be advantageous to the improvement of low-temperature flexibility.In order to obtain the reasonably combined of intensity, plasticity and toughness, the present invention chooses Cr0.14%-
0.24%.
Ni：The intensity of steel can be improved by solution strengthening effect, Ni addition is mainly beneficial to low-temperature flexibility.Advised in thickness
Can also compensate for because of caused by the increase of thickness water cooling intensity deficiency in lattice pipe line steel and caused by toughness decline.The present invention chooses
Ni0.13%-0.28%.
P、S：It is inevitable impurity element in steel, it is desirable to more low better., again can not nothing for the consideration of smelting cost
What is limited is low.Therefore, P, S upper content limit are set as 0.017% and 0.0046% by the present invention.Pass through ultralow S (being less than 30ppm)
And Ca processing carries out inclusion morphology control to sulfide, and pipe line steel can be made to have high impact flexibility.
The process route that the present invention uses for：Stock → converter or electric furnace smelting → external refining → continuous casting → slab add again
Heat → controlled rolling and controlled cooling → plate property is examined and scale → JCOE or UOE tubulations.
Concretely comprise the following steps:
A) to carrying out all heat-treated after the as cast condition blank cleaning in set component control range, temperature control is in 1120-
In the range of 1220 DEG C；
B) high-pressure water descaling is carried out to the blank after coming out of the stove, removes blank caused iron scale in heating process；
C) in order to ensure excellent obdurability matching, two-stage control rolling technique is employed during Plate Production, it is right
Blank after de-scaling carries out two-stage control rolling, accurate rolling temperature control and pass deformation and cumulative deformation immediately；
Wherein first stage rolling rolls for recrystallization zone, the temperature controlling range of recrystallization zone controlled rolling：950-1200℃；The rank
The single pass heavy deformation of at least continuous three passages of section follows 10%-15%-20% drafts changing rule, abundant to obtain
Refine the purpose of original austenite grains；Second stage rolling rolls for non-recrystallization zone, the temperature of non-recrystallization zone controlled rolling
Spend control range：750-900 DEG C, the cumulative deformation in the stage is not less than 60%, completes in fetrite grain refinement and crystal grain
The task of position dislocation density accumulation.
D) steel plate after finish to gauge first carries out air cooling relaxation, and 35%-55% austenite is changed into block iron element during air cooling
Body, 650-750 DEG C of air cooling finishing temperature.
E) section cooling is carried out to the steel plate after air cooling relaxation, section cooling begins to cool down temperature：650-750℃；Eventually
Only chilling temperature：300-500℃；Cooling velocity：5-25℃/s.Steel plate after section cooling is air-cooled to room temperature.
In Cooling Process, remaining austenite is changed into bainite structure, finally gives the steel of (F+B) duplex structure
Plate, wherein F volume fractions 35%-55%, its horizontal mechanical performance can reach following requirement：Yield strength Rt0.5 is 450-
500MPa, tensile strength Rm are 630-700MPa, yield tensile ratio Rt0.5/Rm≤0.75, -20 DEG C of ballistic work CVN >=260J, -20 DEG C
DWTT section of shear SA >=85%.
F) selection of the optimal expanding amounts of JCOE or UOE
Effect most basic expanding E after JCO or UO tubulations is to ensure the accurate geometry of steel pipe.After steel pipe O forming,
Its inwall compression chord, outer wall tension stress, in subsequent tensile property detection, due to the influence of Bauschinger effect, sample
Inner side intensity declines, and outer wall intensity rises, thus sample bulk strength has the complex situations for rising and having drop.In order to ensure tubulation
Afterwards, the intensity of steel keeps rising, it is necessary to expanding amount is maintained in a rational scope, i.e., steel pipe is integrally in drawing and answered
Power state, expanding amount now should meet e >=t/D limitation.In order to ensure the safety of steel pipe, enlarging rate maximum is not to be exceeded
2.5%.
The derivation of expanding amount minimum value is as described below.
Take D, t, D ', t ', e represent respectively the external diameter before pipe expanding, wall thickness, it is expanding after external diameter, wall thickness and enlarging rate,
The relation of these parameters is as follows
(D '-D)/D=e formulas 1
D '=(1+e) D formulas 2
T=(1+e) t ' formulas 3
According to the internal diameter of expanding rear steel pipe not less than expanding preceding pipe diameter and the average value of external diameter
That is D '/2-t ' >=D/2-t/2 formulas 4
Because enlarging rate is much smaller than 100%, the present invention takes maximum to be no more than 2.5%, then expanding front and rear steel plate thickness can
To think equal, then convolution 1- formulas 4 can obtain following relational expression
E >=t/D formulas 5.
As above made steel pipe can reach after JCO or UO shapings, then through E processes, the horizontal mechanical performance of made steel pipe
It is following to require：Yield strength Rt0.5 is 555-600MPa, and tensile strength Rm is 630-710MPa, yield tensile ratio Rt0.5/Rm≤
0.86, -15 DEG C of ballistic work CVN >=260J, -10 DEG C of DWTT section of shear SA >=85%.
The advantage of the invention is that：
(1) present invention has the obvious feature of tubulation post-processing hardening effect for (F+B) duplex structure, thin with crystal grain
Based on the material reinforcement theory such as change, phase transformation strengthening, precipitation strength and dislocation strengthening, to the composition with duplex structure's pipe line steel
Design employs low-carbon plus Mn, super-low sulfur, Nb, V, Ti combined microalloying, controls the Cr alloyings of tissue and is suitably added
Ni, Mo, Cu composition design are not added, significantly reduces production cost；
(2) hot rolling technology employs the thermo-mechanical processi technology of controlled rolling and controlled cooling, is carried out most by rational composition and technique
The organizational controls of finished product, to obtain (F+B) tissue with high intensity, high tenacity.The method rolled using two-stage control,
In deformation process, using suitable deformation temperature and deflection, austenite crystal is set effectively to be refined；Middle base air cooling treats temperature
In the stage, Niobium Carbonitride Second Phase Precipitation is obvious, and austenite grain boundary obtains effectively pin, and crystal grain stability is good, will not occur
Obvious grain coarsening phenomenon；
(3) after finish to gauge, steel plate carries out air cooling and treats temperature, and making the austenite of 35%-55% in steel plate, to be changed into plasticity excellent
Polygonal ferrite；
(4) treat the steel plate after temperature and carry out laminar flow order but, cooling velocity scope control is in 5-25 DEG C/s, final cooling temperature control
In the range of 300-500 DEG C, ensure in Cooling Process, remaining austenite is changed into bainite structure, the polygon first separated out
Ferrite will not substantially grow up, and finally give (F+B) duplex structure；
(5) steel plate after section cooling is air-cooled to room temperature, and intensity and plasticity index are excellent；
(6) steel plate is qualified through performance detection and after cutting scale, carries out JCO or UO shapings, and E is molded again after welding, in E shapings
Enlarging rate e range of choice is t/D × 100%≤e≤2.5%, and the yield strength of steel pipe rises substantially compared with steel plate, at least risen
70MPa, its horizontal mechanical performance can reach following requirement：Yield strength Rt0.5 is 450-500MPa, and tensile strength Rm is
630-700MPa, yield tensile ratio Rt0.5/Rm≤0.75, -20 DEG C of ballistic works CVN >=260J, -20 DEG C of DWTT sections of shear SA >=
85%；So that low level steel plate prepares high-level X80 straight-line joint submerged arc welding tubes and become a reality.
Embodiment
With reference to embodiment, the present invention is further described：
The content range of each composition is by weight percentage in designed steel pipe in the present invention：C0.039%-0.079%,
Si0.16%-0.26%, Mn1.33%-1.83%, P≤0.017%, S≤0.0046%, Cr0.14%-0.24%,
Nb0.019%-0.059%, V0.019%-0.039%, Ti 0.0051%-0.028%, Al0.011%-0.057%, Ni
0.13%-0.28%, surplus are Fe and micro inevitable impurity.
The process route that the present invention uses for：Stock → converter or electric furnace smelting → external refining → continuous casting → slab add again
Heat → controlled rolling and controlled cooling → plate property is examined and scale → JCOE or UOE tubulations.
Concretely comprise the following steps:
A) to carrying out all heat-treated after the as cast condition blank cleaning in set component control range, temperature control is in 1120-
In the range of 1220 DEG C；
B) high-pressure water descaling is carried out to the blank after coming out of the stove, removes blank caused iron scale in heating process；
C) in order to ensure excellent obdurability matching, two-stage control rolling technique is employed during Plate Production, it is right
Blank after de-scaling carries out two-stage control rolling, accurate rolling temperature control and pass deformation and cumulative deformation immediately；
Wherein first stage rolling rolls for recrystallization zone, the temperature controlling range of recrystallization zone controlled rolling：950-1200℃；The rank
The single pass heavy deformation of at least continuous three passages of section follows 10%-15%-20% drafts changing rule, abundant to obtain
Refine the purpose of original austenite grains；Second stage rolling rolls for non-recrystallization zone, the temperature of non-recrystallization zone controlled rolling
Spend control range：750-900 DEG C, the cumulative deformation in the stage is not less than 60%, completes in fetrite grain refinement and crystal grain
The task of position dislocation density accumulation.
D) steel plate after finish to gauge first carries out air cooling relaxation, and 35%-55% austenite is changed into block iron element during air cooling
Body, 650-750 DEG C of air cooling finishing temperature.
E) section cooling is carried out to the steel plate after air cooling relaxation, section cooling begins to cool down temperature：650-750℃；Eventually
Only chilling temperature：300-500℃；Cooling velocity：5-25℃/s.Steel plate after section cooling is air-cooled to room temperature.
F) present invention is to ensure the accurate geometry of steel pipe using the most basic effects of the expanding E after JCO or UO tubulations.
Enlarging rate should meet e >=t/D limitation.In order to ensure the safety of steel pipe, enlarging rate maximum is not to be exceeded 2.5%.
The present invention use above-mentioned design composition and the embodiment 1-10 of technique as several preferred forms, its it is chemical into
Point, technological parameter and results of property be as shown in table 1-4.
1. chemical composition
Embodiment 1-10 chemical composition (wt%) such as table 1.
The chemical composition of table 1 (wt%)
| C | Si | Mn | P | S | Ti | Nb | V | Ni | Cr | Al | |
| 1 | 0.039 | 0.16 | 1.33 | 0.01 | 0.003 | 0.017 | 0.019 | 0.019 | 0.28 | 0.14 | 0.04 |
| 2 | 0.049 | 0.23 | 1.53 | 0.01 | 0.003 | 0.012 | 0.039 | 0.039 | 0.21 | 0.24 | 0.03 |
| 3 | 0.059 | 0.26 | 1.73 | 0.01 | 0.003 | 0.015 | 0.059 | 0.029 | 0.13 | 0.19 | 0.03 |
| 4 | 0.069 | 0.23 | 1.83 | 0.01 | 0.003 | 0.015 | 0.029 | 0.021 | 0.26 | 0.16 | 0.03 |
| 5 | 0.079 | 0.16 | 1.43 | 0.01 | 0.003 | 0.015 | 0.049 | 0.031 | 0.18 | 0.23 | 0.03 |
| 6 | 0.039 | 0.16 | 1.43 | 0.01 | 0.003 | 0.015 | 0.019 | 0.031 | 0.28 | 0.23 | 0.03 |
| 7 | 0.049 | 0.23 | 1.83 | 0.01 | 0.003 | 0.015 | 0.039 | 0.021 | 0.21 | 0.16 | 0.03 |
| 8 | 0.059 | 0.26 | 1.73 | 0.01 | 0.003 | 0.015 | 0.059 | 0.029 | 0.13 | 0.19 | 0.03 |
| 9 | 0.069 | 0.23 | 1.53 | 0.01 | 0.003 | 0.015 | 0.029 | 0.039 | 0.26 | 0.24 | 0.03 |
| 10 | 0.079 | 0.16 | 1.33 | 0.01 | 0.003 | 0.015 | 0.049 | 0.019 | 0.18 | 0.14 | 0.03 |
2. hot rolling technology
Process route is as follows：Stock → converter or electric furnace smelting → external refining → casting → slab reheating → control are rolled
System → control cooling.
Embodiment 1-10 technological parameter is shown in Table 2.
The technological parameter of table 2
3. results of property
Mechanics, Charpy impact, DWTT experiments, embodiment 1-10 horizontal plate property result of the test such as table 3 are carried out respectively
Shown, steel tube performance is as shown in table 4.
The steel plate horizontal mechanical performance result of table 3
The steel pipe transverse mechanical property result of table 4
Claims (1)
- A kind of 1. preparation method of inexpensive X80 ERWs, it is characterised in that the process route used for：Stock → converter Or electric furnace smelting → external refining → continuous casting → slab reheating → controlled rolling and controlled cooling → plate property examine with scale → JCOE or UOE tubulations,Concretely comprise the following steps:A) to carrying out all heat-treated after the as cast condition blank cleaning in set component control range, temperature control is at 1120-1220 DEG C In the range of；B) high-pressure water descaling is carried out to the blank after coming out of the stove, removes blank caused iron scale in heating process；C) rolled using two-stage control, two-stage control rolling is carried out immediately to the blank after de-scaling, the wherein first stage rolls It is made as recrystallization zone rolling, the temperature controlling range of recrystallization zone controlled rolling：950-1200℃；The stage is at least continuous three The single pass heavy deformation of passage follows 10%-15%-20% drafts changing rule, and second stage rolling is non-recrystallization zone Rolling, the temperature controlling range of non-recrystallization zone controlled rolling：750-900 DEG C, the cumulative deformation in the stage is not less than 60%；D) steel plate after finish to gauge first carries out air cooling relaxation, and 35%-45% austenite is changed into granular ferrite during air cooling, empty Cold 650-750 DEG C of finishing temperature；E) section cooling is carried out to the steel plate after air cooling relaxation, 55%-65% austenite is changed into bayesian during section cooling Body, section cooling begin to cool down temperature：650-750℃；Terminate chilling temperature：300-500℃；Cooling velocity：5-25 DEG C/s, Steel plate after section cooling is air-cooled to room temperature, and steel plate yield strength is 450-500MPa, tensile strength 630-700MPa；F) steel plate of room temperature is air-cooled to through performance detection and after cutting scale, and using JCO or UO tubulations, enlarging rate meets e >=t/D's Limitation, enlarging rate maximum are not to be exceeded 2.5%,Wherein e：Steel pipe expanding rate,t：Thickness of steel pipe,D：Outer diameter of steel pipes；Steel pipe property indices can meet the performance requirement of API X80 straight-line joint submerged arc welding tubes；The chemical composition of steel pipe, by weight Measure percentage：C0.039%-0.079%, Si0.16%-0.26%, Mn1.33%-1.83%, P≤0.017%, S≤ 0.0046%, Cr0.14%-0.24%, Nb0.019%-0.059%, V0.019%-0.039%, Ti 0.0051%- 0.028%, Al0.011%-0.057%, Ni 0.13%-0.28%, surplus are Fe and micro inevitable impurity.
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| CN108531814B (en) * | 2018-05-22 | 2020-06-12 | 湖南华菱湘潭钢铁有限公司 | Preparation method of large-diameter X80 longitudinal submerged arc welded pipe |
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| CN101456034A (en) * | 2009-01-06 | 2009-06-17 | 北京科技大学 | X80 level large-deformation resistance pipe line steel medium and heavy plate production method |
| CN102666898A (en) * | 2009-11-25 | 2012-09-12 | 杰富意钢铁株式会社 | Welded steel pipe for linepipe with superior compressive strength, and process for producing same |
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| CN102666898A (en) * | 2009-11-25 | 2012-09-12 | 杰富意钢铁株式会社 | Welded steel pipe for linepipe with superior compressive strength, and process for producing same |
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