CN105088096A - X80 pipeline steel with high stress ratio and high arrest toughness and preparation method and application of X80 pipeline steel - Google Patents
X80 pipeline steel with high stress ratio and high arrest toughness and preparation method and application of X80 pipeline steel Download PDFInfo
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Abstract
The invention specifically relates to X80 pipeline steel with the high stress ratio and high arrest toughness and a preparation method and application of the X80 pipeline steel. The X80 pipeline steel is composed of, by weight, 0.03% to 0.08% of C, 0.15% to 0.35% of Si, 1.50% to 2.00% of Mn, not larger than 0.010% of P, not larger than 0.003% of S, 0.04% to 0.08% of Nb, 0.015% to 0.025% of Ti, 0.015% to 0.025% of Zr, not larger than 0.03% of Mo, not larger than 0.35% of Cu, not larger than 0.30% of Ni, not larger than 0.30% of Cr and the balance Fe and inevitable impurities. Zirconium is added to promote precipitation of proeutectoid ferrite, the banded structure level is reduced, and the stress ratio and the arrest toughness of a steel plate are effectively improved. The heating temperature is strictly controlled, and the recrystallization deformation temperature section in a rough rolling stage and the rolling reduction and the temperature of the last phase of rough rolling are reasonably matched, so that the austenite grain size is reduced to the maximum degree; and a rough-rolled intermediate billet is cooled, so that grain growth generated after recrystallization deformation is reduced.
Description
Technical field
The invention belongs to structural low alloy steel field, be specifically related to X80 pipe line steel of a kind of High stress ratio height arrest toughness and preparation method thereof and application.
Background technology
In recent years along with the continuous growth of energy demand, the pipeline of transfer oil Sweet natural gas mostly will through cold, that landform is unstable region.In this type of region, need to use the steel pipe with higher deformability and high arrest toughness.For achieving the above object, in the production process of X80M pipe line steel, the austenite grain refinement effect of steel plate recrystallization district rolling must be ensured, the low temperature large pressure rolling of Unhydrated cement and the accurate controlled cooling technique after rolling.Come production grain refining, steel plate containing polyphase structure with this, realize the feature of High stress ratio height arrest toughness.
A kind of resistance to deformation X80-100 Pipeline Steel Plate and manufacture method thereof is described in Chinese patent application CN102851587A disclosed on 01 02nd, 2013.This patent does not control effectively to rough rolling process passage texturing temperature, do not carry out intermediate blank cooling, do not carry out the multistage cooling of cooling stages, the therefore grain-size of refinement steel plate not yet in effect, unrealized acicular ferrite structure is that main polyphase structure controls, and realizes high arrest toughness.
Describe the large sstrain X80M dual phase sheet steel that the large soft reduction process of a kind of low temperature is produced in Chinese patent application CN103866204A disclosed on 06 18th, 2014, the specification of not mentioned steel plate, and only obtain ferrite and bainite duplex structure.
Describe a kind of method obtaining X80M grade of steel duplex structure large-strain pipeline steel in Chinese patent application CN103131833A disclosed on 06 05th, 2013, its processing parameter is that laboratory obtains, and produces bigger difference with industry spot.
X80M pipeline steel and the production method thereof of the distortion of a kind of Chinese People's Anti-Japanese Military and Political College is described in Chinese patent application CN103103449A disclosed on 05 15th, 2013, rough rolling step in its production technique does not control the lower limit of finishing temperature in texturing temperature, and intermediate blank is not lowered the temperature after terminating, can not effectively prevent growing up of grain-size.In addition, adopt two benches to cool after document finish rolling, the first stage temperature drop scope of cooling is less, and rate of cooling is higher, wayward during production.
A kind of method of producing X80M level large-deformation resistance pipe line steel plate of moderate thickness is described in Chinese patent mandate CN101456034B disclosed in 16 days February in 2011, the thickness specification of its steel plate is restricted, and only containing proeutectoid ferrite and bainite structure in the tissue of steel plate.
To sum up, all there is certain defect in existing method, needs to improve for above-mentioned defect.
Summary of the invention
The present invention, in order to solve the technical problem existed in prior art, provides X80M pipe line steel of a kind of High stress ratio height arrest toughness and preparation method thereof and application.
In order to solve above technical problem, technical scheme of the present invention is:
An X80 pipe line steel for High stress ratio height arrest toughness, is made up of the component of following weight part: C0.03 ~ 0.08%, Si0.15 ~ 0.35%, Mn1.50 ~ 2.00%, P≤0.010%, S≤0.003%, Nb0.04 ~ 0.08%, Ti0.015 ~ 0.025%, Zr0.015 ~ 0.025%, Mo≤0.03%, Cu≤0.35%, Ni≤0.30%, Cr≤0.30%, all the other are Fe and inevitable impurity.
Preferably, described X80 pipe line steel is made up of the component of following weight part: C0.03 ~ 0.06%, Si0.28 ~ 0.32%, Mn1.72 ~ 1.77%, P≤0.009%, S≤0.002%, Nb0.055 ~ 0.063%, Ti0.017 ~ 0.025%, Zr0.02 ~ 0.023%, Mo≤0.03%, Cu≤0.14%, Ni≤0.30%, Cr≤0.30%, all the other are Fe and inevitable impurity.
Preferably, the percentage composition of the component of described X80 pipe line steel meets following requirement:
Pcm＝C+Si/30+Ni/60+(Mn+Cr+Cu)/20+Mo/15+V/10+5B≤0.21％。
Preferably, the banded structure grading of described X80 pipe line steel is less than 3 grades.
A preparation method for the X80M pipe line steel of High stress ratio height arrest toughness, comprises the steps:
1) molten iron is prepared;
2) molten iron is carried out desulfurization, smelting, refining and sheet billet continuous casting process successively, the total amount of S, P, O, N, H in these three treating processess of desulfurization, smelting and refining in the hierarchy of control is less than 150ppm;
3) heating of plate blank, slab heating temperature is 1150 DEG C-1220 DEG C, and soaking zone soaking time is greater than 40min, and total heat-up time is not less than 270min;
4) slab de-scaling, after de-scaling, the surface temperature of slab is 1070-1120 DEG C;
5) slab rough rolling is obtained intermediate blank, after intermediate blank cooling, then finish rolling is carried out to intermediate blank; In rough rolling process, the rolling temperature of recrystallization zone is 1050-1100 DEG C, and the temperature of final pass is draft >=12% of 1050-1070 DEG C, final pass; Distortion is infiltrated into steel plate heart portion.
6) steel after finish rolling is cooled, before steel plate cooling, steel billet temperature is down to below transformation temperature Ar3 0-50 DEG C;
7) steel plate is cooled; Hot straightening is carried out to cooled steel, obtains required steel plate.Cooling step comprises first stage and subordinate phase, and the first stage adopts the water of 5bar steel plate to be cooled to 500-550 DEG C, rate of cooling 20-30 DEG C/s, and subordinate phase uses the water of 1.5-2bar steel plate to be cooled to 100-250 DEG C, rate of cooling 10-20 DEG C/s.The two benches cooling of cooling stages achieves the control containing the polyphase structure such as acicular ferrite and bainite in tissue.
Preferably, step 2) in, in described sheet billet continuous casting process, the thickness of the slab of production is 295-305mm, and center segregation of casting blank is less than C class 0.5; After sheet billet continuous casting, by continuously cast bloom slow cooling 45-55h.
Preferred further, in described sheet billet continuous casting process, the thickness of the slab of production is 300mm, after sheet billet continuous casting, by continuously cast bloom slow cooling 48h.
Preferably, step 4) in, in de-scaling process, the roller table speed of De-scaling box is 0.6-0.8m/s.Be the cooling in order to strengthen slab, ensure that the surface temperature range after the thick de-scaling of slab is 1070-1120 DEG C.
Preferred further, step 4) in, after de-scaling, the surface temperature of slab is 1090 DEG C.De-scaling under this condition, can ensure that the iron scale of surface of steel plate is eliminated on clean basis, makes the internal-external temperature difference of steel plate less, and can not cause edge waviness or the middle part arch camber of steel plate, the template of the steel plate obtained is better.
Preferably, step 5) in, when the thickness of described intermediate blank is 80-140mm, the accumulation draft of rough rolling step is 50-75%, realizes the at utmost refinement of austenite grain size.
Preferred further, step 5) in, the thickness of described intermediate blank is 120mm.
Preferred further, step 5) in, in rough rolling process, the rolling temperature of recrystallization zone is 1080 DEG C, and total deformation is 60%.Because texturing temperature is lower, after steel plate deformed, grain-size is grown up not too much.
Preferably, step 5) in, to the process of cooling of intermediate blank for utilizing high pressure water, the pressure range of high pressure water is 18-22MPa, and the temperature of intermediate blank is down to 930-960 DEG C.This high pressure water can be de-scaling high pressure water, lowers the temperature to intermediate blank with high pressure water, can reduce the grain growth after recrystallize distortion, and each high pressure water cooling need wait for that steel plate carries out after returning red end.
Preferred further, be utilize the high pressure water of 18-22MPa that the temperature of intermediate blank is down to 880 DEG C to the process of cooling of intermediate blank.Intermediate blank is cooled to this temperature, the grain growth after recrystallize distortion can be reduced better.
Preferably, step 5) in, in finishing stands, the start rolling temperature of non-recrystallization zone is 850-940 DEG C, and finishing temperature is 820-850 DEG C, rolling 8-16 passage, and accumulation draft is 75-80%.By controlling finish rolling stage rolling temperature and draft, improving the flattening degree of austenite crystal while distortion is penetrated into steel plate heart portion, increasing phase transformation nucleation site, thus the grain-size of steel plate after refinement phase transformation, improve the stability of steel plate.
Preferably, step 6) in, after finish rolling terminates, steel plate is carried out air cooling, make the temperature of steel plate lower than transformation temperature Ar320 DEG C.Air cooling step accurately controls out cold temperature, realizes the rational proportion of steel plate ferrite and bainite duplex structure.
Preferably, step 7) in, cooling step adopts MULPIC (multi-functional discontinuous cooling system).This device adopts water convexity and edge part shading cooling technology to ensure that the homogeneity of cooling, cools fast, effectively achieves large sstrain ability and high block hammer performance.
Preferably, step 7) in, the first stage is cooled to 530 DEG C, and speed of cooling is 25 DEG C/s, and subordinate phase is cooled to 230 DEG C, and speed of cooling is 15 DEG C/s.
The application of described X80M pipe line steel in extremely frigid zones transfer oil, Sweet natural gas.
The application of described X80M pipe line steel in regions with complex terrain transfer oil, Sweet natural gas.
In the present invention, the effect of each component is as follows:
Carbon: along with carbon content increases, the intensity of steel increases and toughness, welding property reduce.But due to reaching its maturity of cooling controlling and rolling controlling process and micro-alloying technology, simultaneously for improving the performance of welded heat affecting zone (HAZ), the carbon content in steel reduces gradually, and X80 steel-grade pipe line steel carbon content should below 0.08%.
Silicon: Si is reductor conventional in steel, and has very strong solution strengthening ability, can't cause the deterioration of plasticity and toughness in certain scope.
Manganese: being most common alloys element in steel, is conventional reductor and sweetening agent.Mn can significantly improve the hardening capacity of steel, also can improve the toughness of tissue, but will damage plasticity and toughness and welding property during content height when certain content.Mn has solution strengthening effect, also can reduce γ-α transformation temperature, and then fining ferrite grains.As interpolation 1.5% ~ 2.0%Mn, acicular ferrite structure can be obtained.Mn also can improve toughness, reduce ductile-brittle transition temperature.
Niobium: Nb can postpone austenite recrystallization, reduce transformation temperature, is obtained the performance of requirement by mechanism such as solution strengthening, phase transformation strengthening, precipitation strengths.The Nb be solid-solubilized in steel can suppress austenite recrystallization and grain growth, contribute to producing tiny ferrite crystal grain, and Nb element and C, atom N have extremely strong avidity, easy formation small and dispersed Nb (C, N), crystal boundary migration can be stoped, improve grain growth temperature, thus reach thinning effect.
Titanium: in austenite, can suppress growing up of austenite crystal by disperse, tiny TiN particle.Ti and N has very strong avidity, and in molten steel, Ti just defines TiN with N, does not substantially change intensity when the add-on of Ti is below 0.025%.Ti can improve the low-temperature flexibility of matrix metal and welded heat affecting zone simultaneously, the TiN formed can effective fixed nitrogen, when Al content is lower (being less than about 0.005%), Ti can form a kind of nitride, refinement heat affected zone microstructure, Ti content general control, below 0.025%, too much can cause the alligatoring of the nitride of Ti, unfavorable to low-temperature flexibility.
Zirconium: Zr is carbide in steel, and its effect in steel and niobium, tantalum, vanadium are similar.Add a small amount of zirconium have degassed, purification and Grain refinement, be conducive to the low-temperature performance of steel.The content of Zr is generally between 0.01%-0.03%.
Chromium: Cr can improve the hardening capacity of steel, reduces the transformation temperature of steel, can improve erosion resistance and anti-hydrogen induced cracking ability simultaneously, and can improve the abrasion resistance properties of steel.Add chromium cross separate out at most thick, to low-temperature flexibility and weldability unfavorable, general control is below 0.30%.
Nickel: Ni is complete solid solution element in steel, has the effect obviously reducing ductile-brittle transition temperature.Ni and Fe is present in α and γ phase with the form of dissolving each other, and by its adsorption fining ferrite grains in crystal grain, improves the impelling strength of steel.But Ni expands austenitic area element, reduces austenitic transition temperature, thus affects the velocity of diffusion of carbon and alloying element simultaneously, stop austenite to perlitic transformation, reduce the critical cooling velocity of steel, the hardening capacity of steel can be improved, easily make in steel, to occur bainite and martensite.Ni and Mn, Cr with the use of time can significantly improve hardening capacity.
Copper: Cu is dissolved in matrix will play solid solution strengthening effect, but too high levels will damage toughness and weldability.Cu also can improve the erosion resistance of steel.But easily there is the danger of embrittlement containing Cu steel when hot rolling, need appropriate Ni to eliminate its harm.
List above what these components of the present invention were concrete act on, except the effect that these are basic, these components, in the processes such as smelting, refining, continuous casting, rolling, obtain specific weave construction, can produce synergy between each component; As Cu and Ni in the present invention, the content of copper is larger, solid solution strengthening effect can be played, also the erosion resistance of steel can be improved, but too high levels will damage toughness and the weldability of steel, and nickel can eliminate its harm, and the impelling strength of steel can be improved, so the cooperation of copper and mickel can significantly improve erosion resistance and the toughness of steel.Zirconium can improve ferrite transformation temperature, promotes the formation of proeutectoid ferrite.Zirconium can reduce the spread coefficient of C and Mn in austenite, alleviates banded structure, is less than 3 grades provides useful effect for realizing banded structure.
In addition, due to the huge number of element, except conventional element, the element added in different patent is different, so, in numerous elements, select this several element of the present invention, and obtain the proportioning of this several element, the performance of the steel obtained is met the demands, select the process of an inherently great many of experiments, because also refer to, between different element, have synergy above, can not only carry out adding or reducing according to the character of element.
Preparation method of the present invention, as the selection of Heating temperature in preparation process, the selection of the parameter of finish rolling and rough rolling process, the selection of cooling step and speed of cooling all can affect weave construction and the structure properties of pipe line steel, the various parameter of preparation method and pipe line steel component need on the basis of lot of experiments, could finally determine by constantly adjusting, the internal organizational structure of pipe line steel, synergy between the effect of component and the component excellent low-temperature flexibility that jointly made pipe line steel possess and possess large sstrain performance, and the thickness of the steel plate prepared in production process is larger, the oil of cold zone can be met completely, the conveying task of Sweet natural gas etc.
So the component of pipe line steel of the present invention, the proportioning between component and the preparation method of pipe line steel are non-obvious.
Beneficial effect of the present invention is:
1, the present invention is by adding zirconium, promotes the precipitation of proeutectoid ferrite, reduces banded structure rank, effectively improves stress ratio and the arrest toughness of steel plate.
2, the present invention is by strictly controlling Heating temperature, and the recrystallize texturing temperature of rough rolling step is interval, the draught of last passage of roughing and the rational Match of temperature, farthest fining austenite grains size; By cooling the intermediate blank after roughing, decrease the grain growth after recrystallize distortion.
3, by controlling finish rolling stage rolling temperature and draft, improving the flattening degree of austenite crystal while distortion is penetrated into steel plate heart portion, increasing phase transformation nucleation site, thus the grain-size of steel plate after refinement phase transformation, improve the stability of steel plate.
4, before steel plate cooling, adopt air cooling relaxation accurately to control out cold temperature, realized in tissue containing proeutectoid ferrite by the two benches cooling of cooling stages; The formation of acicular ferrite is promoted by the first stage cooling in accelerating cooling stage; Realized the transformation completely of bainite by the subordinate phase in accelerating cooling stage, thus realize the control of polyphase structure.And controlled by the little cooling rate in accelerating cooling stage, realize the release of internal stress in steel plate, ensure that the straight of template.
5, produce the X80M pipe line steel of below 33mm, have the feature of High stress ratio, high arrest toughness, improve ability and the crack arrest ability that distortion resisted by steel pipe, banded structure is less than 3 grades, improves the security of pipeline.
Accompanying drawing explanation
Fig. 1 is process flow sheet of the present invention;
Fig. 2 is the thickness direction surface metallurgical structure figure of 33mm specification X80M steel plate of the present invention;
Fig. 3 is the metallurgical structure figure at thickness direction 1/4 place of 33mm specification X80M steel plate of the present invention;
Fig. 4 is the metallurgical structure figure at thickness direction 1/2 place of 33mm specification X80M steel plate of the present invention;
Fig. 5 is the thickness direction surface metallurgical structure figure of 27mm specification X80M steel plate of the present invention;
Fig. 6 is the metallurgical structure figure at thickness direction 1/4 place of 27mm specification X80M steel plate of the present invention;
Fig. 7 is the metallurgical structure figure at thickness direction 1/2 place of 27mm specification X80M steel plate of the present invention.
Fig. 8 is the thickness direction surface metallurgical structure figure of 18.4mm specification X80M steel plate of the present invention;
Fig. 9 is the metallurgical structure figure at thickness direction 1/4 place of 18.4mm specification X80M steel plate of the present invention;
Figure 10 is the metallurgical structure figure at thickness direction 1/2 place of 18.4mm specification X80M steel plate of the present invention.
Embodiment
Below in conjunction with the drawings and specific embodiments, the present invention is further described, so that those skilled in the art more understands the present invention, but does not limit the present invention with this.
Embodiment 1 the present embodiment is 33mmX80M, and its concrete composition is as shown in table 1.
The preparation method of the heterogeneous X80M Pipeline Steel Plate of the High stress ratio height arrest toughness of the present embodiment is as follows:
(1) smelting and continuous casting process: adopt Clean Steel to smelt mode, on the basis of ultralow P, S, control five large harmful element total amounts, namely these five kinds of element sums of control S, P, O, N, H are less than 150ppm, ensure purity, the homogeneity of steel.The main chemical compositions of steel is as shown in table 1: in sheet billet continuous casting process, and adopt dynamic soft reduction technology, center segregation of casting blank reaches C class 0.5, and slab thickness is 300mm.
Table 133mmX80M chemical composition
(2) heating of plate blank: in the heating process of slab, slab heating temperature 1190 DEG C.
(3) thick de-scaling: the board briquette controlling thick de-scaling step is 1105 DEG C.
(4) roughing: the temperature of recrystallization zone controlled rolling is 1080 DEG C, the lower limit 1060 DEG C that last passage is meeting deformation temperature range carries out, and ensures effective combination of draft >=15% and texturing temperature.After steel plate recrystallization rolling, grain-size is grown up not too much.Workpiece thickness 135mm, accumulative draft 55%;
(5) intermediate blank cooling: utilize roughing mill frame high pressure descaling water to cool intermediate blank, cooling termination temperature 940 DEG C.
(6) finish rolling: it is 860 DEG C that Unhydrated cement controls finish rolling start rolling temperature, finishing temperature 830 DEG C, rolling 14-16 passage.In this stage rolling, adopt large cumulative deformation, improve austenitic flattening degree, increase phase transformation nucleation site, thus after phase transformation, obtain the grain-size of refinement.Control 2-3 pass deformation rate is 15% simultaneously, improves distortion rate of permeation.Accumulation draft 75.6%.
(7) air cooling: after finish rolling terminates, carries out air cooling cooling to steel plate, is down to below Ar3 transformation temperature 20 DEG C.
(8) cool: adopt MULPIC to cool fast, first stage cooling final cooling temperature 540 DEG C, cooling rate 25 DEG C/s, subordinate phase final cooling temperature 220 DEG C, speed of cooling 15 DEG C/s.
(9) hot straightening: adopt large straightening force at utmost to discharge stress in steel plate.
Adopt the steel plate of above explained hereafter, final surface, 1/4,1/2 organize as shown in Figure 2, Figure 3 and Figure 4.The mechanical property of steel plate is as shown in table 7 and table 8.Stress ratio Rt1.5/Rt0.5=1.21; Rt2.0/Rt1.0=1.11 ,-15 DEG C of DWTT=85%.
Embodiment 2 the present embodiment is 27mmX80M, and its specific chemical composition is as shown in table 2.
The preparation method of the heterogeneous X80M Pipeline Steel Plate of the High stress ratio height arrest toughness of the present embodiment is as follows.
(1) smelting and continuous casting: adopt Clean Steel to smelt mode, on the basis of ultralow P, S, control five large harmful element total amounts, namely these five kinds of element sums of control S, P, O, N, H are less than 150ppm, ensure purity, the homogeneity of steel.In sheet billet continuous casting process, adopt dynamic soft reduction technology, slab quality reaches C class 0.5, and slab thickness is 300mm.
Table 227mmX80M chemical composition
(2) heat: in the heating process of slab, slab heating temperature 1200 DEG C.
(3) thick de-scaling: the board briquette controlling thick de-scaling step is 1095 DEG C.
(4) roughing: the temperature that recrystallization zone controls to start rolling is 1080 DEG C, ensures effective combination of draft >=12% and texturing temperature, and after distortion, grain-size is grown up not too much, and finishing temperature control is at 1055 DEG C.Workpiece thickness 110mm, accumulative draft 63%.
(5) intermediate blank cooling: utilize roughing mill frame high pressure descaling water to cool intermediate blank, cooling termination temperature 935 DEG C.
(6) finish rolling: the temperature range of Unhydrated cement controlled rolling is 880 DEG C, stops rolling temperature 835 DEG C, rolling 14-16 passage.In this stage rolling, adopt the cumulative deformation that the finish rolling stage is large, improve pass deformation rate, improve distortion rate of permeation, improve austenitic flattening degree, increase phase transformation nucleation site, the grain-size of steel plate after refinement phase transformation.Accumulation draft 75.5%.
(7) air cooling: after finish rolling terminates, carries out air cooling cooling to steel plate, is down to below Ar3 transformation temperature 20 DEG C.
(8) cool: adopt MULPIC to cool fast, first stage cooling final cooling temperature 510 DEG C, cooling rate 28 DEG C/s, subordinate phase final cooling temperature 230 DEG C, speed of cooling 18 DEG C/s.
(9) hot straightening: adopt large straightening force at utmost to discharge stress in steel plate.
By the final surface, 1/4 of the steel plate of above explained hereafter, the tissue of 1/2 is as shown in Fig. 5, Fig. 6 and Fig. 7.The mechanical property of steel plate is as shown in table 7 and table 8.Stress ratio Rt1.5/Rt0.5=1.20; Rt2.0/Rt1.0=1.10 ,-15 DEG C of DWTT=90%.
Embodiment 3 the present embodiment is 18.4mmX80M, and its specific chemical composition is as shown in table 3.
The preparation method of the heterogeneous X80M Pipeline Steel Plate of the High stress ratio height arrest toughness of the present embodiment is as follows.
(1) smelting and continuous casting: adopt Clean Steel to smelt mode, on the basis of ultralow P, S, control five large harmful element total amounts, namely these five kinds of element sums of control S, P, O, N, H are less than 150ppm, ensure purity, the homogeneity of steel.The main chemical compositions of steel is as shown in table 3: in sheet billet continuous casting process, and adopt dynamic soft reduction technology, slab quality reaches C class 0.5, and slab thickness is 300mm.
Table 318.4mmX80M chemical composition
(2) heat: in the heating process of slab, slab heating temperature 1200 DEG C.
(3) thick de-scaling: the board briquette controlling thick de-scaling step is 1100 DEG C.
(4) roughing: the temperature of recrystallization zone controlled rolling is 1085 DEG C, percentage pass reduction >=12%, after ensureing distortion, grain-size is grown up not too much.Workpiece thickness 80mm.Accumulative draft 73%;
(5) intermediate blank cooling: utilize roughing mill frame high pressure descaling water to cool intermediate blank, cooling termination temperature 950 DEG C.
(6) finish rolling: the temperature range of Unhydrated cement controlled rolling is 935 DEG C, stops rolling temperature 845 DEG C, rolling 8-12 passage.In this stage rolling, adopt the cumulative deformation that the finish rolling stage is large, improve austenitic flattening degree, increase phase transformation nucleation site, the grain-size of steel plate after refinement phase transformation.Accumulation draft 77%.
(7) air cooling: after finish rolling terminates, carries out air cooling to steel plate and is cooled to below Ar3 transformation temperature 15 DEG C.
(8) cool: adopt MULPIC to cool fast, first stage cooling final cooling temperature 515 DEG C, cooling rate 29 DEG C/s, subordinate phase final cooling temperature 235 DEG C, speed of cooling 18 DEG C/s.
(9) hot straightening: adopt large straightening force at utmost to discharge stress in steel plate.
By the final surface, 1/4 of the steel plate of above explained hereafter, 1/2 organize respectively as shown in Fig. 8, Fig. 9 and Figure 10.The mechanical property of steel plate is as shown in table 7 and table 8.Stress ratio Rt1.5/Rt0.5=1.19; Rt2.0/Rt1.0=1.12 ,-15 DEG C of DWTT=100%.
Embodiment 4 the present embodiment is 30.8mmX80M, and its specific chemical composition is as shown in table 4.
The preparation method of the heterogeneous X80M Pipeline Steel Plate of the High stress ratio height arrest toughness of the present embodiment is as follows.
Table 430.8mmX80M chemical composition
(1) smelting and continuous casting: adopt Clean Steel to smelt mode, on the basis of ultralow P, S, control five large harmful element total amounts, namely these five kinds of element sums of control S, P, O, N, H are less than 150ppm, ensure purity, the homogeneity of steel.The main chemical compositions of steel is as shown in table 4: in sheet billet continuous casting process, and adopt dynamic soft reduction technology, center segregation of casting blank reaches C class 1.0, and slab thickness is 300mm.
(2) heating of plate blank: in the heating process of slab, slab heating temperature 1200 DEG C.
(3) thick de-scaling: the board briquette controlling thick de-scaling step is 1100 DEG C.
(4) roughing: the temperature range of recrystallization zone controlled rolling is 1080 DEG C, carries out during last passage 1060 DEG C, ensures effective combination of draft >=15% and texturing temperature.After steel plate recrystallization rolling, grain-size is grown up not too much.Workpiece thickness 135mm, accumulative draft 60%.
(5) intermediate blank cooling: utilize roughing mill frame high pressure descaling water to cool intermediate blank, cooling termination temperature 870 DEG C.
(6) finish rolling: the temperature range of Unhydrated cement controlled rolling is 860 DEG C, stops rolling temperature 830 DEG C, rolling 12-16 passage.In this stage rolling, adopt the cumulative deformation that the finish rolling stage is large, improve austenitic flattening degree, increase phase transformation nucleation site, the grain-size of steel plate after refinement phase transformation.Control 2-3 pass deformation rate is 15% simultaneously, improves distortion rate of permeation.Accumulation draft 77.2%.
(7) air cooling: after finish rolling terminates, carries out air cooling to steel plate and is cooled to below Ar3 transformation temperature 20 DEG C.
(8) cool: adopt MULPIC to cool fast at refrigerating work procedure, first stage cooling final cooling temperature 535 DEG C, cooling rate 24 DEG C/s, subordinate phase final cooling temperature 240 DEG C, speed of cooling 16 DEG C/s.
(9) hot straightening: adopt large straightening force at utmost to discharge stress in steel plate.
Adopt the steel plate of above explained hereafter, the mechanical property of steel plate is as shown in table 7,8.Stress ratio Rt1.5/Rt0.5=1.20; Rt2.0/Rt1.0 >=1.11 ,-15 DEG C of DWTT >=87%.
Embodiment 5 the present embodiment is 22mmX80M, and its specific chemical composition is as shown in table 5.
The preparation method of the heterogeneous X80M Pipeline Steel Plate of the High stress ratio height arrest toughness of the present embodiment is as follows.
(1) smelting and continuous casting: adopt Clean Steel to smelt mode, on the basis of ultralow P, S, control five large harmful element total amounts, namely these five kinds of element sums of control S, P, O, N, H are less than 150ppm, ensure purity, the homogeneity of steel.The primary chemical of steel is as shown in table 5: in sheet billet continuous casting process, and adopt dynamic soft reduction technology, center segregation of casting blank reaches C class 1.0, and slab thickness is 300mm.
Table 522mmX80M chemical composition
(2) heating of plate blank: in the heating process of slab, slab heating temperature 1200 DEG C.
(3) thick de-scaling: the board briquette controlling thick de-scaling step is 1100 DEG C.
(4) roughing: the temperature range of recrystallization zone controlled rolling is 1090 DEG C, and last passage is carried out at 1055 DEG C, ensures effective combination of draft >=15% and texturing temperature.After steel plate recrystallization rolling, grain-size is grown up not too much.Workpiece thickness 95mm, accumulative draft 68%;
(5) intermediate blank cooling: utilize roughing mill frame high pressure descaling water to cool intermediate blank, cooling termination temperature 945 DEG C.
(6) finish rolling: the temperature range of Unhydrated cement controlled rolling is 905 DEG C, stops rolling temperature 845 DEG C, rolling 12-16 passage.In this stage rolling, adopt the cumulative deformation that the finish rolling stage is large, improve austenitic flattening degree, increase phase transformation nucleation site, the grain-size of steel plate after refinement phase transformation.Control 2-3 pass deformation rate is 15% simultaneously, improves distortion rate of permeation.Accumulation draft 76.8%.
(7) air cooling: after finish rolling terminates, carries out air cooling to steel plate and is cooled to below Ar3 transformation temperature 20 DEG C.
(8) cool: adopt MULPIC to cool fast at refrigerating work procedure, first stage cooling final cooling temperature 505 DEG C, cooling rate 27 DEG C/s, subordinate phase final cooling temperature 230 DEG C, speed of cooling 19 DEG C/s.
(9) hot straightening: adopt large straightening force at utmost to discharge stress in steel plate.
Adopt the steel plate of above explained hereafter, the mechanical property of steel plate is as shown in table 7,8.Stress ratio Rt1.5/Rt0.5=1.19; Rt2.0/Rt1.0=1.12 ,-15 DEG C of DWTT=87%.
The horizontal salient features detection statistics table of each embodiment of table 7
Longitudinal salient features detection statistics table of each embodiment of table 8
Embodiment 6
The present embodiment is that the concrete composition of 33mmX80M is as shown in table 8.
The pipe line steel of the present embodiment is except in component, the content of zirconium is had any different, and the content of other component and preparation method, Selecting parameter are all just the same with embodiment 1
Table 833mmX80M chemical composition (%)
Adopt the mechanical property of the steel plate of above explained hereafter as shown in Table 9 and Table 10.
Embodiment 7
The present embodiment is that the concrete composition of 33mmX80M is as shown in table 9.
The pipe line steel of the present embodiment is except in component, the content of zirconium is had any different, and the content of other component and preparation method, Selecting parameter are all just the same with embodiment 1
Table 933mmX80M chemical composition (%)
Adopt the mechanical property of the steel plate of above explained hereafter as shown in Table 10 and Table 11.
The horizontal salient features detection statistics table of each embodiment of table 10
Longitudinal salient features detection statistics table of each embodiment of table 11
From table 10 and table 11, the low-temperature flexibility of the pipe line steel that embodiment 6,7 is obtained, stress ratio and uniform elongation are compared with the example poor performance within the scope of application claims, and visible zirconium can have larger contribution to improving the low-temperature flexibility of pipe line steel, stress ratio and uniform elongation simultaneously.
By reference to the accompanying drawings the specific embodiment of the present invention is described although above-mentioned; but the restriction not to invention protection domain; one of ordinary skill in the art should be understood that; on the basis of technical scheme of the present invention, those skilled in the art do not need to pay various amendment or distortion that creative work can make still in protection scope of the present invention.
Claims (10)
1. an X80 pipe line steel for High stress ratio height arrest toughness, is characterized in that: be made up of the component of following weight part: C0.03 ~ 0.08%, Si0.15 ~ 0.35%, Mn1.50 ~ 2.00%, P≤0.010%, S≤0.003%, Nb0.04 ~ 0.08%, Ti0.015 ~ 0.025%, Zr0.015 ~ 0.025%, Mo≤0.03%, Cu≤0.35%, Ni≤0.30%, Cr≤0.30%, all the other are Fe and inevitable impurity.
2. X80 pipe line steel according to claim 1, is characterized in that: be made up of the component of following weight part: C0.03 ~ 0.06%, Si0.28 ~ 0.32%, Mn1.72 ~ 1.77%, P≤0.009%, S≤0.002%, Nb0.055 ~ 0.063%, Ti0.017 ~ 0.025%, Zr0.02 ~ 0.023%, Mo≤0.03%, Cu≤0.14%, Ni≤0.30%, Cr≤0.30%, all the other are Fe and inevitable impurity.
3. the preparation method of the X80M pipe line steel of the High stress ratio height arrest toughness described in claim 1 or 2, is characterized in that: comprise the steps:
1) molten iron is prepared;
2) molten iron is carried out desulfurization, smelting, refining and sheet billet continuous casting process successively, the total amount of S, P, O, N, H in these three treating processess of desulfurization, smelting and refining in the hierarchy of control is less than 150ppm;
3) heating of plate blank, slab heating temperature is 1150 DEG C-1220 DEG C, and soaking zone soaking time is greater than 40min, and total heat-up time is not less than 270min;
4) slab de-scaling, after de-scaling, the surface temperature of slab is 1070-1120 DEG C;
5) slab rough rolling is obtained intermediate blank, after intermediate blank cooling, then finish rolling is carried out to intermediate blank; In rough rolling process, the rolling temperature of recrystallization zone is 1050-1100 DEG C, and the temperature of final pass is draft >=12% of 1050-1070 DEG C, final pass; Distortion is infiltrated into steel plate heart portion;
6) steel after finish rolling is cooled, before steel plate cooling, steel billet temperature is down to below transformation temperature Ar3 0-50 DEG C;
7) steel plate is cooled; Hot straightening is carried out to cooled steel, obtains required steel plate.Cooling step comprises first stage and subordinate phase, and the first stage adopts the water of 5bar steel plate to be cooled to 500-550 DEG C, rate of cooling 20-30 DEG C/s, and subordinate phase uses the water of 1.5-2bar steel plate to be cooled to 100-250 DEG C, rate of cooling 10-20 DEG C/s.
4. preparation method according to claim 3, is characterized in that: step 5) in, when the thickness of described intermediate blank is 80-140mm, the accumulation draft of rough rolling step is 50-70%.
5. preparation method according to claim 3, is characterized in that: step 5) in, be utilize the high pressure water of 18-22MPa that the temperature of intermediate blank is down to 850-960 DEG C to the process of cooling of intermediate blank.
6. preparation method according to claim 3, is characterized in that: step 5) in, in finishing stands, the start rolling temperature of non-recrystallization zone is 850-940 DEG C, and finishing temperature is 820-850 DEG C, rolling 8-16 passage, and accumulation draft is 75-80%.
7. preparation method according to claim 3, is characterized in that: step 6) in, after finish rolling terminates, steel plate is carried out air cooling, make the temperature of steel plate lower than transformation temperature Ar320 DEG C.
8. preparation method according to claim 3, is characterized in that: step 7) in, the first stage is cooled to 530 DEG C, and speed of cooling is 25 DEG C/s, and subordinate phase is cooled to 230 DEG C, and speed of cooling is 15 DEG C/s.
9. the arbitrary described application of X80M pipe line steel in extremely frigid zones transfer oil, Sweet natural gas of claim 1-2.
10. the arbitrary described application of X80M pipe line steel in regions with complex terrain transfer oil, Sweet natural gas of claim 1-2.
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