CN100434562C - Cr-containing high-strength pipeline steel hot-rolled flat plate and production method thereof - Google Patents
Cr-containing high-strength pipeline steel hot-rolled flat plate and production method thereof Download PDFInfo
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 51
- 239000010959 steel Substances 0.000 title claims abstract description 51
- 238000004519 manufacturing process Methods 0.000 title claims abstract description 11
- 238000005096 rolling process Methods 0.000 claims abstract description 32
- 229910001563 bainite Inorganic materials 0.000 claims abstract description 16
- 229910052799 carbon Inorganic materials 0.000 claims abstract description 9
- 229910052802 copper Inorganic materials 0.000 claims abstract description 9
- 229910052748 manganese Inorganic materials 0.000 claims abstract description 8
- 229910052758 niobium Inorganic materials 0.000 claims abstract description 8
- 238000001816 cooling Methods 0.000 claims abstract description 7
- 229910000734 martensite Inorganic materials 0.000 claims abstract description 7
- 239000000126 substance Substances 0.000 claims abstract description 7
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 6
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 6
- 229910052759 nickel Inorganic materials 0.000 claims abstract description 6
- 229910052719 titanium Inorganic materials 0.000 claims abstract description 5
- 238000010438 heat treatment Methods 0.000 claims abstract description 4
- 239000012535 impurity Substances 0.000 claims abstract description 3
- 229910052742 iron Inorganic materials 0.000 claims abstract description 3
- 229910052698 phosphorus Inorganic materials 0.000 claims abstract description 3
- 238000002360 preparation method Methods 0.000 claims abstract description 3
- 229910052717 sulfur Inorganic materials 0.000 claims abstract description 3
- 238000005098 hot rolling Methods 0.000 claims description 24
- 239000004615 ingredient Substances 0.000 claims description 6
- 230000001186 cumulative effect Effects 0.000 claims description 3
- 230000000994 depressogenic effect Effects 0.000 claims description 2
- 229910052804 chromium Inorganic materials 0.000 abstract description 3
- 238000010008 shearing Methods 0.000 abstract 1
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 abstract 1
- 239000011651 chromium Substances 0.000 description 21
- 239000011572 manganese Substances 0.000 description 15
- 239000010955 niobium Substances 0.000 description 10
- 239000010949 copper Substances 0.000 description 9
- 238000005516 engineering process Methods 0.000 description 8
- PXHVJJICTQNCMI-UHFFFAOYSA-N nickel Substances [Ni] PXHVJJICTQNCMI-UHFFFAOYSA-N 0.000 description 7
- 239000010936 titanium Substances 0.000 description 7
- VNWKTOKETHGBQD-UHFFFAOYSA-N methane Chemical compound C VNWKTOKETHGBQD-UHFFFAOYSA-N 0.000 description 6
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- 229910000859 α-Fe Inorganic materials 0.000 description 5
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 4
- RYGMFSIKBFXOCR-UHFFFAOYSA-N Copper Chemical compound [Cu] RYGMFSIKBFXOCR-UHFFFAOYSA-N 0.000 description 4
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 4
- 230000000694 effects Effects 0.000 description 4
- 238000003801 milling Methods 0.000 description 4
- 238000001556 precipitation Methods 0.000 description 4
- 229910001566 austenite Inorganic materials 0.000 description 3
- 230000015572 biosynthetic process Effects 0.000 description 3
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- 238000010276 construction Methods 0.000 description 2
- 239000013078 crystal Substances 0.000 description 2
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- 229910052757 nitrogen Inorganic materials 0.000 description 2
- RMLPZKRPSQVRAB-UHFFFAOYSA-N tris(3-methylphenyl) phosphate Chemical compound CC1=CC=CC(OP(=O)(OC=2C=C(C)C=CC=2)OC=2C=C(C)C=CC=2)=C1 RMLPZKRPSQVRAB-UHFFFAOYSA-N 0.000 description 2
- VYZAMTAEIAYCRO-UHFFFAOYSA-N Chromium Chemical compound [Cr] VYZAMTAEIAYCRO-UHFFFAOYSA-N 0.000 description 1
- PWHULOQIROXLJO-UHFFFAOYSA-N Manganese Chemical compound [Mn] PWHULOQIROXLJO-UHFFFAOYSA-N 0.000 description 1
- ZOKXTWBITQBERF-UHFFFAOYSA-N Molybdenum Chemical compound [Mo] ZOKXTWBITQBERF-UHFFFAOYSA-N 0.000 description 1
- RTAQQCXQSZGOHL-UHFFFAOYSA-N Titanium Chemical compound [Ti] RTAQQCXQSZGOHL-UHFFFAOYSA-N 0.000 description 1
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- 229910052739 hydrogen Inorganic materials 0.000 description 1
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- GUCVJGMIXFAOAE-UHFFFAOYSA-N niobium atom Chemical compound [Nb] GUCVJGMIXFAOAE-UHFFFAOYSA-N 0.000 description 1
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Abstract
The invention discloses a Cr-containing high-strength pipeline steel hot-rolled flat plate and a production method thereof, wherein the Cr-containing high-strength pipeline steel hot-rolled flat plate comprises the following chemical components in percentage by weight: 0.30 to 0.60 percent of Cr, 0.04 to 0.08 percent of C, 0.10 to 0.35 percent of Si, 1.80 to 2.20 percent of Mn, 0.005 to 0.020 percent of P, less than or equal to 0.003 percent of S, 0.04 to 0.10 percent of Nb, 0.008 to 0.030 percent of Ti, 0.15 to 0.60 percent of Ni, 0.15 to 0.45 percent of Mo, 0.15 to 0.30 percent of Cu, and the balance of iron and inevitable impurities, and has a complex phase structure of 73 to 87 percent of lower bainite and the rest island martensite. The preparation method comprises the following steps: heating temperature is 1160-1220 ℃, rough rolling temperature is 1010-1150 ℃, finish rolling temperature is 830-950 ℃, then water cooling is carried out, final cooling temperature is 300-450 ℃, and cooling speed is controlled to be 15-30 ℃/S. The invention can obtain a complex phase structure mainly comprising the following bainite LB. The yield strength of the hot rolled flat plate of the pipeline steel can reach 690-825 MPa, the tensile strength reaches 780-960 MPa, the impact energy at minus 20 ℃ is more than or equal to 200J, and the shearing area of the DWTT at minus 15 ℃ is more than or equal to 85%. The anisotropy of the steel plate caused by the rolling of the two-phase region is solved, and the requirement of the rolling of the two-phase region on the large rolling force of the rolling mill is released.
Description
Technical field
The invention belongs to a kind of high-intensity high-tenacity metallic substance and preparation method thereof, mainly be applicable to and make high pressure, heavy caliber petroleum natural-gas transfer pipeline high tensile pipeline steel hot-rolling flat plate steel and production method thereof.
Technical background
Oil and Natural Gas Transportation Pipeline is the integral part of energy construction.Along with the development of world industry and the development of metallurgical technology, be to reduce pipe-line construction cost and operation cost, improve oil, natural gas transport efficient, transport pipe rapidly to big caliber, be transferred medium and develop to high pressure and high-density direction.At nearly 2 years, X65, X70 become after the main grade of steel of conveying route, X80 also in broadened application scope progressively, in order to satisfy medium to more high pressure, high-density are grown the demand for development that distance is carried, the X100 pipe line steel that needs the exploitation higher category, the yield strength of the pipe line steel X100 of use that requires reaches more than the 690MPa, the low-temperature flexibility of also having relatively high expectations simultaneously, and-20 ℃ low-temperature flexibility is more than 175J.Roll up the 5th phase the 33rd page of " exploitation of X100 pipe line steel " temple Tian Haonan etc. as " Wide and Thick Slab " the 3rd, article is introduced X100 design mix (weight percent) and is C:0.043%~0.067%, Si:0.06%~0.27%, Mn:1.60%~2.00%, Mo:0.00%~0.39%, Nb:0.032%~0.045%, Ti:0.012%~0.019%, B:0.000%~0.0016%, and other contains Ni, Cu.Adopt TMCP technology: heat 1150~1250 ℃, breaking down is not mentioned, 880~720 ℃ of finish to gauges, cold 450 ℃~room temperature eventually.After the production, the performance yield strength of the X100 that obtains: 437~633MPa, tensile strength: 619~805MPa, its weak point is that yield strength is not enough." Wide and Thick Slab " the 6th volume the 5th phase 43 " exploitation of X80-X100 level pipe line steel " Lu Yuezhang, Zhou Yuhong, the X100 design mix (weight percent) that article is introduced is C:0.06%~0.08%, Si:0.20%~0.40%, Mn:1.80%~2.00%, Mo:0.10%~0.30%, Nb:0.04%~0.06%, Ti:0.015%~0.025%, Ni:0.00%~0.25%, Cu:0.00%~0.25%, concrete technology is not mentioned, the performance yield strength of the X100 that obtains: pole sample 739~755MPa, plate tensile sample 665~681MPa, tensile strength: pole sample 792~820MPa, plate tensile sample 785~816MPa, its weak point is that the yield strength of the plate tensile sample that adopts of condition of delivery is not enough.At publication number is CN1148416A, denomination of invention is that ferrite by martensite/bainite and 20%~90% constitutes for the tissue of steel of introducing in " the high strength line pipes steel with low yielding ratio and good low-temperature flexibility ", to be that two-phase region accumulative total is rolling depress than being 10%~70% its rolling technology, the hot rolling final temperature is 650~800 ℃, its shortcoming is that the rolling load of milling train is required than higher, general milling train is difficult to adapt to, and two-phase region is rolling, has each diversity on the performance.
Summary of the invention
For overcoming the problems referred to above, the object of the present invention is to provide and a kind of tabular the and yield strength pole sample is reached more than the 690MPa, the high tensile pipeline steel hot-rolling flat plate and the production method thereof that contain lower bainite+martensite heterogeneous structure are to avoid the problem that the rolling load of milling train is restricted in the operation of rolling.
The object of the present invention is achieved like this, a kind of Cr high-strength line-pipe steel hot-rolling flat plate that contains, its chemical ingredients (weight percent) is: Cr 0.30%~0.60%, C 0.04%~0.08%, Si 0.10%~0.35%, Mn 1.80%~2.20%, P 0.005%~0.020%, S≤0.003%, and Nb 0.04%~0.10%, Ti0.008%~0.030%, Ni 0.15%~0.60%, and Mo 0.15%~0.45%, and Cu 0.15%~0.30%, all the other are iron and inevitable impurity, have the heterogeneous structure of 73%~87% lower bainite and remaining island martensite body.
The Cr high-strength line-pipe steel hot-rolling flat plate that contains of the present invention can also be on the basis of adopting mentioned component, and chemical ingredients (weight percent) also comprises N≤0.008% and Als:0.015%~0.045%.
The present invention adopts the reason of technique scheme to be:
Chromium (Cr): can widen the formation temperature interval of lower bainite, obtain enough lower bainites, thereby improve intensity, Cr and Nb use simultaneously in addition, can promote separating out of Nb, improve the effect of precipitation strength.Along with the interpolation of Cr, intensity is close to straight line and rises.But too big as add-on, significantly reduce welded heat affecting zone (HAZ) toughness and weldability, so on be limited to 0.60%.Be lower than 0.30%, the effect of Cr is not obvious.
Carbon (C): along with carbon content increases, the intensity of steel increases and toughness, welding property reduce.But because reaching its maturity of cooling controlling and rolling controlling process and micro-alloying technology is the performance of improving welded heat affecting zone (HAZ) simultaneously, the carbon content in the steel reduces gradually, and the high tensile pipeline steel carbon content should be advisable 0.04%~0.08%.
Manganese (Mn): the solution strengthening effect is arranged, also can reduce γ-α transformation temperature, and then the refinement ferrite crystal grain.Studies show that: add 1.80%~2.20%Mn, γ-α transformation temperature reduces by 50 ℃, but refinement ferrite crystal grain and keep Polygons; When adding 1.5%~2.0%Mn, can obtain acicular ferrite structure.Mn also can improve toughness, reduce ductile-brittle transition temperature, so early stage pipe line steel is based on C-Mn.But Mn content is crossed the center segregation that the controlled rolling steel plate is quickened in conference, thereby causes the anisotropy of steel plate and steel pipe mechanical property, and causes the reduction of anti-HIC performance.Thereby in high grade of steel pipe line steel, the content of Mn should remain in the reasonable range (1.80%~2.20%), and Mn/C ratio also should suit.Because Mn suppresses pearlitic formation, promote simultaneously lower bainite to form, thereby will obtain the X100 grade of steel that Mn content should reach 1.80% can effectively control the lower bainite shape.
Niobium (Nb): can postpone austenite recrystallization, reduce transformation temperature, the performance that obtains to require by mechanism such as solution strengthening, phase transformation strengthening, precipitation strengths.0.04%~0.10%Nb steel cooperates rational rolling technology, and can obtaining uniformly, following bainite structure is main compound phase and excellent toughness.
Titanium (Ti): after adding trace Ti, the embrittlement temperature district disappears.This is because in the austenite high-temperature zone, and (N, C) easier generation so N is fixed on the austenite high-temperature zone by TiN, form tiny TiN to TiN, improve the low-temperature flexibility of welded H AZ, during the Ti too high levels, easily form the TiN of alligatoring, and low-temperature flexibility reduces than Nb.Therefore, Ti 0.008%~0.030%.
Molybdenum (Mo): can reduce formation, the promotion bainite transformation of transformation temperature, inhibition granular ferrite, and can improve the precipitation strength effect of Nb (C, N), the pipe line steel of this alloy system has the tiny lower bainite tissue that contains high density dislocation, and intensity height (reaching X100), impelling strength are good.In the X100 pipe line steel, Mo content is more satisfactory 0.15%~0.45%.
Copper (Cu): by precipitation strength, intensity is improved greatly, and can improve corrosion resistance and anti-hydrogen induced cracking (HIC) ability.Copper content is low, and is inoperative, when too high, can cause that again matrix metal and HAZ toughness descend, and generation copper splits when hot-work.Therefore, Cu 0.15%~0.30%.
Nickel (Ni): purpose is to improve intensity and don't reduce low-temperature flexibility and on-the-spot weldability, can also avoid the copper in continuous casting and the course of hot rolling to split.From improving intensity and improving HAZ toughness aspect, especially effectively the add-on of Ni is 0.15%~0.60%, and is too many not only uneconomical but also can reduce HAZ toughness and on-the-spot weldability.
The present invention prepares the production method of the above-mentioned Cr of containing high-strength line-pipe steel hot-rolling flat plate, adopt TMCP technology, slab heating temperature: 1160~1220 ℃, roughing temperature range: 1010~1150 ℃, final rolling temperature interval: 830~950 ℃, water-cooled then, the final cooling temperature interval: 300~450 ℃, 15~30 ℃/S of controlled chilling speed.
The present invention produces when containing Cr high-strength line-pipe steel hot-rolling flat plate as stated above, and rough rolling step has guaranteed that at least three are depressed passage 〉=15%, finish rolling stage cumulative deformation 〉=60%.
The present invention produces contains the Cr high-strength line-pipe steel and compares with existing X100 pipe line steel and have following advantage:
1. the tabular and yield strength pole sample reaches the above design requirements of 690MPa fully, and tensile strength reaches the above design requirements of 780MPa fully.
2. the present invention can obtain based on lower bainite, and remainder is the complex tissue of island martensite body, has good low-temperature flexibility, and its-20 ℃ of ballistic works are greater than 200J.The shear area of-15 ℃ of DWTT reaches more than 90%.
3. the interval broad (120 ℃) of the final rolling temperature of technology of the present invention, finish the dislocation accumulation in finish rolling interval and grain refining task for the line steel hot rolling flat plate of uni-tension rolling and created possiblely, be suitable for the bigger characteristics of temperature drop during the finish rolling that line steel hot rolling flat plate is different from hot-rolled coil.
4. final rolling temperature of the present invention interval is 830~950 ℃, has avoided two-phase region rolling, has solved the anisotropy by the rolling steel plate that causes of two-phase region, has liberated the rolling requirement to the big rolling load of milling train of two-phase region simultaneously.
Description of drawings
Fig. 1 organizes photo for the transmission electron microscope that the present invention contains Cr high-strength line-pipe steel hot-rolling flat plate sample;
Fig. 2 organizes photo for the transmission electron microscope that the present invention contains another sample of Cr high-strength line-pipe steel hot-rolling flat plate.
Embodiment
The chemical ingredients that the present invention contains Cr high-strength line-pipe steel hot-rolling flat plate sees Table 1.
Table 1 contains Cr high-strength line-pipe steel hot-rolling flat plate chemical ingredients (wt%)
Sequence number | C | Si | Mn | P | S | Cu | Ni | Cr | Mo | Nb | Ti | N | Als |
1 | 0.079 | 0.24 | 2.03 | 0.011 | 0.003 | 0.21 | 0.46 | 0.35 | 0.32 | 0.06 | 0.015 | 0.006 | 0.020 |
2 | 0.055 | 0.25 | 1.97 | 0.013 | 0.003 | 0.20 | 0.45 | 0.32 | 0.31 | 0.04 | 0.013 | 0.007 | 0.040 |
3 | 0.071 | 0.26 | 2.02 | 0.013 | 0.002 | 0.20 | 0.46 | 0.35 | 0.31 | 0.07 | 0.019 | 0.008 | 0.030 |
4 | 0.080 | 0.33 | 2.20 | 0.018 | 0.003 | 0.30 | 0.58 | 0.58 | 0.43 | 0.10 | 0.029 | 0.005 | 0.040 |
5 | 0.041 | 0.11 | 1.83 | 0.008 | 0.001 | 0.15 | 0.16 | 0.30 | 0.15 | 0.04 | 0.010 | 0.004 | 0.025 |
The production method of the Cr of containing high-strength line-pipe steel hot-rolling flat plate of the present invention sees Table 2.
Table 2 contains Cr high-strength line-pipe steel hot-rolling flat plate production method
Sequence number | Heating temperature, ℃ | The roughing temperature range, ℃ | Roughing 〉=15% road number of times | The final rolling temperature interval, ℃ | The finish rolling cumulative deformation, % | Final cooling temperature, ℃ | Cooling rate ℃/S |
1 | 1194 | 1100-1010 | 4 | 950-832 | 68 | 380 | 21 |
2 | 1163 | 1109-1012 | 3 | 950-843 | 68 | 367 | 23 |
3 | 1220 | 1148-1030 | 4 | 950-835 | 64 | 394 | 21 |
4 | 1160 | 1130-1010 | 3 | 950-850 | 66 | 450 | 15 |
5 | 1220 | 1150-1050 | 4 | 930-830 | 65 | 300 | 30 |
The Cr of containing high-strength line-pipe steel hot-rolling flat plate assay of the present invention sees Table 3.
Table 3 contains Cr high-strength line-pipe steel hot-rolling flat plate performance
As shown in Figure 1, 2, the tissue that contains Cr high-strength line-pipe steel hot-rolling flat plate of the present invention is based on lower bainite, and all the other are the island martensite body.By quantitative metallography statistics, calculating, the lower bainite content of sample shown in Figure 1 is 87%, and the lower bainite content of sample shown in Figure 2 is 80%.
Claims (4)
1. one kind contains Cr high-strength line-pipe steel hot-rolling flat plate, it is characterized in that: chemical ingredients (weight percent) is: Cr 0.30%~0.60%, C 0.04%~0.08%, Si 0.10%~0.35%, Mn 1.80%~2.20%, P 0.005%~0.020%, S≤0.003%, Nb 0.04%~0.10%, and Ti 0.008%~0.030%, and Ni 0.15%~0.60%, Mo 0.15%~0.45%, Cu 0.15%~0.30%, and all the other are iron and inevitable impurity, has the heterogeneous structure of 73%~87% lower bainite and remaining island martensite body.
2. the Cr high-strength line-pipe steel hot-rolling flat plate that contains according to claim 1, it is characterized in that: chemical ingredients (weight percent) also comprises N≤0.008% and Als:0.015%~0.045%.
3. prepare the described a kind of production method that contains Cr high-strength line-pipe steel hot-rolling flat plate of claim 1, it is characterized in that: slab heating temperature: 1160~1220 ℃, roughing temperature range: 1010~1150 ℃, final rolling temperature interval: 830~950 ℃, water-cooled then, the final cooling temperature interval: 300~450 ℃, 15~30 ℃/S of controlled chilling speed.
4. a kind of preparation according to claim 3 contains the production method of Cr high-strength line-pipe steel hot-rolling flat plate, it is characterized in that: rough rolling step has guaranteed that at least three are depressed passage 〉=15%, finish rolling stage cumulative deformation 〉=60%.
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CN1148416A (en) * | 1995-02-03 | 1997-04-23 | 新日本制铁株式会社 | High strength line-pipe steel having low-yield ratio and excullent low-temp toughness |
JP2001303191A (en) * | 2000-04-19 | 2001-10-31 | Nippon Steel Corp | Ultrahigh strength steel pipe for line pipe, excellent in haz toughness in weld zone, and its manufacturing method |
JP2004099930A (en) * | 2002-09-05 | 2004-04-02 | Nippon Steel Corp | High-strength welded steel pipe having excellent toughness of weld zone, and method for manufacturing the same |
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CN104894338A (en) * | 2014-03-05 | 2015-09-09 | 鞍钢股份有限公司 | Low-temperature segmented heating method for dual-phase steel |
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