CN103882327B - There is pipeline steel and the manufacture method thereof of excellent strain aging performance - Google Patents
There is pipeline steel and the manufacture method thereof of excellent strain aging performance Download PDFInfo
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Abstract
The present invention discloses a kind of pipeline steel and the manufacture method thereof with excellent strain aging performance, its chemical composition composition by wt% is: C:0.02% ~ 0.06%, Si:0.10% ~ 0.40%, Mn:1.0% ~ 2.0%, P < 0.015%, S < 0.005%, Ni:0.15% ~ 0.35%, Cr:0.15% ~ 0.45%, Nb:0.02% ~ 0.49%, Ti≤0.015%, constraint element H≤0.0002%, N≤0.004%, O≤0.0015%, wherein Ti/N >=3.42, surplus is Fe and inevitable impurity, slab soaking temperature 1150-1250 DEG C, controlled rolling in two stages, recrystallization zone rolling and Unhydrated cement rolling, speed of cooling 15 ~ 40 DEG C/s, final cooling temperature controls at 500 DEG C and following, stacking slow cooling 15-30 hour, the present invention is owing to adopting low-carbon (LC)+Mn+Ni, Cr and according to the Composition Design of steel plate thickness preferably interpolation Mo, Cu then, after two-stage control rolling, air cooling adds water-cooled and final cooling temperature, obtains intensity, plasticity is excellent, the pipeline steel that strain aging effect is low.<!--1-->
Description
Technical field
The present invention relates to a kind of production technology of high-strength high-plasticity pipeline plate of moderate thickness, particularly relate to a kind of employing low-carbon (LC) Composition Design, utilize the required tissue morphology of technology acquisition rolling rear air cooling and add water-cool control phase transformation, produce X70 and above pipeline plate of moderate thickness and the manufacture method thereof with excellent strain aging performance thereof.
Background technology
Oil and gas pipes is as a kind of economy of oil and natural gas, long distance delivery instrument safely, uninterruptedly, and the direction towards major diameter, large wall thickness, high-pressure delivery strides forward, and this over-all properties to pipe line steel proposes more and more higher requirement.Strain aging performance is the brand-new requirement that domestic and international pipework construction proposes, and low strain aging sensitivity is most important to the security of oil and gas pipes, particularly based on the pipework of stress design.
Strain aging is that soft steel stands certain viscous deformation and after being heated to certain temperature, held for some time, the intensity of generation raises, and particularly yield strength raises obviously, a kind of phenomenon causing yield tensile ratio significantly to raise.Pipe line steel is a kind of high added value Low-carbon Microalloyed Steel Production steel, and heating in the viscous deformation of tubulation process and corrosion protection coating preparation process (about 200 DEG C, continue 5min) can bring out strain aging.Strain aging effect can control tubulation, steel pipe site welding is constructed and steel pipe military service performance etc. causes disadvantageous effect, and along with improving constantly of pipe line steel grade of steel, the impact of strain aging effect on steel tube performance is more and more significant.When strain aging sensitivity is higher, change is the most significantly that stress-strain(ed) curve changes discontinuous yielding into by surrendering continuously, and this is unacceptable based on stress design pipework.
In order to obtain the steel plate of low strain dynamic ageing behavior, do a lot of technical trial both at home and abroad.Patent CN101456034 provides " a kind of method of producing X80 level large-deformation resistance pipe line steel plate of moderate thickness ", this patent does not investigate the strain aging performance of steel plate, and require that Unhydrated cement compression ratio is not less than 5, the steel plate of more than 27.6mm thickness can not be produced with the continuously cast bloom of 230mm, Nb content height is at least 0.05%, higher than the addition upper limit of this patent.Patent CN101545079 provides one " the high-strength low-yield ratio X80 hot-rolled steel sheet of good-toughness and production method thereof ", this patent does not investigate the strain aging performance of products made thereby equally, and single pass draught is not less than 15% when requiring recrystallization zone rolling, add mill load and limit Application Areas, compared with this patent, scheme is added in the optimization not optimizing the elements such as Cu, Mo.Patent CN102080194 provides " a kind of large-deformation-resistance pipeline steel and production method thereof with excellent aging resistance ", need in this patent to carry out two-phase region quenching to made steel plate, although reduce strain aging sensitivity, but manufacturing process is added, reduce production efficiency and improve manufacturing cost, do not meet the green Iron & Steel Development trend of " energy-saving and emission-reduction ".Patent WO2011043287 provides " a kind of high-strength high-plasticity pipe line steel and manufacture method thereof ", in this patent, C content (wt%) is 0.07%-0.15%, with this patent C content (wt%) for 0.02%-0.06% does not conflict, and do not investigate the strain aging performance of its steel plate.Although the patent such as patent WO2009125863, JP2005015823 provides good steel plate preparation method, and made steel plate also excellent property, but all do not investigate the strain aging performance of steel plate, the former does not optimize the addition of precious metal Mo, the latter needs to heat-treat, complex process, compared with this patent, adds manufacture difficulty and cost.
Summary of the invention
The present invention is based on the shortcoming that prior art exists, a kind of pipeline steel and the manufacture method thereof with excellent strain aging performance are disclosed, adopt low-carbon (LC)+Mn+Ni, Cr and according to the economical Composition Design of steel plate thickness preferably interpolation Mo, Cu then, after two-stage control rolling, air cooling adds water-cool control phase change technique, coordinate suitable final cooling temperature, obtain suitable organizational composition, obtain intensity, plasticity is excellent, the pipeline steel that strain aging effect is low.Form according to F+B duplex structure, the properties requirement of X70 and above large-deformation-resistance pipeline steel plate thereof can be met completely, and strain aging effect is very low.
For realizing the object of the present invention, carbon component design production X70 and above rank thereof is adopted to have the method for the pipeline steel medium plate of good strain aging performance, comprise two aspects: one is that low-carbon (LC) adds Mn, Ni and becomes offshoot program with the economical steel plate of Cr, have according to steel plate thickness and select to add Mo; Two is process programs of controlled rolling+roll rear air cooling relaxation+water-cooled+stacking slow cooling, and control group is configured to the low pipe line steel of production strain aging effect.
Chemical composition composition of the present invention by wt% is: C:0.02% ~ 0.06%, Si:0.10% ~ 0.40%, Mn:1.0% ~ 2.0%, P:<0.015%, S:<0.005%, Ni:0.15% ~ 0.35%, Cr:0.15% ~ 0.45%, Nb:0.02% ~ 0.49%, Ti :≤0.015%, constraint element H≤0.0002%, N≤0.004%, O≤0.0015%, wherein Ti/N >=3.42, surplus is Fe and inevitable micro impurity element;
After the thickness t of steel plate is more than 20mm, interpolation Mo, Cu:Mo:0 of selection ~ 0.20%, Cu:0 ~ 0.40%, preferred addition manner is that [Mo%]=(t-20) × 0.01+0.02, Cu-Ni adds according to the ratio of 1:1.
Pipe line steel of the present invention adopts following operational path: to get the raw materials ready → converter or electrosmelting → external refining → continuous casting → slab reheat → controlled rolling → air cooling relaxation → controlled cooling model → steel plate stacking slow cooling → sampling detects.
Concrete steps are:
A) carry out thermal treatment again to the continuous casting material in set component span of control, soaking temperature controls in the scope of 1150-1250 DEG C, soaking time (0.2 ~ 0.6) min/mm;
B) high-pressure water descaling is carried out to the blank after coming out of the stove, remove the iron scale that blank produces in heat-processed;
C) immediately two-stage control rolling is carried out to the blank after de-scaling, i.e. recrystallization zone rolling and Unhydrated cement rolling, recrystallization zone rolling, start rolling temperature controls within the scope of 1100 ~ 1200 DEG C, cumulative deformation is more than or equal to 60%, be out of shape in recrystallization zone, with the increase of deflection, austenite recrystallization grain refining effect is obvious, when deflection reaches about 60%, grain-size thinning effect is not obvious, finishing temperature control is within the scope of 1000 ~ 1100 DEG C, obtain intermediate blank, intermediate blank air cooling carries out Unhydrated cement rolling again to less than 950 DEG C, start rolling temperature control is within the scope of 850 ~ 950 DEG C, finishing temperature control is within the scope of 750 ~ 850 DEG C, Unhydrated cement rolling reduction controls to remain on 3 ~ 7 times, Unhydrated cement rolling, makes austenite crystal obtain flattening elongation, for ferrite transformation provides more active position, and the structure refinement after phase transformation.
D) the advanced line space of the steel plate after finish to gauge is cold, then water-cooled: if produce acicular ferrite (AF) shaped steel plate, water-cooled starts temperature more than Ar3 0 ~ 35 DEG C; If produce ferrite-bainite (F+B) shaped steel plate, water-cooled starts temperature below Ar3 10 ~ 60 DEG C, makes steel plate before entering water cooling, generate the ferritic phase of 20% ~ 80%.Intermediate blank air cooling treats thermophase, and niobium titanium carbonitride Second Phase Precipitation is obvious, and austenite grain boundary obtains effectively pin, and crystal grain stability is good, and obvious alligatoring can not occur.
E) in Cooling Process, speed of cooling scope control is at 15 ~ 40 DEG C/s, and final cooling temperature controls, at 500 DEG C and following, the steel plate after water-cooled to be improved the laggard row stacking slow cooling of template through aligning.
F) the stacking slow cooling time environmentally temperature, steel plate thickness adjust: thickness of slab, can not stacking at 20mm and following; Thickness of slab more than after 20mm, envrionment temperature more than 15 DEG C, stacking 4-12 hour; Envrionment temperature below 15 DEG C, stacking 15-30 hour.Air cooling relaxation+water-cooled phase transformation is adopted to control, rolling rear relaxation makes steel plate obtain suitable tissue, steel plate is made to have high strength, high toughness plasticity and low strain dynamic ageing behavior after reasonable stacking slow cooling, compared with normally used low-carbon bainite steel, Hi-Stren steel, under identical intensity rank condition, there is low yield tensile ratio, higher homogeneous deformation elongation and significantly reduced strain aging.
The thickness of described continuous casting material is preferably 230mm.
The yield strength Rt0.5 of the As rolled steel plate that the present invention finally obtains is 485 ~ 620MPa, tensile strength Rm is 605 ~ 755MPa, AF shaped steel plate yield tensile ratio Y/T (Rt0.5/Rm)≤0.82, homogeneous deformation elongation uEL >=9%, F+B shaped steel plate yield tensile ratio Y/T (Rt0.5/Rm)≤0.80, homogeneous deformation elongation uEL >=10%.
As rolled steel plate is through 200 DEG C of oil bath timeliness after 10 ~ 15 minutes, the yield strength Rt0.5 of steel plate is 495 ~ 620MPa, tensile strength Rm is 610 ~ 755MPa, AF shaped steel plate yield tensile ratio Y/T (Rt0.5/Rm)≤0.84, homogeneous deformation elongation uEL >=6%, F+B shaped steel plate yield tensile ratio Y/T (Rt0.5/Rm)≤0.82, homogeneous deformation elongation uEL >=9%.
The present invention compared with prior art, owing to adopting low-carbon (LC)+Mn+Ni, Cr and according to the economical Composition Design of steel plate thickness preferably interpolation Mo, Cu then, after two-stage control rolling, air cooling adds water-cool control phase change technique, coordinate suitable final cooling temperature, obtain suitable organizational composition, obtain intensity, plasticity is excellent, the pipeline steel that strain aging effect is low.
Embodiment
Below by embodiment, the present invention is further described:
Moiety wt% of the present invention is: C:0.02% ~ 0.06%, Si:0.10% ~ 0.40%, Mn:1.0% ~ 2.0%, P:<0.015%, S:<0.005%, Ni:0.15% ~ 0.35%, Cr:0.15% ~ 0.45%, Nb:0.02% ~ 0.49%, Ti :≤0.015%, constraint element H≤0.0002%, N≤0.004%, O≤0.0015%, wherein Ti/N >=3.42, surplus is Fe and inevitable micro impurity element;
After the thickness t of steel plate is more than 20mm, interpolation Mo, Cu:Mo:0 of selection ~ 0.20%, Cu:0 ~ 0.40%, preferred addition manner is that [Mo%]=(t-20) × 0.01+0.02, Cu-Ni adds according to the ratio of 1:1.
Do to illustrate to composition of the present invention, technique and implementation result below by the preferred embodiments of the present invention.
The operational path that the present invention adopts is as follows: get the raw materials ready → converter or electrosmelting → external refining → casting → slab reheat → controlled rolling → air cooling relaxation → controlled cooling model → stacking slow cooling → sampling detection.
Feature of the present invention is as follows: (1) adopts low-carbon (LC) to add Mn, Ni and Cr, has the economical Composition Design selecting to add Mo, Cu, effectively reduce production cost according to steel plate thickness.
(2) method of two-stage control rolling is adopted, i.e. recrystallization zone rolling and Unhydrated cement rolling.In recrystallization zone distortion, start rolling temperature controls within the scope of 1100 ~ 1200 DEG C, finishing temperature is at about 1000 ~ 1100 DEG C, and deflection is not less than 60%, effective refinement austenite crystal.
(3) intermediate blank air cooling treats thermophase, and temperature is reduced to 850 ~ 950 DEG C.Niobium titanium carbonitride Second Phase Precipitation is obvious, and austenite grain boundary obtains effectively pin, and crystal grain stability is good, and obvious grain coarsening phenomenon can not occur.
(4) Unhydrated cement rolling, start rolling temperature controls within the scope of 850 ~ 950 DEG C, and compression ratio remains on 3-7 doubly, and finishing temperature control is within the scope of 750 ~ 850 DEG C, and austenite crystal is flattened and elongates, the tissue after phase transformation obtains effective refinement.
(5) steel plate after finish to gauge carries out air cooling relaxation, and steel plate is according to the difference of required uniform elongation before entering water cooling, and water-cooled starts temperature and is reduced near transformation temperature Ar3, and object is that the organizational composition of control steel plate is to obtain required performance.
(6) carry out water-cooled to the steel plate after relaxation, speed of cooling scope control is at 15 ~ 40 DEG C/s, and final cooling temperature controls at 500 DEG C and following.
(7) by the steel plate stacking slow cooling after water-cooled to room temperature, stacking slow cooling effectively can promote the precipitation of niobium titanium carbonitride second-phase, reduces in steel matrix the C, the atom N number that exist, reduces plate strain ageing behavior.
Below for the chemical composition of embodiments of the invention 1-13 and comparative example 14-16, processing parameter and results of property are as shown in table 1-3, comparative example is respectively from patent CN101456034, CN102080194 and WO2009125863.
1. chemical composition
The chemical composition (wt%) of embodiment 1-12 and comparative example 13-16 is as table 1.
Table 1 chemical composition (wt%)
| C | Si | Mn | Ni | Cr | Nb | Ti | Cu | Mo | N | P | S | Thickness, mm | |
| 1 | 0.02 | 0.25 | 1.50 | 0.25 | 0.15 | 0.04 | 0.01 | 0 | 0 | 0.004 | 0.01 | 0.003 | 17.5 |
| 2 | 0.04 | 0.25 | 1.50 | 0.25 | 0.15 | 0.04 | 0.01 | 0 | 0 | 0.004 | 0.01 | 0.003 | 17.5 |
| 3 | 0.06 | 0.25 | 1.50 | 0.25 | 0.15 | 0.04 | 0.01 | 0 | 0 | 0.004 | 0.01 | 0.003 | 18.4 |
| 4 | 0.04 | 0.10 | 1.00 | 0.15 | 0.15 | 0.02 | 0.01 | 0.40 | 0.03 | 0.004 | 0.01 | 0.003 | 21 |
| 5 | 0.04 | 0.25 | 1.50 | 0.25 | 0.30 | 0.04 | 0.01 | 0.20 | 0 | 0.004 | 0.01 | 0.003 | 22 |
| 6 | 0.04 | 0.40 | 2.00 | 0.35 | 0.45 | 0.045 | 0.01 | 0 | 0.03 | 0.004 | 0.01 | 0.003 | 18.4 |
| 7 | 0.05 | 0.20 | 1.70 | 0.20 | 0.20 | 0.04 | 0.015 | 0.20 | 0 | 0.004 | 0.01 | 0.003 | 21 |
| 8 | 0.05 | 0.20 | 1.70 | 0.20 | 0.20 | 0.04 | 0.015 | 0.20 | 0 | 0.004 | 0.01 | 0.003 | 23.7 |
| 9 | 0.05 | 0.20 | 1.70 | 0.20 | 0.20 | 0.04 | 0.015 | 0.20 | 0.12 | 0.004 | 0.01 | 0.003 | 28.2 |
| 10 | 0.05 | 0.20 | 1.70 | 0.20 | 0.20 | 0.04 | 0.015 | 0 | 0.22 | 0.004 | 0.01 | 0.003 | 30 |
| 11 | 0.05 | 0.20 | 1.70 | 0.20 | 0.20 | 0.04 | 0.015 | 0 | 0.12 | 0.004 | 0.01 | 0.003 | 40 |
| 12 | 0.05 | 0.20 | 1.70 | 0.20 | 0.20 | 0.04 | 0.015 | 0.20 | 0.22 | 0.004 | 0.01 | 0.003 | 30 |
| 13 | 0.05 | 0.20 | 1.70 | 0.20 | 0.20 | 0.04 | 0.015 | 0.20 | 0 | 0.004 | 0.01 | 0.003 | 40 |
| 14 | 0.037 | 0.2 | 1.5 | 0.22 | 0.22 | 0.06 | 0.012 | 0 | 0 | 0.0015 | 0.005 | 0.003 | 12 |
| 15 | 0.08 | 0.22 | 1.57 | 0.25 | 0.13 | 0.03 | 0.012 | 0.04 | 0 | * | 0.008 | 0.0007 | * |
| 16 | 0.03 | 0.25 | 1.91 | 0 | 0 | 0 | 0.011 | 0.00 | 0.1 | 0.0026 | 0.007 | 0.0018 | 20 |
Note: the concrete numerical value that relevant item is not provided in * referenced patent.
2. hot rolling technology
The processing parameter of embodiment 1-13, comparative example 14-16 is in table 2.
Table 2 processing parameter
Note: the concrete numerical value that relevant item is not provided in * referenced patent.
3. results of property
Detect the mechanical property of steel plate before and after timeliness respectively, embodiment 1-13, comparative example 14-16 performance test results are as shown in table 3.Aging test adopts oil bath, and oil temperature 200 DEG C, sample is incubated 12min and detects after room temperature preliminary draft 1% in oil.
Performance test results before and after table 3 timeliness
Note: the concrete numerical value that relevant item is not provided in * referenced patent.
Claims (2)
1. one kind has the manufacture method of the pipeline steel of excellent strain aging performance, it is characterized in that, its chemical composition composition by wt% is: C:0.02% ~ 0.06%, Si:0.10% ~ 0.40%, Mn:1.0% ~ 2.0%, P:<0.015%, S:<0.005%, Ni:0.15% ~ 0.35%, Cr:0.15% ~ 0.45%, Nb:0.02% ~ 0.49%, Ti:0 ~ 0.015%, constraint element H≤0.0002%, N≤0.004%, O≤0.0015%, wherein Ti/N >=3.42, surplus is Fe and inevitable micro impurity element, adopt following operational path: to get the raw materials ready → converter or electrosmelting → external refining → continuous casting → slab reheat → controlled rolling → air cooling relaxation → controlled cooling model → steel plate stacking slow cooling → sampling detects, and concrete steps are:
A) carry out thermal treatment again to the continuous casting material in set component span of control, soaking temperature controls in the scope of 1150-1250 DEG C, soaking time 0.2 ~ 0.6min/mm;
B) high-pressure water descaling is carried out to the blank after coming out of the stove, remove the iron scale that blank produces in heat-processed;
C) immediately two-stage control rolling is carried out to the blank after de-scaling, i.e. recrystallization zone rolling and Unhydrated cement rolling, recrystallization zone rolling, start rolling temperature controls within the scope of 1100 ~ 1200 DEG C, cumulative deformation is more than or equal to 60%, be out of shape in recrystallization zone, finishing temperature control is within the scope of 1000 ~ 1100 DEG C, obtain intermediate blank, intermediate blank air cooling carries out Unhydrated cement rolling again to less than 950 DEG C, start rolling temperature control is within the scope of 850 ~ 950 DEG C, finishing temperature control is within the scope of 750 ~ 850 DEG C, Unhydrated cement rolling reduction controls to remain on 3-7 doubly,
D) the advanced line space of the steel plate after finish to gauge is cold, then water-cooled: if produce acicular ferrite (AF) shaped steel plate, water-cooled starts temperature more than Ar3 0 ~ 35 DEG C; If produce ferrite-bainite (F+B) shaped steel plate, water-cooled starts temperature below Ar3 10 ~ 60 DEG C, make steel plate enter water cooling to become previous existence volume fraction be 20% ~ 80% ferritic phase;
E) in Cooling Process, speed of cooling scope control is at 15 ~ 40 DEG C/s, and final cooling temperature controls, at 500 DEG C and following, the steel plate after water-cooled to be improved the laggard row stacking slow cooling of template through aligning;
F) the stacking slow cooling time environmentally temperature, steel plate thickness adjust: thickness of slab at 20mm and following, not stacking; Thickness of slab more than after 20mm, envrionment temperature more than 15 DEG C, stacking 4-12 hour; Envrionment temperature below 15 DEG C, stacking 15-30 hour.
2. a kind of manufacture method with the pipeline steel of excellent strain aging performance according to claim 1, it is characterized in that, described steel plate is after thickness t is more than 20mm, add Mo, Cu:Mo:0 ~ 0.20%, Cu:0 ~ 0.40%, addition manner is that [Mo%]=(t-20) × 0.01+0.02, Cu-Ni adds according to the ratio of 1:1.
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| CN104789863B (en) * | 2015-03-20 | 2017-01-18 | 宝山钢铁股份有限公司 | X80 pipeline steel with good anti-strain aging property, pipeline pipe and manufacturing method of pipeline pipe |
| CN105002437B (en) * | 2015-07-02 | 2017-11-10 | 首钢总公司 | A kind of production method of low yield strength ratio acid-resisting submerged pipeline steel |
| CN106636958B (en) * | 2015-07-16 | 2018-09-04 | 中国科学院金属研究所 | One kind pipe line steel containing Cu and its reinforcing heat treatment process |
| CN106702118B (en) * | 2016-12-23 | 2020-04-21 | 首钢集团有限公司 | Cooling process for reducing work hardening effect of titanium microalloyed high-strength steel |
| CN107988557A (en) * | 2017-12-08 | 2018-05-04 | 江苏省沙钢钢铁研究院有限公司 | With excellent strain-aging performance plus Ti pipe line steel and preparation method |
| CN111167866A (en) * | 2020-01-04 | 2020-05-19 | 鞍钢股份有限公司 | Hardness control method for thick X80M grade pipeline bent pipe steel plate |
| CN111139405A (en) * | 2020-03-10 | 2020-05-12 | 唐山中厚板材有限公司 | Production method of low-cost short-process flaw detection-guaranteed medium plate |
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| CN101906568A (en) * | 2010-08-12 | 2010-12-08 | 中国石油天然气集团公司 | High-grade large-strain pipeline steel and manufacturing method of steel pipe |
| CN102828125A (en) * | 2011-06-14 | 2012-12-19 | 鞍钢股份有限公司 | Strain design based pipe line steel X70 and its manufacturing method |
| CN102828120A (en) * | 2011-06-14 | 2012-12-19 | 鞍钢股份有限公司 | Strain design based economical pipe line steel and its manufacturing method |
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| JPH08209240A (en) * | 1995-02-02 | 1996-08-13 | Nippon Steel Corp | Production of steel plate for line pipe excellent in co2 corrosion resistance and low temperature toughness |
| JP5143473B2 (en) * | 2007-05-15 | 2013-02-13 | 株式会社神戸製鋼所 | Manufacturing method of high strength and low yield ratio steel sheet with excellent HAZ toughness |
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| CN101906568A (en) * | 2010-08-12 | 2010-12-08 | 中国石油天然气集团公司 | High-grade large-strain pipeline steel and manufacturing method of steel pipe |
| CN102828125A (en) * | 2011-06-14 | 2012-12-19 | 鞍钢股份有限公司 | Strain design based pipe line steel X70 and its manufacturing method |
| CN102828120A (en) * | 2011-06-14 | 2012-12-19 | 鞍钢股份有限公司 | Strain design based economical pipe line steel and its manufacturing method |
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