CN105803327A - Economic HIC-resistant X90 pipeline steel plate and manufacturing method thereof - Google Patents
Economic HIC-resistant X90 pipeline steel plate and manufacturing method thereof Download PDFInfo
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Abstract
The invention discloses an economic HIC-resistant X90 pipeline steel plate. The steel plate comprises the following chemical components by mass percent: 0.02 to 0.06% of C, 1.7 to 1.90% of Mn, 0.15 to 0.35% of Si, 0.0005% of less of S, 0.010% of less of P, 0.04 to 0.07% of Nb, 0.008 to 0.03% of Ti, 0.10% or less of V, 0.06% of less of Al, 0.010% or less of N, 0.006% or less of O, 0.20% of less of Mo, 0.20% or less of Cu, 0.20% or less of Ni, 0.20% or less of Cr and 0.0005 to 0.0015% of Ca, and the balance being Fe and unavoidable impurity elements, wherein the ratio of the content of Ca to the content of S is 1.0 to 2.0. According to the economic HIC-resistant X90 pipeline steel plate, the improved technology of refining, continuous casting, high temperature reheating and TMCP is adopted according to the behavioral rule of hydrogen in structures, so that the steel has an excellent structure resisting HIC and has excellent low-temperature toughness.
Description
Technical field
The invention belongs to X90 pipeline steel manufacturing technology field, be specifically related to economical hic resistance X90 pipeline steel and manufacture method thereof.
Background technology
In the energy of current world demand, fossil energy also accounts for the principal status of public economy in energy resource structure, in recent years World Economics increase the growth rapidly greatly having driven fossil energy demand rapidly.The resources such as land and alkalescence petroleum gas have exploited a century, face day by day exhausted.Therefore the mankind turn one's attention to acid petroleum gas region gradually, and the characteristic in acid-soluble oil gas field is containing certain H in oil or natural gas2The sour gas such as S, cause corrosion to conveyance conduit, and its forms of corrosion mainly has HIC(hydrogen induced cracking) and SSCC(stress corrosion) two ways, the most Hi-grade steel of current hic resistance and the application of anti-SSCC pipe line steel is at X65 grade of steel.For reducing pipe-line construction cost, the developing direction of pipeline engineering is high intensity Large Diameter Pipeline, has started to carry out the test section of X90 grade of steel pipe laying at present both at home and abroad, but X90 grade of steel hic resistance steel plate or steel pipe yet there are no and report for work.
Summary of the invention
The technical problem to be solved is the X90 Pipeline Steel Plate and the manufacture method that provide a kind of economical hic resistance for above-mentioned prior art, employing low-carbon (LC) designs, the micro alloying elements such as Nb, V, Ti of being simultaneously introduced trace, and add the elements such as a small amount of Mo, Cu, Ni, according to H Behavior law in the tissue, by refine+continuous casting+TMCP improved process, utilize organizational controls technology, make steel have tissue and the performance of excellent Properties of HIC resistance.
nullThis invention address that the technical scheme that above-mentioned technical problem adopts is，A kind of X90 Pipeline Steel Plate of economical hic resistance，The chemical composition of this steel plate is C:0.02～0.06% by mass percentage，Mn:1.7～1.90%，Si:0.15～0.35%，S :≤0.0005%，P :≤0.010%，Nb:0.04～0.07%，Ti:0.008～0.03%，V :≤0.10%，Al :≤0.06%，N :≤0.010%，O :≤0.006%，Mo :≤0.20%，Cu :≤0.20%，Ni :≤0.20%，Cr≤0.20%，Ca:0.0005～0.0015%，And the content ratio of Ca/S is 1.0～2.0，Surplus is Fe and inevitable impurity element.
Further, the most thickness specification of the hic resistance steel plate of the present invention is at 20mm.There is the high intensity high/low temperature toughness of excellence simultaneously, if yield tensile ratio is about 300J not higher than 0.83 ,-46 DEG C of low-temperature impact；-60 DEG C of low-temperature impacts are at about 250J；-30 DEG C are dropped hammer the section of shear more than 85%, and obtain the Properties of HIC resistance of excellence..
The chemical composition of steel plate of the present invention is determined such that
C: be intensified element most economical, most basic in steel, the intensity of steel can be significantly improved by solution strengthening and precipitation strength, but the toughness of steel and ductility and welding performance are brought adverse effect, therefore the development trend of pipe line steel is constantly to reduce C content, HIC is very sensitive to C content in steel, consider that grade of steel of the present invention reaches X90, and by relations such as the C solid solution from different microalloy elements formation carbonitride and precipitations, therefore C content in steel is controlled 0.02～0.06%.
Mn: improved the intensity of steel by solution strengthening, it it is the topmost element making up in pipe line steel and causing loss of strength because C content reduces, Mn still expands the element of γ phase region simultaneously, γ → α phase transition temperature of steel can be reduced, contribute to obtaining tiny phase-change product, the toughness of steel can be improved, but too high Mn content can cause Mn segregation, X90 rank has been reached in view of grade of steel, certain Mn content is necessary, therefore alleviate Mn segregation only by subsequent heating process and rolling mill practice, therefore Mn content is controlled 1.7～1.90%.
Nb: be one of topmost micro alloying element in modern micro alloyed steel particularly pipe line steel, to the effect of grain refinement clearly.By the Nb(C in the solid solution towing of Nb and course of hot rolling, N) strain induced precipitate can hinder the recovery and recrystallization of deformed austeaite, the deformed austeaite that Unhydrated cement rolls is made to be changed into tiny phase-change product when phase transformation through TMCP, so that steel has high intensity and high tenacity, the present invention determines Nb content range mainly by the relation of C and Nb equal size.
V: there is higher precipitation strength and more weak Grain Refinement Effect, when in tri-kinds of micro alloying elements of Nb, V, Ti, compound is on probation, V its precipitation strength effect main.
Ti: be strong solid N element, the stoichiometric proportion of Ti/N is 3.42, the Ti utilizing about 0.02% just can fix the N of below 60ppm in steel, sheet billet continuous casting process can be formed TiN precipitated phase, this tiny precipitated phase can effectively stop slab the growing up of austenite crystal in heating process, it is favorably improved Nb solid solubility in austenite, the impact flexibility of welding heat affected zone can be improved simultaneously, be indispensable element in pipe line steel.
Mo: first precipitate out the formation of ferritic phase when can postpone γ → α phase transformation, promotes the essential element that acicular ferrite is formed, and plays an important role to controlling phase transformation, also it is the quenching degree element improving steel simultaneously.Obvious acicular ferrite or bainite structure can be obtained by the certain Mo of interpolation under certain rate of cooling and final cooling temperature.
S, P: be inevitable impurity element in pipe line steel, it is desirable to more low more good, processed by super-low sulfur and Ca and change oxide morphology, thus improving the Properties of HIC resistance of steel.
Cu, Ni: can passing through solution strengthening and improve the intensity of steel, Ni adds the toughness that can improve steel on the one hand, separately improves the Cu red brittleness easily caused in steel simultaneously.The addition of Cu can improve the intensity of steel, but Cu is to hic resistance limited capacity under sour environment.
The addition of Cr:Cr can improve the quenching degree of steel, and simultaneously certain Cr content can improve Properties of HIC resistance.
It is a further object of the present invention to provide the manufacture method of the X90 Pipeline Steel Plate of above-mentioned economical hic resistance, concrete technology step is as follows:
First by raw materials for metallurgy successively through KR molten iron pretreatment, converter smelting, LF refine, RH vacuum refining, refining process controls S content≤0.0005% in molten steel, feeding Ca-Si line subsequently, controlling the content ratio of Ca/S in molten steel is 1.0～2.0, and then continuous casting goes out to meet chemical composition requirement, thickness is the continuous casting billet being not less than 350mm, and during continuous casting, the degree of superheat of molten steel is not higher than 15 DEG C；Continuous casting billet is again heated to 1280～1310 DEG C, and insulation is not less than 8 hours；Two-phase control rolling is carried out: overall compression ratio is not less than the ratio of 15(and sotck thinkness and finished product thickness) after coming out of the stove；Rolling in two stages, the first stage is recrystallization zone rolling, and finishing temperature control is at 1180～1210 DEG C, and the single pass reduction ratio controlling continuous two passages during recrystallization zone rolling is not less than 28%；After first stage rolling terminates, adopt intermediate blank appropriateness cooling system cooling intermediate blank.Intermediate blank cooling adopts Mildcooling cooling system (intermediate blank appropriateness cooling system), after recrystallization zone has rolled, intermediate blank immediately enters intermediate blank appropriateness cooling system, and intermediate blank is comparatively fast cooled to the second stage start rolling temperature needed by appropriateness cooling.After intermediate blank enters mildcooling system, blank adopts the mode that swings back and forth appropriateness cooling in intermediate blank appropriateness cooling system, makes rate of cooling control at 9～13 DEG C/s.Second stage is the rolling of non-recrystallization zone, and start rolling temperature is not higher than 900 DEG C, until final thickness, finishing temperature control is not higher than 830 DEG C, and the accumulative deformation rate in non-recrystallization zone is not less than 60%；Cooled down by ACC subsequently, terminate chilling temperature not higher than 500 DEG C；Rate of cooling is 15～25 DEG C/s；It is cooled to room temperature afterwards and namely obtains steel plate finished product.
The present invention by arranging the cooling of intermediate blank appropriateness between hot rolling first stage and second stage, after this intermediate blank type of cooling is to ensure that recrystallization zone rolling deformation, austenite crystal is no longer grown up, in big thickness steel plate course of hot rolling, reduce intermediate blank surface and the heart portion temperature difference.As it is shown on figure 3, intermediate blank appropriateness cooling system is arranged between roughing mill and the finishing mill of 4300mm wide and heavy plate mill production line.This system is body structure, amount to long 18m, at casing top, dense distribution spray spout, intermediate blank after roughing is carried out appropriateness cooling, according to different workpiece thickness, it is thus achieved that intermediate blank rate of cooling be 4～18 DEG C/s, workpiece thickness is according to product and produces needs, generally about 40～180mm thickness, less than 40mm thickness intermediate blank due to relatively thin, unless needed for, generally do not need to carry out intermediate blank cooling.For think gauge intermediate blank, it is contemplated that design limit, maximum rate of cooling is at 4 DEG C/s, and for Thin Specs, maximum rate of cooling can reach 18 DEG C/s.Why can not adopt higher cooling rate, two factors are had to need to consider: one is due under higher cooling rate, intermediate blank through-thickness can produce bigger temperature difference, this temperature difference causes Deformation in thickness uneven when rolling due to temperature difference, steel plate can be produced during finish rolling rolling to upwarp or lower button, affect productivity ratio；Two is that this through-thickness temperature difference will cause through-thickness region austenite deformation different, thus affecting the final tissue of acquisition.
Blank is after the first stage has rolled, according to producing needs, it may be judged whether open the cooling of intermediate blank appropriateness.When needing to adopt intermediate blank cooling system to carry out appropriateness cooling, intermediate blank is after entering intermediate blank appropriateness cooling system, in system, corresponding roller-way enters weave mode, intermediate blank is made to swing back and forth in system, intermediate blank is sprayed water by nozzle spray simultaneously, controls intermediate blank and is cooled to the start rolling temperature of second stage rolling with specific rate of cooling.
After the start rolling temperature that intermediate blank is cooled to second stage rolling, intermediate blank will be sent in intermediate blank appropriateness cooling system, enter later procedure.
Characteristic according to H atom or ion, the diffusion in steel is inevitable, and H enters after in steel can form H trap, and in some hydrogen trap, H will assemble in a large number, ultimately forms gross imperfection.This kind of hydrogen trap and different tissues, field trash type and pattern, different tissues interface are relevant.
For ensureing excellent Properties of HIC resistance, the degree of purity of steel is extremely important, wherein need to control as far as possible S content and S inclusion content and pattern in steel, S is controlled 0.0005% and following by the present invention, make MnS exist in nodularization mode by Ca process simultaneously, such MnS total amount in steel is little, and substantially by nodularization.Practice have shown that Ca/S ratio controls when 1～2, and MnS nodularization is complete, and now in steel, Ca content will not be excessive, because of without furnace lining is too corroded when in steel, S content is low to moderate 0.0005% and following.
Banded structure is one of major reason causing HIC.For pipe line steel X90 grade of steel, intensity is very high, is generally guarantee pipe line steel Properties of HIC resistance, and Mn content is all less than about 1.45%, in this low Mn situation, for guaranteeing X90 grade of steel intensity and Properties of HIC resistance, it is necessary to more alloy, thus being greatly increased cost.And the present invention is from cost consideration, then still adopt higher Mn to design, but technique, control Mn segregation formed, it may be assumed that 1) from continuous casting, adopt low overheat during cast, adopt slighter compress simultaneously, the original band in strand can be improved as far as possible；2) slab reheating temperature (than conventional pipeline steel heating-up temperature improve about 120 DEG C) it is greatly improved in follow-up reheating operation and extends rethermalization time, slowing down Mn segregation further；3) ensure that recrystallization also fully occurs in blank heart portion by roughing process high-temperature and continuous 3 passage roughing heavy reduction rates, thus eliminating the impact of blank original austenite；4) owing to roughing end temp is significantly high, it is necessary to carry out intermediate blank cooling by mildcooling intermediate blank appropriateness cooling system, thus preventing intermediate blank austenite crystal thick.That is original in steel and secondary banding particularly heart portion banded structure can be controlled by continuous casting+elevated heating processes and specific TMCP technique, thus ensure that the hic resistance energy that superhigh intensity X90 steel grade steel plate heart portion is excellent in low cost situation.
The present invention has a characteristic that 1) adopt the design of low-carbon (LC) higher Mn composition, and by controlling banded structure formed from continuous casting and subsequent heat and rolling, thus the hic resistance X90 steel grade steel plate of very economical can be obtained；2) adopting S≤0.0005% one-tenth divisional processing and control the ratio 1.0～2.0 of Ca/S, making MnS nodularization, in molten steel, Ca content is inexcessive, can be greatly reduced the Ca erosion to furnace lining, contributes to extending the service life of refining furnace, and reduces cost；3) adopt low overheat and slighter compress to carry out continuous casting, improve original band organization formation；4) adopt specific T MCP technique when follow-up heating of plate blank and rolling, it is thus achieved that specifically organize, formed by the secondary banded structure in specific T MCP technology controlling and process steel simultaneously, so that steel plate obtains excellent Properties of HIC resistance, and there is the low-temperature flexibility of excellence；3) adopt the design of this composition and technological design, the X90 Pipeline Steel Plate of 20mm thickness specification can be produced.
Accompanying drawing explanation
Fig. 1 is the organization chart of the embodiment of the present invention 1 light plate；
Fig. 2 is the hic resistance detection figure of embodiment of the present invention steel plate；
Fig. 3 is the operation sketch of intermediate blank appropriateness cooling system in the embodiment of the present invention.
Detailed description of the invention
Below in conjunction with accompanying drawing, embodiment, the present invention is described in further detail.
Embodiment 1
The thickness of the X90 Pipeline Steel Plate of the hic resistance of the present embodiment is 20mm, and its chemical composition is by mass percentage: C:0.06%, Mn:1.70%, Si:0.15%, S:0.0005%, P:0.01%, Nb:0.055%, Ti:0.018%, V :≤0.05%, Al:0.030%, Mo+Cu+Ni+Cr≤0.6%, N≤0.010%, O :≤0.006%, Ca:0.0008%, surplus is Fe and inevitable impurity element.
First by raw materials for metallurgy successively through KR molten iron pretreatment, converter smelting, LF refine, RH vacuum refining, refining process controls S content≤0.0005% in molten steel, feeding Ca-Si line subsequently, controlling the content ratio of Ca/S in molten steel is 1.0～2.0, and then continuous casting goes out to meet chemical composition requirement, thickness is the continuous casting billet being not less than 350mm, during continuous casting, the degree of superheat of molten steel is not higher than 15 DEG C, and carries out slighter compress；Overall compression ratio is 15, and continuous casting billet is again heated to 1280～1310 DEG C, and insulation is not less than 8 hours；Carrying out two-phase control rolling after coming out of the stove: the first stage is recrystallization zone rolling, finishing temperature control is at 1210 DEG C, and the single pass reduction ratio controlling continuous two passages during recrystallization zone rolling is not less than 28%；After first stage rolling terminates, intermediate blank immediately enters intermediate blank appropriateness cooling system, it is illustrated in figure 3 the operation sketch of intermediate blank appropriateness cooling system, intermediate blank is appropriateness cooling in the way of swinging back and forth in intermediate blank appropriateness cooling system, rate of cooling controls at 12 DEG C/s, cools down, by appropriateness, the second stage start rolling temperature that intermediate blank is comparatively fast cooled to need by technique；Second stage is the rolling of non-recrystallization zone, and start rolling temperature is not higher than 890 DEG C, until final thickness, finishing temperature is 820 DEG C, and the accumulative deformation rate in non-recrystallization zone is not less than 60%；Cooled down by ACC subsequently, terminate chilling temperature not higher than 420 DEG C；Rate of cooling is 18 DEG C/s；It is cooled to room temperature afterwards and namely obtains steel plate finished product.
Via the X90 pipeline steel thick for 20mm that above-mentioned manufacturing process prepares, excellent combination property, mechanical performance refers to table 1, and Properties of HIC resistance is in Table 2.
Embodiment 2
The thickness of the X90 Pipeline Steel Plate of the hic resistance of the present embodiment is 19.6mm, and its chemical composition is by mass percentage: C:0.04%, Mn:1.90%, Si:0.28%, S:0.0005%, P:0.01%, Nb:0.058%, Ti:0.018%, V :≤0.05%, Al:0.030%, Mo+Cu+Ni+Cr≤0.9%, N≤0.010%, O :≤0.006%, Ca:0.0008%, surplus is Fe and inevitable impurity element.
First by raw materials for metallurgy successively through KR molten iron pretreatment, converter smelting, LF refine, RH vacuum refining, refining process controls S content≤0.0005% in molten steel, feeding Ca-Si line subsequently, controlling the content ratio of Ca/S in molten steel is 1.0～2.0, and then continuous casting goes out to meet chemical composition requirement, thickness is the continuous casting billet of 300mm, during continuous casting, the degree of superheat of molten steel is not higher than 15 DEG C, and carries out slighter compress；Continuous casting billet is again heated to 1290～1300 DEG C, is incubated 8 hours；Overall compression ratio is 15.3, carries out two-phase control rolling after coming out of the stove: the first stage is recrystallization zone rolling, and finishing temperature control is at 1200 DEG C, and the single pass reduction ratio controlling continuous two passages during recrystallization zone rolling is not less than 28%；After first stage rolling terminates, intermediate blank immediately enters intermediate blank appropriateness cooling system, intermediate blank is appropriateness cooling in the way of swinging back and forth in intermediate blank appropriateness cooling system, rate of cooling controls at 10 DEG C/s, cools down, by appropriateness, the second stage start rolling temperature that intermediate blank is comparatively fast cooled to need by technique；Second stage is the rolling of non-recrystallization zone, and start rolling temperature is not higher than 890 DEG C, until final thickness, finishing temperature is 800 DEG C, and the accumulative deformation rate in non-recrystallization zone is not less than 60%；Cooled down by ACC subsequently, terminate chilling temperature not higher than 480 DEG C；Rate of cooling is 25 DEG C/s；It is cooled to room temperature afterwards and namely obtains steel plate finished product.
Via the X90 pipeline steel thick for 19.6mm that above-mentioned manufacturing process prepares, excellent combination property, mechanical performance refers to table 1, and Properties of HIC resistance is in Table 2.
Embodiment 3
The thickness of the X90 Pipeline Steel Plate of the hic resistance of the present embodiment is 20mm, and its chemical composition is by mass percentage: C:0.02%, Mn:1.85%, Si:0.35%, S:0.0005%, P:0.01%, Nb:0.058%, Ti:0.018%, V :≤0.05%, Al:0.030%, Mo+Cu+Ni+Cr≤0.9%, N≤0.010%, O :≤0.006%, Ca:0.0008%, surplus is Fe and inevitable impurity element.
First by raw materials for metallurgy successively through KR molten iron pretreatment, converter smelting, LF refine, RH vacuum refining, refining process controls S content≤0.0005% in molten steel, feeding Ca-Si line subsequently, controlling the content ratio of Ca/S in molten steel is 1.0～2.0, and then continuous casting goes out to meet chemical composition requirement, thickness is the continuous casting billet of 370mm, during continuous casting, the degree of superheat of molten steel is not higher than 15 DEG C, and carries out slighter compress；Continuous casting billet is again heated to 1280～1300 DEG C, is incubated 8 hours；Overall compression ratio is 18.5, carries out two-phase control rolling after coming out of the stove: the first stage is recrystallization zone rolling, and finishing temperature control is at 1180 DEG C, and the single pass reduction ratio controlling continuous two passages during recrystallization zone rolling is not less than 28%；After first stage rolling terminates, intermediate blank immediately enters intermediate blank appropriateness cooling system, intermediate blank is appropriateness cooling in the way of swinging back and forth in intermediate blank appropriateness cooling system, rate of cooling controls at 10 DEG C/s, cools down, by appropriateness, the second stage start rolling temperature that intermediate blank is comparatively fast cooled to need by technique；Second stage is the rolling of non-recrystallization zone, and start rolling temperature is not higher than 900 DEG C, until final thickness, finishing temperature is 800 DEG C, and the accumulative deformation rate in non-recrystallization zone is not less than 60%；Cooled down by ACC subsequently, terminate chilling temperature not higher than 400 DEG C；Rate of cooling is 15 DEG C/s；It is cooled to room temperature afterwards and namely obtains steel plate finished product.
Via the X90 pipeline steel thick for 20mm that above-mentioned manufacturing process prepares, excellent combination property, mechanical performance refers to table 1, and Properties of HIC resistance is in Table 2.
The mechanical performance of the steel plate that each embodiment of table 1 produces
The hic resistance of the produced steel plate of each embodiment of table 2 and anti-SSCC performance
Claims (4)
1. the X90 Pipeline Steel Plate of an economical hic resistance, the chemical composition of this steel plate is C:0.02～0.06% by mass percentage, Mn:1.7～1.90%, Si:0.15～0.35%, S :≤0.0005%, P :≤0.010%, Nb:0.04～0.07%, Ti:0.008～0.03%, V :≤0.10%, Al :≤0.06%, N :≤0.010%, O :≤0.006%, Mo :≤0.20%, Cu :≤0.20%, Ni :≤0.20%, Cr≤0.20%, Ca:0.0005～0.0015%, and the content ratio of Ca/S is 1.0～2.0, surplus is Fe and inevitable impurity element.
2. the method for the X90 Pipeline Steel Plate manufacturing economical hic resistance as claimed in claim 1, it is characterised in that: processing step is as follows:
By raw materials for metallurgy successively through KR molten iron pretreatment, converter smelting, LF refine, RH vacuum refining, refining process controls S content≤0.0005% in molten steel, feeding Ca-Si line subsequently, controlling the content ratio of Ca/S in molten steel is 1.0～2.0, and then continuous casting goes out to meet that chemical composition requires, thickness is not less than the continuous casting billet of 350mm, and during continuous casting, the degree of superheat of molten steel is not higher than 15 DEG C；
Continuous casting billet is again heated to 1280～1310 DEG C, and insulation is not less than 8 hours；Two-phase control rolling is carried out: the overall compression ratio of sotck thinkness and finished product thickness is not less than 15 after coming out of the stove；Rolling in two stages, the first stage is recrystallization zone rolling, and finishing temperature control is at 1180～1210 DEG C, and the single pass reduction ratio controlling continuous two passages during recrystallization zone rolling is not less than 28%；After first stage rolling terminates, intermediate blank immediately enters intermediate blank appropriateness cooling system, intermediate blank is appropriateness cooling in the way of swinging back and forth in intermediate blank appropriateness cooling system, rate of cooling controls at 9～13 DEG C/s, cools down, by appropriateness, the second stage start rolling temperature that intermediate blank is comparatively fast cooled to need by technique；Second stage is the rolling of non-recrystallization zone, and start rolling temperature is not higher than 900 DEG C, until final thickness, finishing temperature control is not higher than 830 DEG C, and the accumulative deformation rate in non-recrystallization zone is not less than 60%；Cooled down by ACC subsequently, terminate chilling temperature not higher than 500 DEG C；Rate of cooling is 15～25 DEG C/s；It is cooled to room temperature afterwards and namely obtains steel plate finished product.
3. the manufacture method of the X90 Pipeline Steel Plate of economical hic resistance according to claim 2, it is characterized in that: described intermediate blank appropriateness cooling system is arranged between roughing mill and the finishing mill of 4300mm wide and heavy plate mill production line, this system is body structure, amount to long 18m, at casing top, dense distribution spray spout, intermediate blank after roughing is carried out appropriateness cooling, according to different workpiece thickness, the intermediate blank rate of cooling obtained is 4～18 DEG C/s, workpiece thickness is according to product and produces needs generally about 40～180mm thickness, less than 40mm thickness intermediate blank due to relatively thin, unless needed for, general need carries out opening the cooling of intermediate blank appropriateness；For think gauge intermediate blank, it is contemplated that design limit, maximum rate of cooling is at 4 DEG C/s, and for Thin Specs, maximum rate of cooling can reach 18 DEG C/s.
4. the manufacture method of the X90 Pipeline Steel Plate of economical hic resistance according to claim 3, it is characterized in that: the work flow of described intermediate blank appropriateness cooling system: blank obtains intermediate blank after roughing completes, according to producing needs, judge whether to open the cooling of intermediate blank appropriateness, when needing to adopt intermediate blank cooling system to carry out appropriateness cooling, intermediate blank is after entering intermediate blank appropriateness cooling system, in system, corresponding roller-way enters weave mode, intermediate blank is made to swing back and forth in system, intermediate blank is sprayed water by nozzle spray simultaneously, control intermediate blank and be cooled to the start rolling temperature of second stage rolling with specific rate of cooling, after the start rolling temperature that intermediate blank is cooled to second stage rolling, intermediate blank will be sent in intermediate blank appropriateness cooling system, enter later procedure.
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| PCT/CN2016/102373 WO2017193537A1 (en) | 2016-05-13 | 2016-10-18 | Economical hic-resistant x90 pipeline steel plate and manufacturing method therefor |
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|---|---|---|---|---|
| CN107099744A (en) * | 2017-04-01 | 2017-08-29 | 江阴兴澄特种钢铁有限公司 | The X80 bend pipes Pipeline Steel Plate and its manufacture method of a kind of hic resistance |
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Citations (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR20010060763A (en) * | 1999-12-28 | 2001-07-07 | 이구택 | Method of manufacturing hot rolling steel sheet having high strength for linepipe |
| CN101376947A (en) * | 2007-08-28 | 2009-03-04 | 宝山钢铁股份有限公司 | High strength X90 pipeline steel and production method thereof |
| JP4276480B2 (en) * | 2003-06-24 | 2009-06-10 | 新日本製鐵株式会社 | Manufacturing method of high strength steel pipe for pipelines with excellent deformation performance |
| CN101642780A (en) * | 2009-06-05 | 2010-02-10 | 中冶赛迪工程技术股份有限公司 | Intermediate blank cooling system and cooling control technology |
| CN101886222A (en) * | 2010-07-05 | 2010-11-17 | 华油钢管有限公司 | Method for manufacturing high-strength X90 steel grade spiral submerged arc welded pipe |
| CN102397941A (en) * | 2011-11-14 | 2012-04-04 | 中国石油集团渤海石油装备制造有限公司 | Manufacturing method for X90 pipeline steel longitudinal submerged arc welding pipe |
| CN103243278A (en) * | 2013-05-10 | 2013-08-14 | 武汉钢铁(集团)公司 | X90 pipeline steel and production method thereof |
| CN103981461A (en) * | 2014-05-30 | 2014-08-13 | 秦皇岛首秦金属材料有限公司 | X90 pipeline steel wide and thick plate and production method thereof |
| CN104532155A (en) * | 2014-12-19 | 2015-04-22 | 山东钢铁股份有限公司 | X90 level heterogeneous structure pipeline steel plate for longitudinal welded pipe and manufacturing method of pipeline steel plate |
Family Cites Families (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP4254551B2 (en) * | 2003-07-31 | 2009-04-15 | Ｊｆｅスチール株式会社 | High strength steel plate for line pipe with excellent HIC resistance and method for producing the same |
| CN100398684C (en) * | 2005-12-22 | 2008-07-02 | 宝山钢铁股份有限公司 | Superhigh strength X100 pipeline steel and its hot rolled plate making process |
| JP5278188B2 (en) * | 2009-06-19 | 2013-09-04 | 新日鐵住金株式会社 | Thick steel plate with excellent resistance to hydrogen-induced cracking and brittle crack propagation |
| CN104805375B (en) * | 2015-04-02 | 2017-03-01 | 江阴兴澄特种钢铁有限公司 | A kind of ultra thick gauge high tenacity X80 pipeline steel and its manufacture method |
| CN104831182B (en) * | 2015-04-02 | 2017-03-01 | 江阴兴澄特种钢铁有限公司 | A kind of low yield strength ratio hic resistance and anti-SSCCX70 Pipeline Steel Plate and its manufacture method |
| CN105803327B (en) * | 2016-05-13 | 2018-02-23 | 江阴兴澄特种钢铁有限公司 | The X90 Pipeline Steel Plates and its manufacture method of a kind of economical hic resistance |
-
2016
- 2016-05-13 CN CN201610314574.5A patent/CN105803327B/en active Active
- 2016-10-18 WO PCT/CN2016/102373 patent/WO2017193537A1/en active Application Filing
Patent Citations (9)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| KR20010060763A (en) * | 1999-12-28 | 2001-07-07 | 이구택 | Method of manufacturing hot rolling steel sheet having high strength for linepipe |
| JP4276480B2 (en) * | 2003-06-24 | 2009-06-10 | 新日本製鐵株式会社 | Manufacturing method of high strength steel pipe for pipelines with excellent deformation performance |
| CN101376947A (en) * | 2007-08-28 | 2009-03-04 | 宝山钢铁股份有限公司 | High strength X90 pipeline steel and production method thereof |
| CN101642780A (en) * | 2009-06-05 | 2010-02-10 | 中冶赛迪工程技术股份有限公司 | Intermediate blank cooling system and cooling control technology |
| CN101886222A (en) * | 2010-07-05 | 2010-11-17 | 华油钢管有限公司 | Method for manufacturing high-strength X90 steel grade spiral submerged arc welded pipe |
| CN102397941A (en) * | 2011-11-14 | 2012-04-04 | 中国石油集团渤海石油装备制造有限公司 | Manufacturing method for X90 pipeline steel longitudinal submerged arc welding pipe |
| CN103243278A (en) * | 2013-05-10 | 2013-08-14 | 武汉钢铁(集团)公司 | X90 pipeline steel and production method thereof |
| CN103981461A (en) * | 2014-05-30 | 2014-08-13 | 秦皇岛首秦金属材料有限公司 | X90 pipeline steel wide and thick plate and production method thereof |
| CN104532155A (en) * | 2014-12-19 | 2015-04-22 | 山东钢铁股份有限公司 | X90 level heterogeneous structure pipeline steel plate for longitudinal welded pipe and manufacturing method of pipeline steel plate |
Cited By (14)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| WO2017193537A1 (en) * | 2016-05-13 | 2017-11-16 | 江阴兴澄特种钢铁有限公司 | Economical hic-resistant x90 pipeline steel plate and manufacturing method therefor |
| CN107099744A (en) * | 2017-04-01 | 2017-08-29 | 江阴兴澄特种钢铁有限公司 | The X80 bend pipes Pipeline Steel Plate and its manufacture method of a kind of hic resistance |
| CN107460407A (en) * | 2017-08-25 | 2017-12-12 | 中冶华天南京工程技术有限公司 | Rare earth reinforced long-distance transport pipes steel and preparation method and application |
| CN109055868A (en) * | 2018-10-10 | 2018-12-21 | 鞍钢股份有限公司 | Production method of X80 thick ultra-wide longitudinal submerged arc welding pipeline steel |
| CN109055868B (en) * | 2018-10-10 | 2020-02-18 | 鞍钢股份有限公司 | Production method of X80 thick ultra-wide longitudinal submerged arc welding pipeline steel |
| CN110284066B (en) * | 2019-07-24 | 2021-04-16 | 宝钢湛江钢铁有限公司 | Thin-gauge low-yield-ratio pipeline steel and manufacturing method thereof |
| CN110284066A (en) * | 2019-07-24 | 2019-09-27 | 宝钢湛江钢铁有限公司 | A kind of thin gauge low-yield ratio pipeline steel and its manufacturing method |
| WO2021218933A1 (en) * | 2020-04-27 | 2021-11-04 | 宝山钢铁股份有限公司 | Economical low-yield ratio and high-strength steel and manufacturing method therefor |
| CN111607750A (en) * | 2020-06-30 | 2020-09-01 | 武汉钢铁有限公司 | X90-grade high-strength pipeline steel plate coil with thickness of more than or equal to 20mm and manufacturing method thereof |
| WO2022001904A1 (en) * | 2020-06-30 | 2022-01-06 | 武汉钢铁有限公司 | X90-grade high-strength pipeline steel plate coil having thickness of ≥ 20 mm and manufacturing method therefor |
| CN112063918A (en) * | 2020-07-29 | 2020-12-11 | 江阴兴澄特种钢铁有限公司 | Pipeline steel plate for low-temperature high-toughness X90 steel grade hot-bending bend pipe and manufacturing method thereof |
| CN112680659A (en) * | 2020-12-04 | 2021-04-20 | 安阳钢铁股份有限公司 | Low-compression-ratio economical X70 pipeline steel and production method thereof |
| CN112680659B (en) * | 2020-12-04 | 2022-04-22 | 安阳钢铁股份有限公司 | Low-compression-ratio economical X70 pipeline steel and production method thereof |
| CN114411065A (en) * | 2021-12-08 | 2022-04-29 | 唐山中厚板材有限公司 | Large-size low-temperature-resistant high-strength angle steel and production method thereof |
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| WO2017193537A1 (en) | 2017-11-16 |
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