CN105088096B - 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 low-alloy structural steel field, and in particular to a kind of X80 pipe line steels of the high arrest toughness of High stress ratio
And preparation method and application.
Background technology
Recently as the continuous growth of energy demand, the pipeline of transfer oil natural gas mostly will be through cold, landform
Unstable region.In such region, need using the steel pipe with higher deformability and high arrest toughness.On reaching
Purpose is stated, in the production process of X80M pipe line steels, it is necessary to assure the austenite grain refinement effect of steel plate recrystallization area rolling,
The big accurate controlled cooling technique depressed after rolling and rolling of low temperature of Unhydrated cement.Crystal grain refinement is produced with this, containing many
The steel plate of phase constitution, realizes the feature of the high arrest toughness of High stress ratio.
A kind of resistance to deformation X80-100 has been recorded in Chinese patent application CN102851587A disclosed in 02 day within 01 month 2013
Pipeline Steel Plate and its manufacture method.The patent does not control effectively to rough rolling process passage deformation temperature, does not carry out middle base
Cooling, does not carry out the multistage cooling of cooling stage, therefore the crystallite dimension of refinement steel plate not yet in effect, and acicular ferrite is not implemented
Heterogeneous structure control based on tissue, realizes high arrest toughness.
A kind of big pressure work of low temperature is recorded in Chinese patent application CN103866204A disclosed in 18 days within 06 month 2014
The big strain X80M dual phase sheet steels of skill production, do not refer to the specification of steel plate, and only obtain ferrite and bainite duplex structure.
A kind of acquisition X80M grade of steels are recorded in Chinese patent application CN103131833A disclosed in 05 day within 06 month 2013
The method of duplex structure's large-strain pipeline steel, its technological parameter is laboratory acquisition, has bigger difference with industry spot production.
A kind of anti-large deformation has been recorded in Chinese patent application CN103103449A disclosed in 15 days within 05 month 2013
X80M pipeline steels and its production method, the rough rolling step in its production technology does not control finishing temperature under deformation temperature
Limit, and middle base is not lowered the temperature after terminating, it is impossible to effectively prevent growing up for crystallite dimension.In addition, adopting after document finish rolling
Cooled down with two benches, the first stage temperature drop scope of cooling is less, and cooldown rate is higher, wayward during production.
Illustrate that a kind of production X80M levels are anti-big in 2 months 2011 CN101456034B of Chinese patent mandate disclosed in 16 days
The method of deformation pipeline steel medium plate, the thickness specification of its steel plate is restricted, and only contains pro-eutectoid ferrum in the tissue of steel plate
Ferritic and bainite structure.
From the point of view of to sum up, there is certain defect in existing method, need to be improved for above-mentioned defect.
The content of the invention
The present invention is in order to solve technical problem present in prior art, there is provided a kind of high arrest toughness of High stress ratio
X80M pipe line steels and preparation method and application.
In order to solve above technical problem, the technical scheme is that：
A kind of X80 pipe line steels of the high arrest toughness of High stress ratio, are made up of the component of following weight portion：C 0.03～
0.08%, Si 0.15～0.35%, Mn 1.50～2.00%, P≤0.010%, S≤0.003%, Nb 0.04～0.08%,
Ti 0.015～0.025%, Zr 0.015～0.025%, Mo≤0.03%, Cu≤0.35%, Ni≤0.30%, Cr≤
0.30%, remaining is Fe and inevitable impurity.
Preferably, the X80 pipe line steels are made up of the component of following weight portion：C 0.03～0.06%, Si 0.28～
0.32%, Mn 1.72～1.77%, P≤0.009%, S≤0.002%, Nb 0.055～0.063%, Ti 0.017～
0.025%, Zr 0.02～0.023%, Mo≤0.03%, Cu≤0.14%, Ni≤0.30%, Cr≤0.30%, remaining is Fe
With inevitable impurity.
Preferably, the percentage composition of the component of the X80 pipe line steels meets claimed below：
Pcm=C+Si/30+Ni/60+ (Mn+Cr+Cu)/20+Mo/15+V/10+5B≤0.21%.
Preferably, the banded structure grading of the X80 pipe line steels is less than 3 grades.
A kind of preparation method of the X80M pipe line steels of the high arrest toughness of High stress ratio, comprises the steps：
1) molten iron is prepared；
2) molten iron is carried out successively desulfurization, smelting, refine and sheet billet continuous casting to process, desulfurization, smelting and refine these three
The total amount of S, P, O, N, H in processing procedure in control system is less than 150ppm；
3) heating of plate blank, slab heating temperature is 1150 DEG C -1220 DEG C, and soaking zone temperature retention time is more than 40min, total heating
Time is not less than 270min；
4) slab de-scaling, the surface temperature of slab is 1070-1120 DEG C after de-scaling；
5) slab rough rolling is obtained into middle base, after cooling down to middle base, then finish rolling is carried out to middle base；In rough rolling process,
The rolling temperature of recrystallization zone is 1050-1100 DEG C, and the temperature of final pass is 1050-1070 DEG C, the reduction ratio of final pass
>=12%；Deformation is infiltrated into into steel plate center portion.
6) steel after finish rolling is cooled down, steel billet temperature is down to 0-50 DEG C below transformation temperature Ar3 before steel plate cooling；
7) steel plate is cooled down；Thermal straightening is carried out to the steel after cooling, required steel plate is obtained.Cooling step includes first
Steel plate is cooled to 500-550 DEG C by stage and second stage, the first stage using the water of 5bar, cooldown rate 20-30 DEG C/s, and
Steel plate is cooled to 100-250 DEG C by the two-stage using the water of 1.5-2bar, cooldown rate 10-20 DEG C/s.Two ranks of cooling stage
Section cooling is realized in tissue containing the control of the heterogeneous structure such as acicular ferrite and bainite.
Preferably, step 2) in, during the sheet billet continuous casting, the thickness of the slab of production is 295-305mm, in strand
Heart segregation is less than C classes 0.5；After sheet billet continuous casting, by continuous casting billet slow cooling 45-55h.
It is further preferred that during the sheet billet continuous casting, the thickness of the slab of production is 300mm, and after sheet billet continuous casting, will
Continuous casting billet slow cooling 48h.
Preferably, step 4) in, during de-scaling, the roller table speed of De-scaling box is 0.6-0.8m/s.It is right in order to increase
The cooling of slab, it is ensured that the surface temperature range after the thick de-scaling of slab is 1070-1120 DEG C.
It is further preferred that step 4) in, after de-scaling, the surface temperature of slab is 1090 DEG C.De-scaling under this condition,
On the basis of can ensure that the iron scale of surface of steel plate is cleaned, make the internal-external temperature difference of steel plate less, do not result in steel
The edge waviness of plate or middle part arch camber, the template of the steel plate for obtaining is preferable.
Preferably, step 5) in, when the thickness of the middle base is 80-140mm, the accumulation reduction ratio of rough rolling step is
50-75%, realizes the at utmost refinement of austenite grain size.
It is further preferred that step 5) in, the thickness of the middle base is 120mm.
It is further preferred that step 5) in, in rough rolling process, the rolling temperature of recrystallization zone is 1080 DEG C, total deformation
For 60%.Because deformation temperature is relatively low, crystallite dimension is grown up not too much after steel plate deformed.
Preferably, step 5) in, it is to utilize water under high pressure to the cooling procedure of middle base, the pressure limit of water under high pressure is 18-
22MPa, by the temperature of middle base 930-960 DEG C is down to.The water under high pressure can be de-scaling water under high pressure, and middle base is entered with water under high pressure
Row cooling, it is possible to reduce the crystal grain after recrystallization deformation is grown up, the cooling of each water under high pressure needs to wait for steel plate to be returned and carried out after red end.
It is further preferred that being to be dropped the temperature of middle base using the water under high pressure of 18-22MPa to the cooling procedure of middle base
To 880 DEG C.Middle base is cooled to into the temperature, the crystal grain after recrystallization deformation can be preferably reduced and be grown up.
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, 8-16 passages are rolled, accumulation reduction ratio is 75-80%.By controlling finish rolling stage rolling temperature and reduction ratio,
The flattening degree of austenite crystal is improved while deformation is penetrated into into steel plate center portion, increases phase transformation nucleation site, so as to refine
The crystallite dimension of steel plate after phase transformation, improves the stability of steel plate.
Preferably, step 6) in, after finish rolling terminates, steel plate being carried out into air cooling, the temperature for making steel plate is less than transformation temperature Ar320
℃.Air cooling step precise control opens 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).The device adopts water
Convexity and edge part shading cooling technology ensure that the uniformity of cooling, quick cooling, effectively realize big adaptability to changes and height
Block hammer performance.
Preferably, step 7) in, the first stage is cooled to 530 DEG C, and rate of cooling is 25 DEG C/s, and second stage is cooled to
230 DEG C, rate of cooling is 15 DEG C/s.
Application of the X80M pipe line steels in extremely frigid zones transfer oil, natural gas.
Application of the X80M pipe line steels in regions with complex terrain transfer oil, natural gas.
The effect of each component is as follows in the present invention：
Carbon：As carbon content increases, the intensity of steel increases and toughness, welding performance reduction.But due to cooling controlling and rolling controlling process
With reaching its maturity for micro-alloying technology, while being the performance for improving welding heat affected zone (HAZ), the carbon content in steel gradually drops
Low, X80 steel-grade pipe line steel carbon content should be below 0.08%.
Silicon：Si is the deoxidizer commonly used in steel, and with very strong solution strengthening ability, can't in certain scope
Cause the deterioration of plasticity and toughness.
Manganese：It is most common alloying element in steel, is conventional deoxidizer and desulfurizing agent.Mn can significantly improve the through hardening of steel
Property, in certain content and the toughness of tissue can be improved, but content will infringement plasticity and toughness and welding performance when high.Mn has solid solution
Invigoration effect, can also reduce γ-α phase transition temperatures, and then fining ferrite grains.When 1.5%～2.0%Mn is added, can obtain
Obtain acicular ferrite structure.Mn can also improve toughness, reduce ductile-brittle transition temperature.
Niobium：Nb can postpone austenite recrystallization, phase transition temperature be reduced, by solution strengthening, phase transformation strengthening, precipitation strength etc.
Mechanism is obtaining the performance of requirement.The Nb being solid-solubilized in steel can suppress austenite recrystallization and crystal grain to grow up, and help to create
Tiny ferrite crystal grain, and Nb elements have extremely strong affinity with C, N atom, easily form small and dispersed Nb (C, N), can
To prevent crystal boundary migration, improve crystal grain and grow up temperature, so as to reach thinning effect.
Titanium：In austenite, growing up for austenite crystal can be suppressed by disperse, tiny TiN granules.Ti has with N
Very strong affinity, Ti just defines TiN with N in molten steel, does not change strong when the addition of Ti is below 0.025% substantially
Degree.Ti can simultaneously improve the low-temperature flexibility of parent metal and welding heat affected zone, the TiN of formation can effective fixed nitrogen, work as Al
(it is less than about 0.005%) when content is relatively low, Ti can form a kind of nitride, refines heat affected area microscopic structure, Ti contents one
As control below 0.025%, can excessively cause the roughening of the nitride of Ti, it is unfavorable to low-temperature flexibility.
Zirconium：Zr is carbide in steel, and its effect in steel is similar to niobium, tantalum, vanadium.Add a small amount of zirconium
There are degassing, purification and Grain refinement, be conducive to the cryogenic property of steel.The content of Zr is typically between 0.01%-0.03%.
Chromium：Cr can improve the quenching degree of steel, the transformation temperature of steel be reduced, while corrosion resistance and anti-hydrogen induced cracking energy can be improved
Power, and the abrasion resistance properties of steel can be improved.Add chromium to cross and at most separate out thick, it is unfavorable to low-temperature flexibility and weldability, typically
Control is below 0.30%.
Nickel：Ni is complete solid solution element in steel, with the effect for substantially reducing ductile-brittle transition temperature.Ni and Fe is dissolving each other
Form is present in α and γ phases, the adsorption fining ferrite grains by it in crystal grain, improves the impact flexibility of steel.
But while Ni is to expand austenitic area element, the transition temperature of austenite is reduced, so as to affect the diffusion of carbon and alloying element
Speed, prevents austenite to perlitic transformation, reduces the critical cooling rate of steel, can improve the quenching degree of steel, easily makes in steel
There is bainite and martensite.Ni and Mn, Cr can significantly improve quenching degree when using cooperatively.
Copper：Cu is dissolved in matrix will play solid solution strengthening effect, but too high levels would detract from toughness and weldability.Cu also can
Improve the corrosion resistance of steel.But steel containing Cu easily occurs the danger of embrittlement in hot rolling, need appropriate Ni to eliminate its harm.
These components of the present invention are specifically acted on and listed above, in addition to these basic effects, these
Component obtains specific organizational structure during smelting, refine, continuous casting, rolling etc., and collaboration can be produced between each component
Effect；As Cu and Ni in the present invention, the content of copper are larger, solid solution strengthening effect can be played, it is also possible to improve the corrosion resistant of steel
Corrosion, but too high levels would detract from the toughness and weldability of steel, and nickel can eliminate its harm, and rushing for steel can be improved
Toughness is hit, so the cooperation of copper and mickel can significantly improve the corrosion resistance and toughness of steel.Zirconium can improve ferritic transformation temperature
Degree, promotes the formation of pro-eutectoid ferrite.Zirconium can reduce the diffusion coefficient of C and Mn in austenite, alleviate banded structure,
To realize that banded structure provides beneficial effect less than 3 grades.
Further, since the huge number of element, except conventional element, the element added in different patents is different, so,
This several element of the present invention are selected in numerous elements, and obtains the proportioning of this several element so that the performance of obtained steel
Meet and require, select the process of an inherently many experiments, because also refer to above, collaboration is had between different elements and is made
With, it is impossible to only it is added or reduces according to the property of element.
The preparation method of the present invention, the choosing of the parameter of the selection, finish rolling and rough rolling process of heating-up temperature such as in preparation process
Select, the selection of cooling step and rate of cooling can all affect the organizational structure and structural behaviour of pipe line steel, preparation method it is various
Parameter and pipeline steel constituent are needed on the basis of lot of experiments, could finally be determined by constantly adjustment, pipe line steel it is interior
Synergism between portion's organizational structure, the effect of component and component makes pipe line steel possess excellent low-temperature flexibility and tool jointly
Standby big strain property, and the thickness of the steel plate prepared in production process is larger, can meet completely the oil of cold zone, natural
The conveying task of gas etc..
So, the component of the pipe line steel of the present invention, the preparation method of proportioning and pipe line steel between component is all non-aobvious
And be clear to.
Beneficial effects of the present invention are：
1st, the present invention promotes the precipitation of pro-eutectoid ferrite by adding zirconium, reduces banded structure rank, effectively improves
The stress ratio and arrest toughness of steel plate.
2nd, the present invention is by strict control heating-up temperature, the recrystallization deformation temperature of rough rolling step is interval, roughing last
The drafts of passage and the Proper Match of temperature, farthest fining austenite grains size；Centre after to roughing
Base is cooled down, and is reduced the crystal grain after recrystallization deformation and is grown up.
3rd, by controlling finish rolling stage rolling temperature and reduction ratio, while deformation is penetrated into into steel plate center portion Ovshinsky is improved
The flattening degree of body crystal grain, increases phase transformation nucleation site, so as to refine phase transformation after steel plate crystallite dimension, improve the property of steel plate
Stabilizability.
4th, before steel plate cooling, cold temperature is opened using air cooling relaxation precise control, is cooled down by the two benches of cooling stage
Realize containing pro-eutectoid ferrite in tissue；Promote the shape of acicular ferrite by accelerating the first stage cooling of cooling stage
Into；The transformation completely of bainite is realized by accelerating the second stage of cooling stage, so as to realize the control of heterogeneous structure.And lead to
Cross accelerate cooling stage little cooling rate control, realize the release of internal stress in steel plate, it is ensured that template it is straight.
5th, the X80M pipe line steels of below 33mm are produced, the characteristics of with High stress ratio, high arrest toughness, steel pipe is improve
The ability and crack arrest ability of deformation are resisted, banded structure is less than 3 grades, improves the safety of pipeline.
Description of the drawings
Fig. 1 is the process chart of the present invention；
Fig. 2 is the thickness direction surface metallurgical structure figure of the 33mm specification X80M steel plates of the present invention；
Fig. 3 is the metallurgical structure figure at the thickness direction 1/4 of the 33mm specification X80M steel plates of the present invention；
Fig. 4 is the metallurgical structure figure at the thickness direction 1/2 of the 33mm specification X80M steel plates of the present invention；
Fig. 5 is the thickness direction surface metallurgical structure figure of the 27mm specification X80M steel plates of the present invention；
Fig. 6 is the metallurgical structure figure at the thickness direction 1/4 of the 27mm specification X80M steel plates of the present invention；
Fig. 7 is the metallurgical structure figure at the thickness direction 1/2 of the 27mm specification X80M steel plates of the present invention.
Fig. 8 is the thickness direction surface metallurgical structure figure of the 18.4mm specification X80M steel plates of the present invention；
Fig. 9 is the metallurgical structure figure at the thickness direction 1/4 of the 18.4mm specification X80M steel plates of the present invention；
Figure 10 is the metallurgical structure figure at the thickness direction 1/2 of the 18.4mm specification X80M steel plates of the present invention.
Specific embodiment
Come with reference to the accompanying drawings and detailed description to be further described the present invention, so as to the technology of this area
Personnel know more about the present invention, but with this do not limit the present invention.
The present embodiment of embodiment 1 is 33mmX80M, and its concrete composition is as shown in table 1.
The preparation method of the multiphase X80M Pipeline Steel Plate of the high arrest toughness of High stress ratio of the present embodiment is as follows：
(1) smelt and continuous casting process：Using clean steel smelting mode, on the basis of ultralow P, S, the big harmful unit of control five
Plain total amount, that is, control this five kinds of element sums of S, P, O, N, H less than 150ppm, it is ensured that the degree of purity of steel, uniformity.The master of steel
Want chemical composition as shown in table 1：During sheet billet continuous casting, using dynamic soft reduction technology, center segregation of casting blank reaches C classes 0.5,
Slab thickness is 300mm.
The 33mm X80M chemical compositions of table 1
(2) heating of plate blank：In the heating process of slab, 1190 DEG C of slab heating temperature.
(3) thick de-scaling：The board briquette for controlling thick de-scaling step is 1105 DEG C.
(4) roughing：The temperature of recrystallization zone controlled rolling is 1080 DEG C, and last a time is meeting deformation temperature range
1060 DEG C of lower limit is carried out, it is ensured that effective combination of reduction ratio >=15% and deformation temperature.Crystallite dimension after steel plate recrystallization rolling
Grow up not too much.Workpiece thickness 135mm, adds up reduction ratio 55%；
(5) base cooling in the middle of：Middle base is cooled down using roughing mill frame high pressure descaling water, cooling termination temperature
940℃。
(6) finish rolling：Unhydrated cement controls finish rolling start rolling temperature for 860 DEG C, and 830 DEG C of finishing temperature rolls 14-16 roads
It is secondary.In this stage rolling, using big cumulative deformation, the flattening degree of austenite is improved, increase phase transformation nucleation site, so as to
The crystallite dimension for refining is obtained after phase transformation.2-3 pass deformation rates are controlled simultaneously 15%, improve deformation permeability.Accumulation pressure
Rate 75.6%.
(7) air cooling：After finish rolling terminates, air cooling cooling is carried out to steel plate, be down to 20 DEG C below Ar3 transformation temperatures.
(8) cool down：Quickly cooled down using MULPIC, 540 DEG C of final cooling temperature of first stage cooling, 25 DEG C/s of cooling rate, second
220 DEG C of stage final cooling temperature, 15 DEG C/s of rate of cooling.
(9) thermal straightening：The stress in steel plate is at utmost discharged using big straightening force.
The steel plate produced using process above, final surface, 1/4,1/2 tissue are as shown in Figure 2, Figure 3 and Figure 4.Steel
The mechanical property of 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
DWTT=85%.
The present embodiment of embodiment 2 is 27mmX80M, and its specific chemical composition is as shown in table 2.
The preparation method of the multiphase X80M Pipeline Steel Plate of the high arrest toughness of High stress ratio of the present embodiment is as follows.
(1) smelt and continuous casting：Using clean steel smelting mode, on the basis of ultralow P, S, five big harmful elements of control are total
Amount, that is, control this five kinds of element sums of S, P, O, N, H less than 150ppm, it is ensured that the degree of purity of steel, uniformity.Sheet billet continuous casting mistake
Cheng Zhong, using dynamic soft reduction technology, slab quality reaches C classes 0.5, and slab thickness is 300mm.
The 27mm X80M chemical compositions of table 2
(2) heat：In the heating process of slab, 1200 DEG C of slab heating temperature.
(3) thick de-scaling：The board briquette for controlling thick de-scaling step is 1095 DEG C.
(4) roughing：The temperature that recrystallization zone controls to start to roll is 1080 DEG C, it is ensured that reduction ratio >=12% and deformation temperature
Effective combination, and deform after crystallite dimension grow up not too much, finishing temperature control is at 1055 DEG C.Workpiece thickness 110mm, tires out
Meter reduction ratio 63%.
(5) base cooling in the middle of：Middle base is cooled down using roughing mill frame high pressure descaling water, cooling termination temperature
935℃。
(6) finish rolling：The temperature range of Unhydrated cement controlled rolling is 880 DEG C, terminates 835 DEG C of rolling temperature, rolls 14-
16 passages.In this stage rolling, using the cumulative deformation that the finish rolling stage is big, pass deformation rate is improved, improves deformation permeability,
The flattening degree of austenite is improved, increases phase transformation nucleation site, refine the crystallite dimension of steel plate after phase transformation.Accumulation reduction ratio
75.5%.
(7) air cooling:After finish rolling terminates, air cooling cooling is carried out to steel plate, be down to 20 DEG C below Ar3 transformation temperatures.
(8) cool down：Quickly cooled down using MULPIC, 510 DEG C of final cooling temperature of first stage cooling, 28 DEG C/s of cooling rate, second
230 DEG C of stage final cooling temperature, 18 DEG C/s of rate of cooling.
(9) thermal straightening：The stress in steel plate is at utmost discharged using big straightening force.
Final surface, 1/4,1/2 tissue of the steel plate produced by process above is as shown in Fig. 5, Fig. 6 and Fig. 7.Steel plate
Mechanical property 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%.
The present embodiment of embodiment 3 is 18.4mmX80M, and its specific chemical composition is as shown in table 3.
The preparation method of the multiphase X80M Pipeline Steel Plate of the high arrest toughness of High stress ratio of the present embodiment is as follows.
(1) smelt and continuous casting：Using clean steel smelting mode, on the basis of ultralow P, S, five big harmful elements of control are total
Amount, that is, control this five kinds of element sums of S, P, O, N, H less than 150ppm, it is ensured that the degree of purity of steel, uniformity.Mainization of steel
Study point as shown in table 3：During sheet billet continuous casting, using dynamic soft reduction technology, slab quality reaches C classes 0.5, slab thickness
For 300mm.
The 18.4mm X80M chemical compositions of table 3
(2) heat：In the heating process of slab, 1200 DEG C of slab heating temperature.
(3) thick de-scaling：The board briquette for 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%, it is ensured that brilliant after deformation
Particle size is grown up not too much.Workpiece thickness 80mm.Accumulative reduction ratio 73%；
(5) base cooling in the middle of：Middle base is cooled down using roughing mill frame high pressure descaling water, cooling termination temperature
950℃。
(6) finish rolling：The temperature range of Unhydrated cement controlled rolling is 935 DEG C, terminates 845 DEG C of rolling temperature, rolls 8-
12 passages.In this stage rolling, using the cumulative deformation that the finish rolling stage is big, the flattening degree of austenite is improved, increase phase transformation
Nucleation site, refines the crystallite dimension of steel plate after phase transformation.Accumulation reduction ratio 77%.
(7) air cooling：After finish rolling terminates, air cooling is carried out to steel plate and is cooled to 15 DEG C below Ar3 transformation temperatures.
(8) cool down：Quickly cooled down using MULPIC, 515 DEG C of final cooling temperature of first stage cooling, 29 DEG C/s of cooling rate, second
235 DEG C of stage final cooling temperature, 18 DEG C/s of rate of cooling.
(9) thermal straightening：The stress in steel plate is at utmost discharged using big straightening force.
Final surface, 1/4,1/2 tissue of the steel plate produced by process above is respectively such as Fig. 8, Fig. 9 and Figure 10 institute
Show.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 DWTT=100%.
The present embodiment of embodiment 4 is 30.8mmX80M, and its specific chemical composition is as shown in table 4.
The preparation method of the multiphase X80M Pipeline Steel Plate of the high arrest toughness of High stress ratio of the present embodiment is as follows.
The 30.8mm X80M chemical compositions of table 4
(1) smelt and continuous casting：Using clean steel smelting mode, on the basis of ultralow P, S, five big harmful elements of control are total
Amount, that is, control this five kinds of element sums of S, P, O, N, H less than 150ppm, it is ensured that the degree of purity of steel, uniformity.Mainization of steel
Study point as shown in table 4：During sheet billet continuous casting, using dynamic soft reduction technology, center segregation of casting blank reaches C classes 1.0, strand
Thickness is 300mm.
(2) heating of plate blank：In the heating process of slab, 1200 DEG C of slab heating temperature.
(3) thick de-scaling：The board briquette for controlling thick de-scaling step is 1100 DEG C.
(4) roughing：The temperature range of recrystallization zone controlled rolling is carried out when being 1080 DEG C, 1060 DEG C of last a time, is protected
Effective combination of card reduction ratio >=15% and deformation temperature.Crystallite dimension is grown up not too much after steel plate recrystallization rolling.Middle base
Thickness 135mm, adds up reduction ratio 60%.
(5) base cooling in the middle of：Middle base is cooled down using roughing mill frame high pressure descaling water, cooling termination temperature
870℃。
(6) finish rolling：The temperature range of Unhydrated cement controlled rolling is 860 DEG C, terminates 830 DEG C of rolling temperature, rolls 12-
16 passages.In this stage rolling, using the cumulative deformation that the finish rolling stage is big, the flattening degree of austenite is improved, increase phase transformation
Nucleation site, refines the crystallite dimension of steel plate after phase transformation.2-3 pass deformation rates are controlled simultaneously 15%, improve deformation permeability.
Accumulation reduction ratio 77.2%.
(7) air cooling:After finish rolling terminates, air cooling is carried out to steel plate and is cooled to 20 DEG C below Ar3 transformation temperatures.
(8) cool down：Quickly cooled down using MULPIC in refrigerating work procedure, 535 DEG C of final cooling temperature of first stage cooling, cooling rate 24
DEG C/s, 240 DEG C of second stage final cooling temperature, 16 DEG C/s of rate of cooling.
(9) thermal straightening：The stress in steel plate is at utmost discharged using big straightening force.
The steel plate produced using process above, 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%.
The present embodiment of embodiment 5 is 22mmX80M, and its specific chemical composition is as shown in table 5.
The preparation method of the multiphase X80M Pipeline Steel Plate of the high arrest toughness of High stress ratio of the present embodiment is as follows.
(1) smelt and continuous casting：Using clean steel smelting mode, on the basis of ultralow P, S, five big harmful elements of control are total
Amount, that is, control this five kinds of element sums of S, P, O, N, H less than 150ppm, it is ensured that the degree of purity of steel, uniformity.Mainization of steel
Learn as shown in table 5：During sheet billet continuous casting, using dynamic soft reduction technology, center segregation of casting blank reaches C classes 1.0, slab thickness
For 300mm.
The 22mm X80M chemical compositions of table 5
(2) heating of plate blank：In the heating process of slab, 1200 DEG C of slab heating temperature.
(3) thick de-scaling：The board briquette for 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 a time is carried out at 1055 DEG C, is protected
Effective combination of card reduction ratio >=15% and deformation temperature.Crystallite dimension is grown up not too much after steel plate recrystallization rolling.Middle base
Thickness 95mm, adds up reduction ratio 68%；
(5) base cooling in the middle of：Middle base is cooled down using roughing mill frame high pressure descaling water, cooling termination temperature
945℃。
(6) finish rolling：The temperature range of Unhydrated cement controlled rolling is 905 DEG C, terminates 845 DEG C of rolling temperature, rolls 12-
16 passages.In this stage rolling, using the cumulative deformation that the finish rolling stage is big, the flattening degree of austenite is improved, increase phase transformation
Nucleation site, refines the crystallite dimension of steel plate after phase transformation.2-3 pass deformation rates are controlled simultaneously 15%, improve deformation permeability.
Accumulation reduction ratio 76.8%.
(7) air cooling:After finish rolling terminates, air cooling is carried out to steel plate and is cooled to 20 DEG C below Ar3 transformation temperatures.
(8) cool down：Quickly cooled down using MULPIC in refrigerating work procedure, 505 DEG C of final cooling temperature of first stage cooling, cooling rate 27
DEG C/s, 230 DEG C of second stage final cooling temperature, 19 DEG C/s of rate of cooling.
(9) thermal straightening：The stress in steel plate is at utmost discharged using big straightening force.
The steel plate produced using process above, 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 main performance detection statistics table of each embodiment of table 7
Longitudinal main performance detection statistics table of each embodiment of table 8
Embodiment 6
The present embodiment is as shown in table 8 for the concrete composition of 33mmX80M.
The pipe line steel of the present embodiment in addition to the content of zirconium in component is had any different, the content of other components and preparation side
Method, parameter select all just the same with embodiment 1
33mm X80M chemical compositions (%) of table 8
The mechanical property of the steel plate produced using process above is as shown in Table 9 and Table 10.
Embodiment 7
The present embodiment is as shown in table 9 for the concrete composition of 33mmX80M.
The pipe line steel of the present embodiment in addition to the content of zirconium in component is had any different, the content of other components and preparation side
Method, parameter select all just the same with embodiment 1
33mm X80M chemical compositions (%) of table 9
The mechanical property of the steel plate produced using process above is as shown in Table 10 and Table 11.
The horizontal main performance detection statistics table of each embodiment of table 10
Longitudinal main performance detection statistics table of each embodiment of table 11
From table 10 and table 11, the low-temperature flexibility of pipe line steel, stress ratio and uniform elongation obtained in embodiment 6,7 compared with
Example poor performance in the range of application claims, it is seen that zirconium can simultaneously to improve the low-temperature flexibility of pipe line steel, stress ratio and
Uniform elongation has larger contribution.
Although the above-mentioned accompanying drawing that combines is described to the specific embodiment of the present invention, not to invention protection domain
Restriction, one of ordinary skill in the art should be understood that on the basis of technical scheme those skilled in the art are not required to
The various modifications or deformation made by paying creative work are still within the scope of the present invention.
Claims (9)
1. X80 pipe line steels of the high arrest toughness of a kind of High stress ratio, it is characterised in that：It is made up of the component of following weight portion：C
0.03～0.08%, Si 0.15～0.35%, Mn 1.50～2.00%, P≤0.010%, S≤0.003%, Nb 0.04～
0.08%, Ti 0.015～0.025%, Zr 0.015～0.025%, Mo≤0.03%, Cu≤0.35%, Ni≤0.30%,
Cr≤0.30%, remaining is Fe and inevitable impurity；
The preparation method of the X80 pipe line steels, comprises the steps：
1) molten iron is prepared；
2) molten iron is carried out successively desulfurization, smelting, refine and sheet billet continuous casting to process, desulfurization, smeltings and refine these three process
During the total amount of S, P, O, N, H in control system be less than 150ppm；
3) heating of plate blank, slab heating temperature is 1150 DEG C -1220 DEG C, and soaking zone temperature retention time is more than 40min, total heat time heating time
Not less than 270min；
4) slab de-scaling, the surface temperature of slab is 1070-1120 DEG C after de-scaling；
5) slab rough rolling is obtained into middle base, after cooling down to middle base, then finish rolling is carried out to middle base；In rough rolling process, then tie
The rolling temperature of crystalline region is 1050-1100 DEG C, and the temperature of final pass is 1050-1070 DEG C, the reduction ratio of final pass >=
12%；Deformation is infiltrated into into steel plate center portion；
6) steel after finish rolling is cooled down, steel billet temperature is down to 0-50 DEG C below transformation temperature Ar3 before steel plate cooling；
7) steel plate is cooled down；Thermal straightening is carried out to the steel after cooling, required steel plate is obtained, cooling step includes the first stage
And second stage, steel plate is cooled to 500-550 DEG C by the first stage using the water of 5bar, cooldown rate 20-30 DEG C/s, second-order
Steel plate is cooled to 100-250 DEG C by section using the water of 1.5-2bar, cooldown rate 10-20 DEG C/s.
2. X80 pipe line steels according to claim 1, it is characterised in that：It is made up of the component of following weight portion：C 0.03～
0.06%, Si 0.28～0.32%, Mn 1.72～1.77%, P≤0.009%, S≤0.002%, Nb 0.055～
0.063%, Ti 0.017～0.025%, Zr 0.02～0.023%, Mo≤0.03%, Cu≤0.14%, Ni≤0.30%,
Cr≤0.30%, remaining is Fe and inevitable impurity.
3. X80 pipe line steels according to claim 1, it is characterised in that：Step 5) in, when the thickness of the middle base is
During 80-140mm, the accumulation reduction ratio of rough rolling step is 50-70%.
4. X80 pipe line steels according to claim 1, it is characterised in that：Step 5) in, it is profit to the cooling procedure of middle base
The temperature of middle base is down to into 850-960 DEG C with the water under high pressure of 18-22MPa.
5. X80 pipe line steels according to claim 1, it is characterised in that：Step 5) in, in finishing stands, non-recrystallization zone
Start rolling temperature be 850-940 DEG C, finishing temperature be 820-850 DEG C, roll 8-16 passages, accumulation reduction ratio be 75-80%.
6. X80 pipe line steels according to claim 1, it is characterised in that：Step 6) in, after finish rolling terminates, steel plate is carried out
Air cooling, the temperature for making steel plate is less than 20 DEG C of transformation temperature Ar3.
7. X80 pipe line steels according to claim 1, it is characterised in that：Step 7) in, the first stage is cooled to 530 DEG C, cold
But speed is 25 DEG C/s, and second stage is cooled to 230 DEG C, and rate of cooling is 15 DEG C/s.
8. application of the arbitrary described X80M pipe line steels of claim 1-7 in extremely frigid zones transfer oil, natural gas.
9. application of the arbitrary described X80M pipe line steels of claim 1-7 in regions with complex terrain transfer oil, natural gas.
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| CN108624811B (en) * | 2018-06-04 | 2020-07-14 | 南京钢铁股份有限公司 | Large thick-wall acid-resistant corrosion-resistant pipeline steel and production method thereof |
| CN109182919B (en) * | 2018-11-22 | 2020-06-12 | 湖南华菱湘潭钢铁有限公司 | Production method of multiphase structure high-toughness ship plate steel EH47 |
| CN110566755B (en) * | 2019-08-14 | 2021-03-30 | 中国石油天然气集团有限公司 | Design method for glass fiber composite material crack stopper of X100 gas transmission pipeline |
| CN113025884B (en) * | 2021-02-07 | 2022-05-20 | 首钢集团有限公司 | Pipeline steel and preparation method thereof |
| CN112981257B (en) * | 2021-02-09 | 2022-03-22 | 鞍钢股份有限公司 | Economical thick-wall high-strength high-toughness X70M hot-rolled steel plate and manufacturing method thereof |
| CN116005071B (en) * | 2022-12-27 | 2024-05-24 | 南阳汉冶特钢有限公司 | X80 crack-arrest steel plate and production method thereof |
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