CN106319390A - X70 large deformation resistant pipeline steel and manufacturing method thereof - Google Patents
X70 large deformation resistant pipeline steel and manufacturing method thereof Download PDFInfo
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Abstract
The invention discloses X70 anti-large deformation pipeline steel and a manufacturing method thereof, wherein the steel comprises, by mass, 0.04% -0.09% of C, 0.15% -0.55% of Si, 1.45% -1.75% of Mn, 0.04% -0.10% of Nb, 0.02% -0.08% of V, 0.01% -0.03% of Ti, 0% -0.20% of Cu, 0.15-0.55% of Ni, 0-0.15% of Mo, 0.15% -0.45% of Cr, 0.025% -0.045% of Al, 0.0002% -0.011% of N, less than or equal to 0.015% of P, less than or equal to 0.005% of S, and the balance Fe and other inevitable impurity elements. The production adopts the following process route: the method comprises the steps of material preparation → converter or electric furnace smelting → external refining → casting → slab reheating → controlled rolling → controlled cooling, tempering after two-phase zone quenching or not adopting a tempering process.
Description
Technical field
The invention belongs to technical field of pipeline steel, relate to a kind of X70 large-deformation-resistance pipeline steel and manufacture method, particularly to a kind of X70 large-deformation-resistance pipeline Wide and Thick Slab using two-phase section process for quenching to prepare and preparation method thereof.Pipeline Wide and Thick Slab prepared by the application present invention, can apply to manufacture based on stress design area Longitudinal SAW Pipe.
Background technology
Along with petroleum resources demand increases day by day, the investment construction of new oil gas field gradually increases.Due to the grown place of oil gas, generally require geological conditions such as passing through permafrost band, earthquake zone with area of consumption the most regional, it is thus desirable to long-distance oil & gas pipeline meets requirement based on stress design: the lateral performance of steel pipe meets traditional requirement based on stress design, and longitudinal performance has the feature of anti-large deformation.The typical performance parameter characterizing anti-large deformation feature is yield tensile ratio low (Rt0.5/Rm≤0.80), and uniform elongation is high (UEL >=10%), and stress-strain diagram is thole top-type.In order to quantify the stress-strain diagram of thole top-type, generally using strain hardening exponent n or stress ratio Rt1.5/Rt0.5, Rt2.0/Rt1.0, Rt5.0/Rt1.0, stress ratio index has measurement simplicity, the advantages such as description curve shape is more accurate relative to n.
For the property of resisting large deformation needed for reaching based on stress design, have two kinds of means: 1) use thick walled steel tube；2) the Plate Production steel pipe of duplex structure is used.In actual application, both approaches is not isolated.If improving anti-large deformation ability only with the mode increasing wall thickness, steel plate thickness is the thickest, and industrialized production difficulty is big and cost of investment sharply increases.Based on this, current large-deformation resistance pipe is provided with the feature of heavy wall and two-phase simultaneously.
At present, producing the large deformation Pipeline Steel Plate of heavy wall two-phase, have two kinds of process routes, one is the rolled supply of material after controlled rolling and controlled cooling, and a kind of is to re-use after the steel plate after controlled rolling and controlled cooling carries out heat treatment.Because steel plate wall thickness is big, the dual phase sheet steel that traditional TMCP technique produces, performance exists the shortcomings such as same plate difference is big, low temperature DWTT properties percent of pass is low, there is banding rank organizationally high, along deficiencies such as wall thickness direction uneven microstructure.
In order to overcome these technological deficiencies, heat treatment step can be increased on the basis of TMCP technique.At present, the open source literature using heat treatment mode production large deformation pipe line steel is the rarest.Patent CN201110054270.7 discloses " a kind of large-deformation-resistance pipeline steel with excellent aging resistance and production method thereof ", its steel plate roll rear water-cooled speed low, terminate chilling temperature height be easily generated thick MA, unfavorable to subsequent heat treatment technology controlling and process；Patent CN201010266539.3 discloses " large-deformation-resistance pipeline steel prepared by a kind of heat treatment method and preparation method thereof ", its steel plate thickness 10-25mm, and is not directed to the production technology of rolled steel plate；Patent CN201010289370.3 discloses " low yield strength ratio fine grain, high strength Pipeline Steel Plate and production method thereof ", and its intermediate blank lets cool thin only have finished steel plate 1.7-2.0 times of thickness and rolled final cooling temperature height is easily generated thick rich carbon phase MA constituent element；Patent CN201010235925.6 discloses " a kind of method of manufacturing pipeline steel medium plate with excellent tenacity through normalizing rolling ", and this patent is not intended to produce large-deformation-resistance pipeline steel, and its grade of steel is only X65.
In sum, for subject matters such as the low temperature DWTT poor performance of existence from the point of view of X70 level large-deformation resistance pipe line steel, banded structure rank height, thickness of slab direction uneven microstructure.
Summary of the invention
It is an object of the invention to provide a kind of X70 large-deformation-resistance pipeline steel and preparation method thereof, produce, the weak point such as banded structure rank high big with plate difference performance difference present in large-deformation-resistance pipeline steel process solving current TMCP technique, produce thickness specification the most further higher based on stress design area Wide and Thick Slab, to meet the requirement of Wide and Thick Slab used by X70 and above rank large-deformation-resistance pipeline steel.
Present invention employs the two-phase section quenching technology being more beneficial for improving steel plate property of resisting large deformation, this technology has the advantages such as rate of cooling is higher, the control of steel plate tissue ratio is accurate.Add after thinking about it quenching process, although in operation more complicated, but the structural homogenity of steel plate, properties percent of pass increase substantially with stability, particularly to the thickness steel plate for anti-large deformation more than 25mm, the cost performance that heat treatment produces is substantially better than the cost performance that TMCP produces.
In the present invention, finished steel plate thickness t (unit, mm) represents.
It is an object of the invention to be achieved through the following technical solutions:
X70 large-deformation-resistance pipeline steel of the present invention, it is characterized in that: in this steel, the mass percent of chemical composition is C 0.04%-0.09%, Si 0.15%-0.55%, Mn 1.45%-1.75%, Nb 0.04%-0.10%, V 0.02%-0.08%, Ti 0.01%-0.03%, Cu 0%-0.20%, Ni 0.15-0.55%, Mo 0-0.15%, Cr 0.15%-0.45%, Al 0.025%-0.045%, N 0.0002%-0.011%, P≤0.015%, S≤0.005%, remaining be Fe and other be inevitable impurity element.
In the present invention, the destination organization of large-deformation-resistance pipeline steel plate is ferrite by obvious two phase compositions of nonhomogeneous hardness, the softest phase, including polygonal ferrite, quasi-polygonal ferrite, or their any mixture；Hard is bainite, MA constituent element, martensite, or their any mixture mutually；Ferritic volume fraction is 35%-65%；Ferrite crystal grain average diameter is 3-11um.
Selecting two-phase structure is based on considered below: ferrite is as soft phase, it is provided that low yield strength and high uniform elongation；Bainites etc. can provide high-tensile firmly mutually；Suitable soft or hard Phase Proportion, it is possible to achieve intensity, low-temperature flexibility, the matched well of property of resisting large deformation, thus meet whole requirements based on stress design pipe line steel.When ferrite volume fraction is identical, increase ferrite grain size, be conducive to improving uniform extension numerical value and reducing yield tensile ratio；Ferrite crystal grain is the thickest, and the low-temperature flexibility of steel plate can affect adversely.Therefore, the ferrite volume fraction that the present invention chooses is 35-65%, and ferrite average diameter is 3-11um.
The effect mainly comprising composition in steel of the present invention is as follows:
C: intensified element most economical, most basic in steel, the intensity of steel can be significantly improved by solution strengthening and precipitation strength, but improving C content and to ductility, the toughness of steel and be welded with negative effect, modern age, the evolution of pipe line steel was the process constantly reducing C content.When C content is too low, it is impossible to give full play to the precipitation strength effect of the elements such as Nb.Therefore C content range set is 0.04%-0.09% by the present invention.
Si: adding Si is that Si also has the effect that suppression cementite is formed for deoxidation and the intensity of raising matrix in steelmaking process.If adding the Si of excess, the toughness of mother metal and welding heat affected zone thereof will significantly reduce, field welding procedure degradation.Therefore, Si content is set as 0.15%-0.55% in the present invention.
Mn: improved the intensity of steel by solution strengthening, is to compensate in pipe line steel to cause the main and most economical intensified element of loss of strength because C content reduces.Mn still expands the element of γ phase region, it is possible to decrease γ → α phase transition temperature of steel, contributes to obtaining tiny phase-change product in temperature-fall period, can improve the toughness of steel, reduce ductile-brittle transition temperature；In temperature-rise period, ferrite can be realized at lower temperature and separate out and grow up.Improving the content of Mn, the quenching degree of steel increases, and after content increases to a certain degree, welding performance can be caused to decline the toughness of especially severe exacerbation welding heat affected zone.It addition, too high Mn content also can increase continuous casting billet center segregation, the anisotropy of plate property is made to increase.For the balance between proof strength and low-temperature flexibility and higher slab quality, the Mn content range of the present invention is designed as 1.45%-1.75%.
Nb: being one of topmost micro alloying element in modern pipe line steel, the effect to crystal grain refinement is fairly obvious.The recovery and recrystallization of deformed austeaite is hindered by NbC strain induced precipitate in course of hot rolling, through controlled rolling with control the deformed austeaite that cooling makes non-recrystallization zone roll and be organized in phase transformation and be changed into tiny phase-change product, so that steel has high intensity and high tenacity.The present invention is just to cooperate with C content and adds the effect of appropriate Nb performance NbC, Nb content range 0.04%-0.10%.
V: C or N is combined in steel, has the strongest precipitation strength effect.Compared with Nb, the carbonitride crystallization of the dissolution and precipitation equilibrium temperature containing V is low, is conducive to back dissolving and precipitation under relatively low heating temperature condition, thus plays the effect of anchoring crystal boundary crystal grain thinning.Heat at two-phase section, the carbonitride of Nb, Ti can not back dissolving, and have the tendency grown up, V, because this problem can be there is not with back dissolving, is therefore more suitable for two-phase section heating and uses and act on realizing crystal grain refinement, precipitation strength etc..Too much V is unfavorable to casting process, therefore V content scope 0.02%-0.08% that the present invention chooses.
Ti: being strong solid N element, the stoichiometric proportion of Ti/N is 3.42, utilizes the Ti of about 0.01% just can fix the N of about 30ppm in steel, can form the TiN precipitated phase of tiny high-temperature stable when sheet billet continuous casting.Austenite Grain Growth when this tiny TiN particle can suppress slab to reheat effectively, is favorably improved Nb, V solid solubility in austenite, improves the impact flexibility of welding heat affected zone.When the content of Als too low (as less than 0.005%), Ti can form oxide, and in these, raw particle can play the effect of Intragranular Acicular Ferrite forming core core, refinement welding heat affected zone tissue.In order to obtain this effect, 0.005%Ti to be added.When Ti addition exceedes certain certain value, and TiN granule will be roughened, and the precipitation strength effect of TiC manifests, and causes low-temperature flexibility to deteriorate.Therefore, the present invention chooses Ti content range 0.01%-0.03%.
The existence of Al:Al, typically as the deoxidizer in steel, also has the effect of thinning microstructure.But, when the content of Al is too much, and the amount of aluminium oxide nonmetal inclusion increases thus reduces the cleanliness factor of steel.The oxidizable element recovery rates such as the too low then deoxidation of Al content is insufficient, Ti are low, and therefore the content range of Al is set as 0.025%-0.045%.
Cu, Ni: can be improved the intensity of steel by solution strengthening effect, Cu can also improve the corrosion resistance of steel simultaneously, and the addition of Ni mainly improves the red brittleness that Cu causes in steel, and Ni itself is also useful to low-temperature flexibility.In think gauge pipe line steel, can also compensate for that the water-cooled intensity that causes because of the increase of thickness is not enough and that cause intensity declines.The present invention chooses Cu 0%-0.20%, Ni 0.15%-0.55%.
Cr, Mo: add Cr, Mo element, CCT curve can be made to move to right, the stability of austenite increases, thus promote bainitic transformation, play an important role to controlling phase-change organization, when Cr content is less than 7%, A3 point declines, phase transformation changes to low temperature direction, and tissue can be made to refine further, and structure refinement is conducive to the improvement of low-temperature flexibility.During heat treatment step, suitable Cr, Mo content, it is possible to achieve heat treatment heating-up temperature and the optimization of temperature retention time.Reasonably combined with toughness in order to obtain intensity, plasticity, the present invention chooses Mo 0-0.15%, Cr 0.15%-0.45%.
N:N is one of inevitable impurity element in steel, content is unsuitable too high, but the nitride forming element chemical combination such as N Yu Al, Ti, Nb, V, anchoring crystal boundary crystal grain thinning and the effect of precipitation strength can be played, therefore in steel, N element is not the lowest more good, and it is 0.0002%-0.011% that the present invention chooses the content range of N
P, S: be inevitable impurity element in steel, it is desirable to the lowest more good.For smelting cost and the restriction of production technology, again can not be unconfined low.Therefore, P, S upper content limit is set as 0.015% and 0.005% by the present invention.Processed by ultralow S (less than 50ppm) and Ca and sulfide is carried out inclusion morphology control, the low-temperature flexibility of raising pipe line steel can be made.
The present invention has low manganese, adds the feature of vanadium.Manganese is low, and transformation temperature is low, and ferrite can separate out more amount in relatively low temperature, and ferritic size is the most tiny.
The present invention a kind of X70 large-deformation-resistance pipeline steel is that thickness targets is 26.4mm and above, steel plate uses 230mm-300mm thickness steel billet to carry out the TMCP rolled steel plate produced on cut deal reciprocating rolling mill.
TMCP rolled steel plate used by the present invention a kind of X70 large-deformation-resistance pipeline steel uses following process route: get the raw materials ready → converter or electric furnace smelting → external refining → casting → slab reheating → controlled rolling → control cools down.
Its TMCP technological temperature and cooling rate are controlled according to following parameter: slab heating temperature 1050-1250 DEG C；Recrystallization zone controlled rolling starts temperature 950-1150 DEG C, recrystallization zone controlled rolling final temperature 900-1100 DEG C；Noncrystalline domain controlled rolling starts temperature 830-900 DEG C, noncrystalline domain controlled rolling final temperature 805-850 DEG C；Section cooling begins to cool down temperature 785-835 DEG C, and section cooling terminates chilling temperature 450-550 DEG C, section cooling rate of cooling: 5-25 DEG C/s.
Its TMCP technique reduction in pass is controlled according to following parameter with accumulation drafts: recrystallization zone has rolled rear workpiece thickness (3.0-4.0) t；During recrystallization zone stage rolling, recrystallization zone total deformation 45%-65%；Single pass heavy deformation adjusts according to steel billet exit thickness, when steel billet exit thickness is more than or equal to 7.5t or when being less than 5.9t, and single pass heavy deformation 10%-14%；When steel billet exit thickness is less than 7.5t and is more than or equal to 5.9t, single pass heavy deformation 16%-24%；Non-recrystallization zone cumulative deformation is not less than 65%.
The technological parameter that its TMCP stage is used, based on the insight that
Slab heating temperature: continuous casting billet is through again reheating, and original thick as cast condition dendrite is through reaustenitizing, it is achieved homogenization of composition refines with crystal grain, provides necessary tissue preparation to prepare with temperature for rolling state.Austenite has high plastic deformation's ability, and temperature its mobility the highest is the best, but temperature too high Austenite Grain Growth tendency becomes big.Temperature is too low, and austenite deformation drag becomes big, and the pass deformation in this stage is restricted, and in order to reach good austenitizing effect, slab heating temperature scope of the present invention is designed as 1050-1250 DEG C.
Recrystallization zone controlled rolling temperature and deflection: recrystallization zone controlled rolling, be the characteristic utilizing Austenite Dynamic Recrystallization with Static Recrystallization, make the Austenite Grain Refinement after thick heating of plate blank.In order to realize austenitizing recrystallization, in the case of temperature is certain, there is minima in pass deformation, based on this, this stage single pass heavy deformation is the bigger the better, but due to mill capacity, billet bloom size and the problem such as final steel plate gauge lattice mate, single pass heavy deformation again can not be arbitrarily devised.It addition, temperature is high, occur the single pass least amount of deformation needed for recrystallization the least, but the crystal grain coarsening rate now after recrystallization is the fastest；Temperature is low, and crystal grain coarsening rate is little, but required single pass least amount of deformation is consequently increased；Temperature is low to a certain extent, recrystallization would not occur again, austenite deformation the most just loses the effect of recrystallization softening crystal grain.In this stage, after total deformation is more than 60%, recrystallization is the most inconspicuous to the thinning effect of crystal grain.Therefore, the recrystallization stage control rolling of the present invention starts temperature 950-1150 DEG C, final temperature 900-1100 DEG C；Single pass heavy deformation is chosen as 10%-14% or 16%-20% and total deformation 45%-65% according to steel billet exit thickness.
Non-recrystallization zone controlled rolling temperature and deflection: non-recrystallization rolls, on temperature upper limit designs, need consideration to avoid incomplete recrystallization section, in order to avoid producing mixed grain structure, uniformity and low-temperature flexibility to plate property adversely affect.The rolling of non-recrystallization is because there is accumulative effect in deformation, the resistance of deformation of crystal grain increases along with the increase of deflection, increase along with the reduction of deformation temperature, therefore, the temperature of this stage rolling can not be the lowest, without special concern single pass heavy deformation, as long as ensureing that whole steel plate thickness direction all can be deformed.Therefore, the noncrystalline stage control rolling of the present invention starts temperature 830-900 DEG C, final temperature 805-850 DEG C；Accumulative deflection is not less than 65%.
Section cooling temperature range and rate of cooling: since it is desired that follow-up heat treatment, the beginning temperature of section cooling is the highest more good, but needs to make reasonable arrangement to mate rhythm of production；The finishing temperature of section cooling is too low, it is unfavorable for the control of plate shape, internal stress excessive subsequent heat treatment back plate shape is inevitable bad, if section cooling temperature is too high, the austenite not changed will be changed into pearlite or thick MA constituent element, and the homogenization of composition that this kind of rich carbon is unfavorable in follow-up heat treatment process mutually controls with microstructure homogenization.Heat at two-phase section, because structural transformation needs to realize the long-range diffusion of C and reallocation, if rich carbon is mutually too much or oversize, is necessarily required to extend heat time heating time or heating-up temperature, easily causes excessive grain thick, unfavorable to obdurability coupling.For rate of cooling, high cooling rate is conducive to crystal grain to refine, but also brings along high residual stress, is unfavorable for Strip Shape Control.It addition, steel plate is under high cooling rate, the structural homogenity on thickness direction is the most undesirable.Therefore, the section cooling that the present invention chooses starts temperature 785-835 DEG C, final temperature 450-550 DEG C, rate of cooling are 5-25 DEG C/s.
Tiny TMCP tissue is conducive to the Dispersed precipitate of cenotype during heat treatment, and parent grain is tiny, and the crystal grain of cenotype is also the least；Low steel plate residual stress and wall thickness direction even tissue are the most favourable with the control of plate shape to the stability contorting of plate property.
After TMCP state Plate Production of the present invention completes, carry out two-phase section quenching, it is characterized in that, the method comprises the following steps: heat steel in heat-treatment furnace to 685-795 DEG C, temperature retention time is { (1.1-2.0) t ± 5} minute, then use quenching unit shrend to room temperature, rate of cooling 16-45 DEG C/s.
The present invention is quenched by two-phase section, and steel plate is rolled state tissue, in two-phase section temperature range inside holding a period of time, changes into the two-phase structure that ferrite is constituted with austenite, by quenching subsequently, is transformed into the ferrite+hard phase constitution of room temperature state.Wherein ferrite includes polygonal ferrite, quasi-polygonal ferrite or their any mixture；Hard phase body is bainite, MA constituent element, martensite, or their any mixture.
After two-phase section has quenched, carrying out 150-450 DEG C of tempering, tempering process is selectable heat treatment step, can not use.During tempering, when temperature is 150-195 DEG C, tempering time is { (1.2-1.4) t ± 5} minute；When temperature is more than 195 DEG C and is less than 305 DEG C, tempering time is chosen as { (0.9-1.1) t ± 5} minute；When temperature is 305-450 DEG C, tempering time is { (0.6-0.8) t ± 5} minute.
The technological parameter that heat treatment stages is used, based on the insight that two-phase section heating, its statenchyma is polygonal ferrite+austenite, and along with the rising of temperature, austenite volume fraction increases；Along with the prolongation of temperature retention time, new phase volume fraction gradually increases, but not over the volume fraction of its poised state, if being now further added by temperature retention time, the Main change of cenotype shows as crystallite dimension and increases；Heating-up temperature selects between Ac1-Ac3, when the composition of steel determines, this temperature range also determines that.Improving heating-up temperature, extend temperature retention time, ferrite volume fraction will increase, and ferrite grain size also can be grown up simultaneously；Low temperature retention time, low holding temperature will necessarily reduce production cost, however, to ensure that ferritic amount of precipitation, certainly exist a lower limit.It addition, properly increasing holding temperature is also the selection reducing temperature retention time.Shrend process after having heated, high cooling rate can bring fine grain structure, but for steel plate, cooling rate is too high, and the structural homogenity in whole steel plate thickness direction is undesirable, it addition, the most tiny ferrite crystal grain, is also unfavorable for the raising of uniform elongation.Therefore, the two-phase section heating-up temperature of the present invention is 685-795 DEG C, and the time is { (1.0-2.0) ± 5} minute, shrend cooling rate 16-45 DEG C/s.
Temperature and temperature retention time: after two-phase section quenching, in order to eliminate steel plate internal stress and promote diffusion and the precipitation of the little atoms of solid solution state such as N, O, C, reduce the anchoring effect to dislocation in tubulation after heat coating procedure, reduction timeliness, to the adverse effect of performance after steel plate tubulation, can selectively carry out temper.Temperature is referred to the hot coating processes temperature after tubulation and selects, but in order to realize preferably being tempered effect, reduces temperature retention time, have positive effect equally while properly increasing temperature.Therefore, the present invention selects to be tempered at 150-450 DEG C, and when temperature is 150-195 DEG C, tempering time is { (1.2-1.4) t ± 5} minute；When temperature is 305-450 DEG C, tempering time is { (0.6-0.8) t ± 5} minute；When temperature is more than 195 DEG C and is less than 305 DEG C, tempering time is chosen as { (0.9-1.1) t ± 5} minute.
Heat treatment state large-deformation-resistance pipeline steel of the present invention, compared with existing TMCP state large-deformation-resistance pipeline steel, there is the advantages such as yield tensile ratio is lower, uniform elongation is higher, obdurability coupling is more preferable, steel plate is little with plate poor performance, thickness direction structural homogenity high, banding rank is low, it is adaptable to production based on stress design area Longitudinal SAW Pipe.
In the present invention, steel plate heats at two-phase section, and due to ferritic formation, around parent phase tissue can occur rich carbon, thus increases parent phase structure stability thus improve low-alloy steel quenching degree.The phases such as the ferritic phase after quenching and bainite, difference of hardness, intensity difference between the two are bigger, and the property of resisting large deformation (uniform elongation, yield tensile ratio and stress ratio) of steel plate is more excellent compared with the dual phase steel performance that TMCP technique produces.Because have employed two-phase section quenching, it is higher that quenching cools down relatively section cooling, and evenly, steel plate even tissue, performance is little with plate difference, banded structure rank is low for cooling effect.
The steel plate of any mixture of ferrite+bainite/martensite/MA constituent element of finally giving after heat treatment of the present invention or three is constituted soft or hard phase line and staff control, its horizontal mechanical performance can reach to require as follows: yield strength Rt0.5 is 485-630MPa, tensile strength Rm is 570-760MPa, yield tensile ratio Rt0.5/Rm≤0.73,-20 DEG C of impact absorbings can be more than 200J, and-20 DEG C of DWTT sections of shear SA are not less than 85%.The vertical mixing coefficient of steel plate can reach to require as follows: homogeneous deformation percentage elongation UEL > 16%, yield strength Rt0.5 is 400-550MPa, tensile strength Rm is 550-700MPa, yield tensile ratio Rt0.5/Rm≤0.70, stress-strain diagram without yield point elongation and Rt1.5/Rt0.5 not less than 1.19, Rt2.0/Rt1.0 not less than 1.08, Rt5.0/Rt1.0 not less than 1.12, wherein Rt1.0, Rt1.5, Rt2.0, Rt5.0 be total elongation be the stress value corresponding to 1.0%, 1.5%, 2.0%, 5.0%.
Detailed description of the invention
A kind of X70 large-deformation-resistance pipeline steel of the present invention, in this steel, the mass percent of chemical composition is C 0.04%-0.09%, Si 0.15%-0.55%, Mn 1.45%-1.75%, Nb 0.04%-0.10%, V 0.02%-0.08%, Ti 0.01%-0.03%, Cu 0%-0.20%, Ni 0.15-0.55%, Mo 0-0.15%, Cr 0.15%-0.45%, Al 0.025%-0.045%, N 0.0002%-0.011%, P≤0.015%, S≤0.005%, remaining be Fe and other be inevitable impurity element.
In the present invention, TMCP rolled Plate Production used by a kind of X70 large-deformation-resistance pipeline steel uses following process route: get the raw materials ready → converter or electric furnace smelting → external refining → casting → slab reheating → controlled rolling → control cools down.
Its TMCP technological temperature and cooling rate are controlled according to following parameter: slab heating temperature 1050-1250 DEG C；Recrystallization zone controlled rolling starts temperature 950-1150 DEG C, recrystallization zone controlled rolling final temperature 900-1100 DEG C；Noncrystalline domain controlled rolling starts temperature 830-900 DEG C, noncrystalline domain controlled rolling final temperature 805-850 DEG C；Section cooling begins to cool down temperature 785-835 DEG C, and section cooling terminates chilling temperature 450-550 DEG C, section cooling rate of cooling: 5-25 DEG C/s.
Its TMCP technique reduction in pass is controlled according to following parameter with accumulation drafts: recrystallization zone has rolled rear workpiece thickness (3.0-4.0) t；During recrystallization zone stage rolling, recrystallization zone total deformation 45%-65%；Single pass heavy deformation adjusts according to steel billet exit thickness, when steel billet exit thickness is more than or equal to 7.5t or when being less than 5.9t, and single pass heavy deformation 10%-14%；When steel billet exit thickness is less than 7.5t and is more than or equal to 5.9t, single pass heavy deformation 16%-24%；Non-recrystallization zone cumulative deformation is not less than 65%.
After above-mentioned TMCP state Plate Production completes, carry out two-phase section quenching, it is characterized in that, the method comprises the following steps: heat steel in heat-treatment furnace to 685-795 DEG C, temperature retention time is { (1.1-2.0) t ± 5} minute, then use quenching unit shrend to room temperature, rate of cooling 16-45 DEG C/s.
After two-phase section has quenched, carrying out 150-450 DEG C of tempering, tempering process is selectable heat treatment step, can not use.During tempering, when temperature is 150-195 DEG C, tempering time is { (1.2-1.4) t ± 5} minute；When temperature is 305-450 DEG C, tempering time is { (0.6-0.8) t ± 5} minute；When temperature is more than 195 DEG C and is less than 305 DEG C, tempering time is chosen as { (0.9-1.1) t ± 5} minute.
Below by one group of most preferred embodiment of the present invention, the present invention is elaborated:
The chemical composition of embodiment 1-20, technological parameter and results of property are as shown in tables 1 to 5.
Table 1 chemical composition (wt%)
Table 2 TMCP technological parameter
Table 3 rolls after-baking (two-phase section quenching+tempering) technological parameter
Note: in table " " represent do not carry out tempering heat treatment.
Table 4 horizontal mechanical performance result
Table 5 vertical mixing coefficient result
Claims (4)
1. an X70 large-deformation-resistance pipeline steel, it is characterised in that: chemical composition in this steel
Mass percent be C 0.04%-0.09%, Si 0.15%-0.55%, Mn 1.45%-1.75%,
Nb 0.04%-0.10%, V 0.02%-0.08%, Ti 0.01%-0.03%, Cu 0%-0.20%,
Ni 0.15-0.55%, Mo 0-0.15%, Cr 0.15%-0.45%, Al 0.025%-0.045%, N
0.0002%-0.011%, P≤0.015%, S≤0.005%, remaining is Fe and other is for can not
The impurity element avoided.
A kind of X70 large-deformation-resistance pipeline steel the most according to claim 1, its feature exists
In: described X70 large-deformation-resistance pipeline structure of steel is ferrite and hard phase bayesian by soft phase
Body, MA constituent element, martensite form, and the most ferritic volume fraction is 35%-65%；Ferrum
Ferritic average grain diameter is 3-11um.
3. the system of an a kind of X70 large-deformation-resistance pipeline steel as claimed in claim 1 or 2
Preparation Method, it is characterised in that described X70 large-deformation-resistance pipeline steel is that thickness targets is
26.4mm and above, steel plate thereof use 230-300mm thickness steel billet for rolling cut deal is reciprocating
The TMCP rolled steel plate produced is carried out on machine,
It produces and uses following process route: get the raw materials ready → converter or electric furnace smelting → external refining →
Casting → slab reheating → controlled rolling → control cooling；
Its TMCP technological temperature and cooling rate are controlled according to following parameter: heating of plate blank temperature
Spend 1050-1250 DEG C；Recrystallization zone controlled rolling starts temperature 950-1150 DEG C, recrystallization zone
Controlled rolling final temperature 900-1100 DEG C；Noncrystalline domain controlled rolling starts temperature 830-900
DEG C, noncrystalline domain controlled rolling final temperature 805-850 DEG C；Section cooling begins to cool down temperature
785-835 DEG C, section cooling termination chilling temperature 450-550 DEG C, section cooling, rate of cooling:
5-25℃/s；
Its TMCP technique reduction in pass is controlled according to following parameter with accumulation drafts:
Recrystallization zone has rolled rear workpiece thickness (3.0-4.0) t；During recrystallization zone stage rolling,
Recrystallization zone total deformation 45%-65%；Single pass heavy deformation adjusts according to steel billet exit thickness,
When steel billet exit thickness is more than or equal to 7.5t or when being less than 5.9t, single pass heavy deformation
10%-14%；When steel billet exit thickness is less than 7.5t and is more than or equal to 5.9t, single pass deforms
Amount 16%-24%；Non-recrystallization zone cumulative deformation is not less than 65%；
After above-mentioned TMCP state Plate Production completes, carry out two-phase section quenching, quenching include with
Lower step: heating steel is to 685-795 DEG C in heat-treatment furnace, and temperature retention time is { (1.1-2.0) t ± 5}
Minute, then use quenching unit shrend to room temperature, rate of cooling 16-45 DEG C/s；
In formula, t is finished steel plate thickness, unit mm.
The preparation method of a kind of X70 large-deformation-resistance pipeline steel the most as claimed in claim 3,
It is characterized in that, after having quenched, do not use tempering or carry out 150-450 DEG C of tempering；Adopt
When using tempering process, when temperature is 150-195 DEG C, tempering time is { (1.2-1.4) t ± 5}
Minute；When temperature is 305-450 DEG C, tempering time is { (0.6-0.8) t ± 5} minute；
When temperature is more than 195 DEG C and is less than 305 DEG C, tempering time is chosen as { (0.9-1.1) t ± 5}
Minute；
In formula, t is finished steel plate thickness, unit mm.
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