CN103510003B - A kind of large diameter pipeline Chinese People's Anti-Japanese Military and Political College is out of shape heterogeneous X100 High Strength Steel Plate and manufacture method thereof - Google Patents
A kind of large diameter pipeline Chinese People's Anti-Japanese Military and Political College is out of shape heterogeneous X100 High Strength Steel Plate and manufacture method thereof Download PDFInfo
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Abstract
The invention belongs to low-alloy high-strength pipe line steel manufacturing technology field, more specifically a kind of large diameter pipeline Chinese People's Anti-Japanese Military and Political College is out of shape heterogeneous X100 High Strength Steel Plate and manufacture method thereof, it is made up of component once by weight percentage: C:0.04 ~ 0.08%, Si:0.15 ~ 0.35%, Mn:1.60 ~ 2.00%, P≤0.008%, S≤0.003%, Nb:0.07 ~ 0.11%, Ti:0.015 ~ 0.025%, Mo≤0.25%, Cu≤0.35%, Ni≤0.030%, Cr≤0.030%, all the other are Fe and inevitable impurity, of the present invention effective: P content maximum value 0.010% in Composition Design in the present invention, S content maximum value 0.003%, steel is purer, high niobium Composition Design, to the grain refining of steel plate and strength-enhancing effect comparatively outstanding, steel plate is saved Mo, adding of the noble metals such as Ni, cost is lower, energy-conserving and environment-protective, meet Materials direction, be easier to produce and promote, the yield strength 690-760MPa of steel plate of the present invention, tensile strength 870-920MPa, uniform elongation >=10%, yield tensile ratio≤0.78,-20 DEG C of Charpy-V impact power >=300J,-15 DEG C of drop weight tearing experiment shear area >=85%.
Description
Technical field
The invention belongs to low-alloy high-strength pipe line steel manufacturing technology field, more specifically a kind of large diameter pipeline Chinese People's Anti-Japanese Military and Political College is out of shape heterogeneous X100 High Strength Steel Plate and manufacture method thereof.
Background technology
Along with domestic and international to the continuous demand of the oil and gas energy, the engineering construction of long distance oil-gas transport pipe gets more and more.Pipeline, towards heavy caliber, the development of high pressure-bearing, is reduce engineering construction material cost, and improving the thinning duct thickness of the strength of materials becomes and reduce costs best means.Takeuchi studies proof, and when other factors is constant, along with the rising of steel strength, effective plasticity of material declines gradually, and its uniform elongation is reduction trend.And one of challenging field of pipe-line construction most is seismic region and permafrost band, may there is large viscous deformation in the buried pipeline in these areas, and line pipe needs the performance of higher incompressible and tension strain.In recent years, for improving air input efficiency, the pipeline high tensile steel plate that diameter is greater than 1000mm is applied in long distance Natural Gas Transmission Pipeline Engineering again and again, steel plate width reaches more than 3700mm, the template of steel plate, planeness, the thickness evenness of steel plate, intensity homogeneity control difficulty comparatively greatly, and the production for hot rolling Plate Steel is a challenge greatly.For ensureing pipeline transportation security, based on stress design principle, the heavy caliber high-strength X100 Pipeline Steel Plate with the heterogeneous fine grained texture of property of resisting large deformation is subject to research, planner praises highly.
For meeting the requirements such as X100 pipeline steel strength, toughness, stain resistance energy, weldability, homogeneity, just must formulate according to large-deformation-resistance pipeline steel standard at the beginning of production technique and Composition Design, adopt the system that these technology can provide safe and reliable, ensure economic solution, the innovative design based on stress design solves the practical problems of high-strength line-pipe steel application in engineering conveying simultaneously.
Before making the present invention, there is the research of the relevant Chinese People's Anti-Japanese Military and Political College of Japanese JFE company distortion X100 hot-rolled steel sheet, but the organization design of Japanese Chinese People's Anti-Japanese Military and Political College distortion X100 steel plate is bainite+Ma Ao island (B+M/A) duplex structure, and technological design is TMCP+HOP technique, as shown in Figure 1.Therefore Chinese People's Anti-Japanese Military and Political College's distortion X100 Pipeline Steel Plate that they are produced is obtained by HOP technique, their tissue is made up of bainite+Ma Ao island (B+M/A) dual phase microstructure, the obdurability of this tissue is fine, but plasticity is not fine, steel plate can not be met in length and breadth to the requirement of uniform elongation.If simultaneously because M-A tissue controls bad, thick M-A tissue can be formed, to the toughness of steel plate and arrest toughness very unfavorable, although therefore this invention is feasible, need to invest online equipment for Heating Processing, cost is higher, and process window is very narrow, actually operating difficulty is large.And the domestic this duplex structure filed an application by low C multicomponent microalloying design and specific Controlled Rolling And Controlled Cooling acquisition.Duplex structure is made up of ferrite+bainite (F+B) dual phase microstructure.
The patent of invention comparatively close with the present invention has: 1) Chinese patent, Application Number (patent): CN201010541219.4, a kind of X100 large-deformation-resistance pipeline steel and manufacturing process thereof; 2) Chinese patent, Application Number (patent): CN201210327206.6, resistance to deformation X80-X100 Pipeline Steel Plate and manufacture method thereof; 3) Chinese patent, Application Number (patent): CN200810234506.3, the high strength X 100 pipeline steel that a kind of Steckel mill is produced and production technique thereof; 4) Chinese patent, Application Number (patent): CN201210039663.5, high-strength high-toughness X 100 pipeline steel hot-rolled steel strip and manufacture method thereof; 5) Chinese patent, Application Number (patent): CN201110282962.7, X100 Pipeline Steel Plate of a kind of excellent in low temperature toughness and preparation method thereof; 6) Chinese patent, Application Number (patent): CN200810012150.9, a kind of high strength X 100 pipeline steel hot rolled slab and production method thereof; 7) Chinese patent, Application Number (patent): CN201110062241.5, superhigh strength X 100 pipeline steel and production method thereof;
1 is only had in above patent documentation) and 2) be the pipe line steel with property of resisting large deformation, all the other are the X100 pipe line steels based on stress design, are organized as single bainite structure, intensity is high, and yield tensile ratio is higher, and unit elongation is lower, especially without the requirement of uniform elongation, poor stability; And 1) in S content maximum value be 0.004%, 2) in S content maximum value be 0.005%, P content maximum value 0.015%, 1) Charpy-V impact power lower limit 150J at the product performance-20 DEG C announced, 2) Charpy-V impact power lower limit 250J at the product performance-20 DEG C announced.
Summary of the invention
The object of this invention is to provide a kind of large diameter pipeline Chinese People's Anti-Japanese Military and Political College distortion X100 pipeline steel hot rolled steel plate, while it has high strength, there is excellent low-temperature flexibility, high arrest toughness and property of resisting large deformation, be applicable to the petroleum-gas pipeline engineering construction project that diameter is greater than 1016mm.
The present invention is achieved by the following technical solutions: a kind of heavy caliber petroleum natural gas line resistance to deformation X100 polyphase steel plate, and it is made up of component once by weight percentage: C:0.04 ~ 0.08%, Si:0.15 ~ 0.35%, Mn:1.60 ~ 2.00%, P≤0.008%, S≤0.003%, Nb:0.07 ~ 0.11%, Ti:0.015 ~ 0.025%, Mo≤0.25%, Cu≤0.35%, Ni≤0.030%, Cr≤0.030%, all the other are Fe and inevitable impurity.
The chemical composition of above-mentioned steel plate meets Pcm=C+Si/30+Ni/60+ (Mn+Cr+Cu)/20+Mo/15+V/10+5B≤0.20%.
In its Composition Design, the effect of each element is as follows:
C: carbon is that improving intensity main is also the most cheap element, along with the increase of carbon content, the intensity of steel increases, but the welding property of steel plate and plasticity and toughness are deteriorated simultaneously, therefore the present invention selects low-carbon (LC) Composition Design, makes steel plate have good plasticity and toughness and excellent welding property.
Mn: manganese is the effective element improving intensity and toughness, and it is weak carbide forming element, its effect in smelting is deoxidation and the impact eliminating sulphur, can also reduce austenite transformation temperature, fining ferrite grains, to raising armor plate strength and toughness useful.Simultaneously can also solution strengthening ferrite and the hardening capacity increasing steel.Under low-carbon (LC) condition, it has significant promoter action to bainite transformation.But during Mn too high levels, then hardening of steel and ductility degenerates.Mn, because of its successful, with low costly becomes one of main Addition ofelements in quality plate is produced.
Si: silicon plays the effect of reductor, has solution strengthening effect simultaneously, can also delay the formation of carbide greatly, growing up of delayed cementite, adds stabilization of austenite.But Si content is high, and steel grade easily occurs inclusion, and steel easily get rusty, in hot rolling production, iron rust is easily rolled into steel plate top layer, pot galvanize poor performance, and Si demonstrates local brittle zones when welding multithreading simultaneously hazardness.
Cu: the precipitation strength of copper is the important means of the intensity improving steel, in addition, Cu to the solidity to corrosion of steel, improve weldability, low-temperature flexibility, formability and machinability etc. and be all highly profitable.But on the other hand, easily crack when continuous casting steel billet heating or hot rolling during Cu content height, worsen surface of steel plate performance, appropriate Ni must be added to stop the generation of this crackle according to the difference of intensity rank and steel plate thickness.
Ni: nickel does not have detrimentally affect to welded heat affecting zone hardening and toughness, can make again the intensity of mother metal improve, and low-temperature flexibility is improved greatly.But it is comparatively noble element, causes the cost of steel significantly to rise, less economical.The object of adding Ni element in steel mainly stop containing Cu measure high steel billet heat or hot rolling time the tendency that cracks.According to the content of Cu, Ni content is controlled 0.7-1 times at Cu content.
Ti: the titanium adding trace is in order to the nitrogen element in fixing steel.Ti has strong precipitation strength effect in addition, the intensity of steel can be improved, also the influence had the hardness at welded heat affecting zone place in the best condition, the existence of the nitride particles of Ti can suppress the grain coarsening of welded heat affecting zone to stop steel billet the growing up of crystal grain in heating, rolling, welding process, improves the toughness of mother metal and welded heat affecting zone.Ti lower than 0.005% time, Gu N weak effect, during more than 0.03%, Gu N effect reaches capacity, superfluous Ti separately or can form carbonitride together with Nb, strengthens steel, but forms the precipitated phase of bulk sometimes, will make the toughness deteriorate of steel.When the ratio of the Ti in steel, atom N is 1:1, the most tiny and distribution disperse of TiN particle, the strongest to the refining effect of high temperature austenite crystal grain, not only can obtain excellent toughness, and the Large Heat Input Welding of more than 30KJ/cm can be realized.But too much Ti content can cause the alligatoring of the nitride of titanium, unfavorable to low-temperature flexibility.Therefore, generally by Ti Composition Control about 0.02%.
Mo: improve the hardening capacity of steel to improve the intensity of mother metal, while can improve the solidity to corrosion of steel plate with the element acting in conjunction such as Cu, Ni.Mo belongs to the element reducing austenite phase field, in the sosoloid that it is present in steel and carbide, has solution strengthening effect.In Carbide Phases, when Mo content is lower, form the cementite of compound with iron and carbon, when the content is higher, then form its alloy carbide.The velocity of diffusion of Mo is much smaller than the velocity of diffusion of C.Therefore, it can slow down the dissolution rate of carbide in austenite at steel grade, be that pearlitic transformation has strong restraining effect to steel by austenite decomposition, but it is then insignificant on the impact of the velocity of transformation by austenite decomposition being bainite, by austenite decomposition, ferritic speed is separated out to hypoeutectoid steel and also has restraining effect, be therefore conducive to obtaining bainitic steel.Consider according to performance requriements and economic factors, the Mo added generally is no more than 0.3%.
Cr: the interpolation of chromium can reduce the transformation temperature of steel grade, thinning microstructure, effectively improves intensity, can also improve steel grade oxidation-resistance and high temperature corrosion-resisting performance etc., but Cr crosses and separates out thick at most, causes the embrittlement of steel, bad to welding property, therefore Cr content be designed to≤0.30%.
The manufacture method of above-mentioned a kind of heavy caliber petroleum natural gas line resistance to deformation X100 polyphase steel plate comprises the steps: that proportioning is got the raw materials ready, molten iron KR desulfurization process, converter smelting, CAS Argon, the refining of LF+RH duplex practice, sheet billet continuous casting, slab reheat, two-stage control rolling, pre-straightening, the cooling of control multipath, the operation such as aligning, stacking slow cooling, UT (Ultrasonic Testing).
Molten steel sulfur content≤0.004%, converter smelting endpoint C≤0.04% after above-mentioned molten iron KR desulfurization process, P≤0.007%, after CAS carries out Al deoxidation, [O] reaches 25-30ppm, and LF adds Nb, adds the process of Ti, SiCa line, nodularization inclusion morphology in RH.
Smelting steel process of the present invention controls alloying element addition sequence: after converter, carry out deoxidation treatment, and during deoxidation, AL add-on is abundant, and a deoxidation is abundant, aluminum shot deoxidation is added in the LF later stage, then add Ti iron, and control to add Ti content according to N content in steel, Ti/N ratio controls at 2.0-3.4.The proportioning forming Ti/N=2.0 ~ 3.4 when smelting is utilized to generate tiny TiN particle at high operating temperatures, in During Controlled Rolling thereafter, the stability of TiN ensures TiN evenly tiny in steel plate, during control Plate Welding, crystal grain is thick, improves the welding property of steel plate.
Smelting steel process is by adding Ca process, and nodularization inclusion morphology, achieves the smelting of Clean Steel, has purified steel.
Upper sheet billet continuous casting adopts dynamic soft reduction technology; Described slab reheats in operation, slab heating temperature 1100 DEG C ~ 1200 DEG C.Low-carbon (LC) is added to the pipe line steel of niobium titanium compound, reheats temperature more than 1200 DEG C, the serious alligatoring of tissue can be made, cause final microstructure coarsening, to raising intensity and toughness unfavorable, and Heating temperature is too high, waste resource and the energy;
In above-mentioned two-stage control rolling process, divide recrystallization zone controlled rolling and two stages of Unhydrated cement controlled rolling, recrystallization zone controlled rolling: start rolling temperature 1050 DEG C, stop rolling temperature 1000 DEG C, last percentage pass reduction >=20%, accumulative draft is greater than 55%; Unhydrated cement controlled rolling: start rolling temperature 850 DEG C ~ 950 DEG C, stop rolling temperature 730 DEG C ~ 850 DEG C, accumulative draft is greater than 50%.
Above-mentioned multipath cooling controls in operation, and adopt " air cooling+pre-straightening+MULPIC cools fast ", air cooling 20 ~ 60s, cooling rate controls at 1 ~ 3 DEG C/s; MULPIC cools fast, speed of cooling 15-35 DEG C/s, cooling termination temperature 200 ~ 500 DEG C.Steel plate stacking slow cooling after cooling, carries out self-tempering and removes internal stress.
In above-mentioned stacking slow cooling operation, steel plate to roll off the production line fast stacking slow cooling after aligning, and the slow cooling time is 24 hours, and slow cooling starts temperature > 200 DEG C.
The method is on the basis of Composition Design, by controlling slab heating temperature and heat-up time, adopt two-stage control rolling+multipath process for cooling, the regulation and control of heterogeneous micro organization are carried out to steel plate, obtain the hot-rolled steel sheet with good obdurability and property of resisting large deformation.
Of the present invention effective: P content maximum value 0.010% in Composition Design in the present invention, S content maximum value 0.003%, steel is purer, high niobium Composition Design, to the grain refining of steel plate and strength-enhancing effect comparatively outstanding, steel plate is saved Mo, adding of the noble metals such as Ni, cost is lower, energy-conserving and environment-protective, meet Materials direction, be easier to produce and promote, the yield strength 690-760MPa of steel plate of the present invention, tensile strength 870-920MPa, uniform elongation >=10%, yield tensile ratio≤0.78,-20 DEG C of Charpy-V impact power >=300J,-15 DEG C of drop weight tearing experiment shear area >=85%.
Accompanying drawing explanation
Fig. 1 is the HOP technique of JFE in background technology;
Fig. 2 is the microtexture picture of resistance to deformation X100 polyphase steel plate in embodiment 2;
Fig. 3 is the microtexture picture of resistance to deformation X100 polyphase steel plate in embodiment 3.
Embodiment
Below in conjunction with the drawings and specific embodiments, technical scheme of the present invention is described further, so that those skilled in the art better can understand the present invention, but does not therefore limit the present invention.
Steel plate preparation method of the present invention comprises technique: proportioning is got the raw materials ready, molten iron KR desulfurization process, converter smelting, CAS Argon, the refining of LF+RH duplex practice, sheet billet continuous casting, slab reheat, two-stage control rolling, pre-straightening, the cooling of control multipath, the operation such as aligning, stacking slow cooling, UT (Ultrasonic Testing).
Embodiment 1
The Composition Design of the resistance to deformation X100 Wide and Heavy Plates that this embodiment relates to is in table 1:
Its preparation method design parameter is:
Molten steel sulfur content≤0.004%, converter smelting endpoint C≤0.04% after molten iron KR desulfurization process, P≤0.007%, after CAS carries out Al deoxidation, [O] reaches 28ppm, and LF adds Nb, adds the process of Ti, SiCa line, nodularization inclusion morphology in RH.
Smelting steel process of the present invention controls alloying element addition sequence: after converter, carry out deoxidation treatment, and during deoxidation, AL add-on is abundant, and a deoxidation is abundant, aluminum shot deoxidation is added in the LF later stage, then add Ti iron, and control to add Ti content according to N content in steel, Ti/N ratio controls 2.6.
Sheet billet continuous casting adopts dynamic soft reduction technology; Described slab reheats in operation, slab heating temperature 1120 DEG C.State in two-stage control rolling process, divide recrystallization zone controlled rolling and two stages of Unhydrated cement controlled rolling, recrystallization zone controlled rolling: start rolling temperature 1050 DEG C, stop rolling temperature 1000 DEG C, last percentage pass reduction >=20%, accumulative draft is greater than 55%; Unhydrated cement controlled rolling: start rolling temperature 880 DEG C, stop rolling temperature 760 DEG C, accumulative draft is greater than 50%.
Stating multipath cooling controls in operation, and adopt " air cooling+pre-straightening+MULPIC cools fast ", air cooling 40s, cooling rate controls at 2 DEG C/s; MULPIC cools fast, speed of cooling 20 DEG C/s, cooling termination temperature 240 DEG C.Steel plate stacking slow cooling after cooling, carries out self-tempering and removes internal stress.
State in stacking slow cooling operation, steel plate to roll off the production line fast stacking slow cooling after aligning, and the slow cooling time is 24 hours, and slow cooling starts temperature > 210 DEG C.
Carry out Performance Detection to steel plate, detected result is in table 2.
Embodiment 2
The Composition Design of the resistance to deformation X100 Wide and Heavy Plates that this embodiment relates to is in table 1:
Its preparation method design parameter is:
Molten steel sulfur content≤0.004%, converter smelting endpoint C≤0.04% after molten iron KR desulfurization process, P≤0.007%, after CAS carries out Al deoxidation, [O] reaches 30ppm, and LF adds Nb, adds the process of Ti, SiCa line, nodularization inclusion morphology in RH.
Smelting steel process of the present invention controls alloying element addition sequence: after converter, carry out deoxidation treatment, and during deoxidation, AL add-on is abundant, and a deoxidation is abundant, aluminum shot deoxidation is added in the LF later stage, then add Ti iron, and control to add Ti content according to N content in steel, Ti/N ratio controls 2.8.
Sheet billet continuous casting adopts dynamic soft reduction technology; Described slab reheats in operation, slab heating temperature 1140 DEG C.State in two-stage control rolling process, divide recrystallization zone controlled rolling and two stages of Unhydrated cement controlled rolling, recrystallization zone controlled rolling: start rolling temperature 1050 DEG C, stop rolling temperature 1000 DEG C, last percentage pass reduction >=20%, accumulative draft is greater than 55%; Unhydrated cement controlled rolling: start rolling temperature 910 DEG C, stop rolling temperature 820 DEG C, accumulative draft is greater than 50%.
Stating multipath cooling controls in operation, and adopt " air cooling+pre-straightening+MULPIC cools fast ", air cooling 40s, cooling rate controls at 2 DEG C/s; MULPIC cools fast, speed of cooling 25 DEG C/s, cooling termination temperature 380 DEG C.Steel plate stacking slow cooling after cooling, carries out self-tempering and removes internal stress.
State in stacking slow cooling operation, steel plate to roll off the production line fast stacking slow cooling after aligning, and the slow cooling time is 24 hours, and slow cooling starts temperature > 240 DEG C.
Carry out Performance Detection to steel plate, detected result is in table 2.
Embodiment 3
The Composition Design of the resistance to deformation X100 Wide and Heavy Plates that this embodiment relates to is in table 1:
Its preparation method design parameter is:
Molten steel sulfur content≤0.004%, converter smelting endpoint C≤0.04% after molten iron KR desulfurization process, P≤0.007%, after CAS carries out Al deoxidation, [O] reaches 25ppm, and LF adds Nb, adds the process of Ti, SiCa line, nodularization inclusion morphology in RH.
Smelting steel process of the present invention controls alloying element addition sequence: after converter, carry out deoxidation treatment, and during deoxidation, AL add-on is abundant, and a deoxidation is abundant, aluminum shot deoxidation is added in the LF later stage, then add Ti iron, and control to add Ti content according to N content in steel, Ti/N ratio controls 2.0.
Sheet billet continuous casting adopts dynamic soft reduction technology; Described slab reheats in operation, slab heating temperature 1120 DEG C.State in two-stage control rolling process, divide recrystallization zone controlled rolling and two stages of Unhydrated cement controlled rolling, recrystallization zone controlled rolling: start rolling temperature 1050 DEG C, stop rolling temperature 1000 DEG C, last percentage pass reduction >=20%, accumulative draft is greater than 55%; Unhydrated cement controlled rolling: start rolling temperature 900 DEG C, stop rolling temperature 800 DEG C, accumulative draft is greater than 50%.
Stating multipath cooling controls in operation, and adopt " air cooling+pre-straightening+MULPIC cools fast ", air cooling 40s, cooling rate controls at 2 DEG C/s; MULPIC cools fast, speed of cooling 25 DEG C/s, cooling termination temperature 250 DEG C.Steel plate stacking slow cooling after cooling, carries out self-tempering and removes internal stress.
State in stacking slow cooling operation, steel plate to roll off the production line fast stacking slow cooling after aligning, and the slow cooling time is 24 hours, and slow cooling starts temperature > 210 DEG C.
Carry out Performance Detection to steel plate, detected result is in table 2.
Table 1 large diameter pipeline resistance to deformation 100 polyphase steel plate chemical composition example (wt%)
The performance perameter of each embodiment light plate of table 2
Claims (1)
1. large diameter pipeline is out of shape a manufacture method for heterogeneous X100 High Strength Steel Plate with the Chinese People's Anti-Japanese Military and Political College, and described large diameter pipeline is out of shape heterogeneous X100 High Strength Steel Plate with the Chinese People's Anti-Japanese Military and Political College and is made up of following component by weight percentage: C:0.05%, Si:0.25%, Mn:1.91%, P:0.007%, S:0.001%, Nb:0.1%, Ti:0.018%, Mo:0.18%, Al:0.035%, Ni:0.22%, Cr:0.2%, all the other are Fe and inevitable impurity;
Processing step comprises that proportioning is got the raw materials ready, molten iron KR desulfurization process, converter smelting, CAS Argon, the refining of LF+RH duplex practice, sheet billet continuous casting, slab reheat, two-stage control rolling, pre-straightening, the cooling of control multipath, aligning, stacking slow cooling, UT (Ultrasonic Testing) operation;
Manufacture method is, molten steel sulfur content≤0.004%, converter smelting endpoint C≤0.04% after molten iron KR desulfurization process, P≤0.007%, after CAS carries out Al deoxidation, [O] reaches 28ppm, and LF adds Nb, the process of Ti, SiCa line is added, nodularization inclusion morphology in RH;
After converter, carry out deoxidation treatment, during deoxidation, Al add-on is abundant, and a deoxidation is abundant, adds aluminum shot deoxidation, then add Ti iron in the LF later stage, and controls to add Ti content according to N content in steel, and Ti/N ratio controls 2.6;
Sheet billet continuous casting adopts dynamic soft reduction technology, and described slab reheats in operation, slab heating temperature 1120 DEG C; In two-stage control rolling process, divide recrystallization zone controlled rolling and two stages of Unhydrated cement controlled rolling, recrystallization zone controlled rolling: start rolling temperature 1050 DEG C, stop rolling temperature 1000 DEG C, last percentage pass reduction >=20%, accumulative draft is greater than 55%; Unhydrated cement controlled rolling: start rolling temperature 880 DEG C, stop rolling temperature 760 DEG C, accumulative draft is greater than 50%; Multipath cooling controls in operation, and adopt " air cooling+pre-straightening+MULPIC cools fast ", air cooling 40s, cooling rate controls at 2 DEG C/s; MULPIC cools fast, speed of cooling 20 DEG C/s, cooling termination temperature 240 DEG C, steel plate stacking slow cooling after cooling, carries out self-tempering and removes internal stress; In stacking slow cooling operation, steel plate to roll off the production line fast stacking slow cooling after aligning, and the slow cooling time is 24 hours, and slow cooling starts temperature > 210 DEG C.
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Families Citing this family (8)
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| CN104532155B (en) * | 2014-12-19 | 2017-02-22 | 山东钢铁股份有限公司 | X90 level heterogeneous structure pipeline steel for longitudinal welded pipe |
| CN104388837A (en) * | 2014-12-19 | 2015-03-04 | 山东钢铁股份有限公司 | Acid-corrosion-resistant X70 pipeline steel plate and manufacturing method thereof |
| CN104998901A (en) * | 2015-08-10 | 2015-10-28 | 首钢总公司 | Hot rolling technology for pipeline rolled steel plate |
| CN105200336A (en) * | 2015-10-16 | 2015-12-30 | 首钢总公司 | Strain design region based high-performance pipeline steel with high-deformation resistance and preparation method |
| CN105886924B (en) * | 2016-04-28 | 2017-06-06 | 山东钢铁股份有限公司 | A kind of low-alloy steel of high-strength tenacity energy and preparation method thereof |
| US11773460B2 (en) * | 2018-04-09 | 2023-10-03 | Nippon Steel Corporation | Steel pipe and method for producing steel pipe |
| CN109897928B (en) * | 2019-03-25 | 2021-01-05 | 江阴兴澄特种钢铁有限公司 | Manufacturing method for producing large-thickness steel plate with core part anti-lamellar tearing performance by continuous casting billet |
Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1986861A (en) * | 2005-12-22 | 2007-06-27 | 宝山钢铁股份有限公司 | Superhigh strength X100 pipeline steel and its hot rolled plate making process |
| JP2008274405A (en) * | 2007-03-30 | 2008-11-13 | Jfe Steel Kk | High-strength steel sheet excellent in sr resistant property and deformation performance, and method for manufacturing the same |
| CN101994067A (en) * | 2009-08-10 | 2011-03-30 | 鞍钢股份有限公司 | High-strength pipe steel and production method thereof |
| CN102465235A (en) * | 2010-11-11 | 2012-05-23 | 北京科技大学 | X100 large deformation resistant pipeline steel and manufacturing process thereof |
| CN102644037A (en) * | 2012-05-16 | 2012-08-22 | 湖南华菱湘潭钢铁有限公司 | Production method of pipeline steel |
-
2013
- 2013-09-22 CN CN201310433278.3A patent/CN103510003B/en not_active Expired - Fee Related
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN1986861A (en) * | 2005-12-22 | 2007-06-27 | 宝山钢铁股份有限公司 | Superhigh strength X100 pipeline steel and its hot rolled plate making process |
| JP2008274405A (en) * | 2007-03-30 | 2008-11-13 | Jfe Steel Kk | High-strength steel sheet excellent in sr resistant property and deformation performance, and method for manufacturing the same |
| CN101994067A (en) * | 2009-08-10 | 2011-03-30 | 鞍钢股份有限公司 | High-strength pipe steel and production method thereof |
| CN102465235A (en) * | 2010-11-11 | 2012-05-23 | 北京科技大学 | X100 large deformation resistant pipeline steel and manufacturing process thereof |
| CN102644037A (en) * | 2012-05-16 | 2012-08-22 | 湖南华菱湘潭钢铁有限公司 | Production method of pipeline steel |
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