CN1978695A - Chromium-containing high-strength pipeline steel hot-rolled plate - Google Patents
Chromium-containing high-strength pipeline steel hot-rolled plate Download PDFInfo
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- CN1978695A CN1978695A CN 200510047879 CN200510047879A CN1978695A CN 1978695 A CN1978695 A CN 1978695A CN 200510047879 CN200510047879 CN 200510047879 CN 200510047879 A CN200510047879 A CN 200510047879A CN 1978695 A CN1978695 A CN 1978695A
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Abstract
The invention discloses Cr bearing high strength pipeline steel hot rolling plate and producing method. Its components weight percentages are 0.30-0.60% Cr, 0.40-0.80% C, 0.10-0.35% Si, 1.80-2.20% Mn, 0.005-0.020% P, not more than 0.003% S, 0.04-0.10% Nb, 0.008-0.030% Ti, 0.15-0.60% Ni, 0.15-0.45% Mo, 0.15-0.30% Cu, the rest Fe and unavoidable impurity, contains 73-87% lower bainite, and the rest island martensite. The producing method includes the following steps: heating up to 1160-1220 degree centigrade; rough rolling at 1010-1150 degree centigrade; finish rolling at 830-950 degree centigrade; water cooling; final cooling at 300-450 degree centigrade; controlling cooling speed at 15-30 degree centigrade per second. The invention can gain the LB main complex phase organization which can make the pipeline steel hot rolling plate yield strength reach 690-825MPa, tensile strength reach 780-960MPa, -20 degree centigrade absorbed-in-fracture energy be not less than 200J, -15 degree centigrade DWTT shearing area be not less than 85%, solve steel anisotropy caused by two phase field rolling, release the demand of large rolling load for the two phase field rolling.
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%, 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
| Sequence number | Rt 0.5 MPa | Rm MPa | A％ | Y/R | CVN -20℃，J | DWTT -15℃，SA，％ | |||||
| 1 | 2 | 3 | On average | 1 | 2 | On average | |||||
| 1 pole | 770 | 845 | 21 | 0.91 | 254 | 289 | 254 | 265 | 98 | 95 | 96 |
| 1 plate sample | 755 | 830 | 28 | 0.91 | |||||||
| 2 poles | 750 | 835 | 20 | 0.90 | 208 | 242 | 209 | 220 | 95 | 95 | 95 |
| 2 plate samples | 735 | 825 | 23 | 0.89 | |||||||
| 3 poles | 760 | 855 | 20 | 0.89 | 231 | 256 | 218 | 235 | 90 | 95 | 92 |
| 3 plate samples | 730 | 830 | 26 | 0.88 | |||||||
| 4 poles | 790 | 885 | 21 | 0.89 | 206 | 222 | 210 | 213 | 90 | 90 | 90 |
| 4 plate samples | 775 | 860 | 28 | 0.90 | |||||||
| 5 poles | 710 | 830 | 24 | 0.86 | 289 | 272 | 260 | 274 | 98 | 95 | 96.5 |
| 5 plate samples | 700 | 825 | 30 | 0.85 | |||||||
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%, 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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| CN102851615A (en) * | 2011-06-28 | 2013-01-02 | 鞍钢股份有限公司 | Tensile strength 800 MPa grade structure steel plate with low yield ratio and manufacture method thereof |
| CN103882335A (en) * | 2012-12-21 | 2014-06-25 | 鞍钢股份有限公司 | Hot-rolled high-strength steel with yield strength of 800 MPa and production method thereof |
| CN103882334A (en) * | 2012-12-21 | 2014-06-25 | 鞍钢股份有限公司 | X70 flat plate used for gas-transmission longitudinal welded pipe and producing method thereof |
| CN103882334B (en) * | 2012-12-21 | 2016-04-06 | 鞍钢股份有限公司 | A kind of gas transmission longitudinal welded pipe is dull and stereotyped and production method with X70 |
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