CN101845596A - Wide thick plate for X80 pipe line steel and manufacturing method thereof - Google Patents
Wide thick plate for X80 pipe line steel and manufacturing method thereof Download PDFInfo
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Abstract
The invention relates to a wide thick plate for X80 pipe line steel, which comprises the following chemical compositions in percentage by weight: more than or equal to 0.03 percent and less than or equal to 0.08 percent of C, more than or equal to 0.10 percent and less than or equal to 0.35 percent of Si, more than or equal to 1.65 percent and less than or equal to 2.30 percent of Mn, less than or equal to 0.015 percent of P, less than or equal to 0.050 percent of S, more than or equal to 0.010 percent and less than or equal to 0.35 percent of Ti, more than or equal to 0.20 percent and less than or equal to 0.60 percent of Cr, less than or equal to 0.14 percent of Mo, less than or equal to 0.30 percent of Cu, less than or equal to 0.20 percent of Ni, more than or equal to 0.01percent and less than or equal to 0.04 percent of Al, more than or equal to 0.001 percent and less than or equal to 0.004 percent of Ca, less than or equal to 0.008 percent of N, more than or equal to 0.051 percent and less than or equal to 0.110 percent of Nb, the balance of Fe and other unavoidable impurity elements. A manufacturing method of the wide thick plate for the X80 pipe line steel comprises a heating temperature of a hot-rolling process in the range of 1,100 to 1,200 DEG C, a rolling temperature of a recrystallization zone in the range of 1,170 to 940 DEG C, a rolling temperature of a non-recrystallization zone in the range of 910 to 740 DEG C, more than or equal to 3T (T represents a thickness of a finished product) of a finish rolling compression ratio, 15 DEG C per second of cooling speed and a final cooling temperature in the range of 400 to 600 DEG C. The steel plate can be used for producing a large-caliber high-pressure delivery longitudinal welded pipe.
Description
Technical field
The present invention relates to a kind of low alloy steel and manufacturing thereof, particularly a kind of X80 pipe line steel Wide and Thick Slab and method for manufacturing thereof.
Background technology
Pipe-line transportation is the safest, economic, the carrying method efficiently of oil and gas, therefore is widely used for a long time, and steel for pipe has also obtained continuous development.Early stage in last century, steel for pipe adopts the general carbon steel of C, Mn, Si type always, comprises the pipe line steel of X52 and the following grade of steel of X52.Begin from the sixties, increase along with transfer pressure and transfer lime caliber, oil transportation, tracheae material extensively adopt low-alloy high-strength steel, this steel grade adds a small amount of alloying element and a kind of High Strength Structural Steel of growing up on the basis of general carbon steel, mainly with the delivery of hot rolling or normalizing attitude, can obtain to have certain intensity, toughness, formability, weldability and erosion-resisting good over-all properties.Along with the requirements at the higher level of pipework to the pipe line steel proposition, at the end of the sixties, X56, X60, three kinds of grade of steels of X65 have been added among API 5LX and the API 5LS, these steel are broken through traditional composition design and processes control thinking, in steel, add alloying elements such as micro-Nb, V, Ti, adopt controlled rolling technology, make steel comprehensive mechanical property be improved significantly, from then on pipe line steel enters microalloying and adds the new stage that controlled rolling is produced.The beginning of the seventies is to the eighties, at Mn-Nb is that to develop Mn-Mo-Nb on the basis be the microalloying pipe line steel, the type pipe line steel adopts hot mechanical treatment (Thermo-Mechanical ControlProcessing, TMCP) technology, can obtain high strength and good low-temperature flexibility, be mainly used in the pipe line steel of making X70, X80 intensity rank, and finish practical application the X80 pipe line steel in nineteen ninety.Subsequently, pipe line steel X100, the X120 of higher category succeed in developing in succession, and have laid test section.
Put down in writing a kind of method that adopts hot rolling+thermal treatment process to make thick intensity high tenacity pipeline steel plate with a high standard among the disclosed Japanese patent application JP 2006307324A on November 9th, 2006 (contrast 1).And the present invention adopts TMCP technology, the processing route difference; In addition, the contrast patent has been added the B element and has been improved hardening capacity to improve the intensity of material in the composition design, and the present invention then adopts raising hardening capacity alloying elements such as Cr, Mo to improve the obdurability of steel plate.
Put down in writing a kind of manufacture method among the disclosed Japanese patent application JP 2003003229A on January 8th, 2003 (contrast 2) with good fatigue property, manufacturability, high-strength steel plate.Adopt the composition design method of higher C content, and adopt controlled rolling air cooling+heat treated manufacturing process, different with low-carbon microalloyed composition design of the present invention with the TMCP manufacturing process.
Put down in writing the manufacture method of a kind of high strength, even flexible natural gas transmission pipeline usefulness steel among the disclosed Japanese patent application JP 53118221 on October 16th, 1978 (contrast 3).The main composition design method that adopts C and alloying in this documents, and added higher Mo element (0.60%～2.00%), cost of alloy is higher; And the present invention's employing is the high Nb microalloying composition design method of base with C-Mn, and Mo content is limited in 0.14%, with the contrast patent bigger difference is arranged.
Put down in writing a kind of processing method that is used to make the steel plate of UOE welded tube among the disclosed Japanese Patent JP 2783820 on July 9 nineteen ninety (contrast 4), this steel plate is a main component with C, Si, Mn, P, S and Al, with Cu, Ni, Ca, Nb, Ti, V, Mo, Cr, B and REM is selection component, this method requires the finish rolling compression ratio greater than 50%, and air cooling is to (Ar after the controlled rolling
3-20)～(Ar
3-70) be cooled fast to design temperature after the temperature again, to make the steel plate that obtains to have good low-temperature toughness.The present invention then adopts directly fast cold technology after the controlled rolling, and is different with the processing route of this documents.
Put down in writing a kind of steel plate and rolling method thereof that is used to make subsea pipeline among the disclosed Chinese patent application CN101082108 on June 29th, 2006 (contrast 5).Different with this method is that the present invention has adopted higher Mn content to remedy the loss of strength of low-carbon (LC); Add higher Cr simultaneously to improve the hardening capacity of slab, improved the homogeneity of the performance of steel plate thickness direction; Add higher Nb element with refining grain size and bring into play the precipitation strength effect, improved the obdurability of steel; Do not add low temperature precipitation strength elements such as V, have good low-temperature flexibility to guarantee steel plate.
Put down in writing among the disclosed Chinese patent application CN1978695 on June 13rd, 2007 (contrast 6) and contained Cr high-strength line-pipe steel hot-rolling flat plate and production method thereof.What this method related to is the manufacture method of the high strength X 100 pipeline steel hot rolled slab of a kind of Cr of containing.Do not belong to same intensity rank with the manufacturing of X80 pipe line steel of the present invention.In this external composition design, the contrast patent has adopted higher Mo and Ni content, and cost of alloy is higher, and Mo of the present invention, Ni content are limited in 0.14%, 0.20% composition design less expensive respectively; On technology controlling and process, it is lower that contrast 6 method is stopped cold temperature, obtaining lower bainite+martensitic microstructure, the present invention's design to stop cold temperature higher, design organization is the microstructure based on granular bainite or acicular ferrite.
Pipe-line construction is not only wanted the choose reasonable grade of steel, will consider influence of various factors such as pipe diameter, transfer pressure, delivery medium, Service Environment, weldability and economy simultaneously.By calculating as can be known, in gas transmission line, distribution pressure one timing, displacement increases with caliber; Caliber one timing, displacement increases with transfer pressure, therefore adopts heavy caliber high-pressure delivery pipeline more economically, is the trend of pipeline development, thus intensity, toughness and the thickness specification of pipeline is also had higher requirement.Simultaneously, along with the continuous expansion of the whole world to energy demand, the exploitation of the energy progressively extends to badly zone of environment such as remote polar region, frozen soil, seabed, equally intensity, toughness and the thickness of transport pipe is had higher requirement.Therefore, develop the demand of the X80 level pipe line steel Wide and Thick Slab positive adaptation pipeline development of high strength, high tenacity, thick specification, have broad application prospects.
Summary of the invention
The purpose of this invention is to provide a kind of high-strength X 80 pipe line steel Wide and Thick Slab.
Another object of the present invention provides the production method of a kind of high-strength X 80 pipe line steel with Wide and Thick Slab.
In the present invention, term " Wide and Thick Slab " is meant that thickness is greater than 20mm and the width steel plate greater than 2m.
For realizing purpose of the present invention, a kind of X80 pipe line steel Wide and Thick Slab of the present invention, the chemical ingredients of its weight percent meter is: 0.03≤C≤0.08,0.10≤Si≤0.35,1.65≤Mn≤2.30, P≤0.015, S≤0.050,0.010≤Ti≤0.035,0.20≤Cr≤0.60, Mo≤0.14, Cu≤0.30, Ni≤0.20,0.01≤Al≤0.04,0.001≤Ca≤0.004, N≤0.008,0.051≤Nb≤0.110, surplus are Fe and inevitable other impurity element.
Steel plate thickness of the present invention is greater than 20mm, and width is greater than 2m.
Preferably, thickness is 20～35mm.
Preferably, X80 pipe line steel Wide and Thick Slab of the present invention has yield strength: 550～690MPa; Tensile strength: 625～825MPa; Low-temperature impact toughness :-20 ℃ of following A
Kv＞220J, FA% is greater than 90%; The DWTT performance :-15 ℃ of following SA% are greater than 85%.
For realizing above-mentioned purpose of the present invention, a kind of X80 pipe line steel of the present invention manufacture method of Wide and Thick Slab is characterized in that,
Process for making adopts the Clean Steel smelting technology of inclusion morphology control;
Hot rolling technology adopts the hot mechanical treatment of controlled rolling and controlled cooling;
Wherein, the reheat temperature of hot rolling technology slab: 1100～1200 ℃, austenite recrystallization district rolling temperature scope: 1170～940 ℃, 910 ℃～740 ℃ of the non-recrystallization zone of austenite rolling temperature scopes, warm slab thickness 〉=3T is treated in the centre, T is a finished product thickness, and speed of cooling 〉=15 ℃/s stop 400～600 ℃ of cooling temperature scopes.
Preferably, the reheat temperature range of hot rolling technology slab is 1120 ℃～1170 ℃.
Preferably, austenite recrystallization district rolling temperature scope: 1050～960 ℃.
Preferably, warm slab thickness: 3T～8T is treated in the centre, and T is a finished product thickness, and preferred centre treats that warm slab thickness is 4T～6T.
Preferably, non-recrystallization zone rolling temperature scope is 860 ℃～770 ℃.
Preferably, stopping the cooling temperature span of control is 450～550 ℃.
Preferably, described speed of cooling is 15～30 ℃/s, preferred 20～25 ℃/s.
High-strength X 80 pipe line steel Wide and Thick Slab of the present invention and method for manufacturing thereof, be mainly reflected in by the reasonable component design and processes and control, can produce the thick specification pipeline steel plate of thickness greater than 20mm, intensity rank reaches the X80 grade of steel, and have good low-temperature flexibility and weldability, this steel plate can be used for producing heavy caliber high-pressure delivery longitudinal welded pipe.The present invention adopts the composition system of high Nb in the composition design, be base with C-Mn-Nb-Cr, is aided with a small amount of Cu, Ni, Mo alloying and little Ti treatment technology, reduces greatly on the cost of alloy; Secondly lower reheat temperature, reasonably finish rolling compression ratio control, higher termination rolling temperature and the accurate cooling of employing controlled on technology, when guaranteeing plate property stability, have good advantages such as plate shape, improve labor productivity and lumber recovery, reduce cost.
Therefore, have high-intensity high-tenacity and good welds performance at micro-alloying low-carbon acicular ferrite structure, and low characteristics such as Bauschinger effect, based on material reinforcement theories such as grain refining, phase transformation strengthening, precipitation strength and dislocations strengthenings, use for reference long-term pipe line steel knowhow of Baosteel and pipe line steel laboratory study result, the composition design with acicular ferrite X80 pipe line steel has been adopted the composition design of lower carbon content, super low sulfur, Nb, Ti microalloying with low-carbon (LC) acicular ferrite structure feature.Process for making adopts the smelting Technology for Clean Steel of inclusion morphology control, hot rolling technology has adopted the hot mechanical treatment technology of controlled rolling and controlled cooling, carry out the organizational controls of the finished product by reasonable component and technology, to obtain to have the low-carbon (LC) acicular ferrite structure of high-intensity high-tenacity.
High-strength X 80 pipe line steel Wide and Thick Slab of the present invention, its Chemical Composition (weight percent wt%) is: 0.03≤C≤0.08,0.10≤Si≤0.35,1.65≤Mn≤2.30, P≤0.015, S≤0.050,0.01≤Ti≤0.035,0.20≤Cr≤0.60, Mo≤0.14, Cu≤0.30, Ni≤0.20,0.01≤Al≤0.04,0.001≤Ca≤0.004, N≤0.008,0.051≤Nb≤0.110, surplus are Fe and inevitable other impurity element.The qualification of its composition be the reasons are as follows:
Carbon C: the most basic strengthening element.Carbon dissolution forms interstitial solid solution in steel, play solution strengthening, forms carbide with the strong carbide forming element and separates out, and then plays the effect of precipitation strength.But too high C is unfavorable to ductility, toughness and the welding property of steel, and is easy to segregation and reduces anti-HIC (anti-hydrogen to crack performance, Resistance to Hydrogen-Induced Cracking) performance, influences solid solution and the strengthening effect degree of Nb simultaneously; The intensity of the too low reduction steel of C content helps improving the toughness of pipe line steel, needs to realize good obdurability coupling in conjunction with other strengthening mechanism.So C is controlled at 0.03%～0.08%.
Manganese Mn: be the most basic alloying element of low-alloy high-strength steel kind, by the intensity of solution strengthening raising steel, to cause loss of strength because of C content reduces in the compensation steel.Mn still enlarges the element of γ phase region, can reduce the γ → α transformation temperature of steel, helps to obtain tiny phase-change product, can improve the toughness of steel.This steel grade Mn content is 1.65%～2.30%.
S sulphur, P phosphorus: inevitable detrimental impurity element in the steel, defective such as easily form segregation, be mingled with worsens welding property, impelling strength and the anti-HIC performance of pipe line steel.Therefore, control P≤0.015, S≤0.005 among the present invention in the thick specification X80 pipe line steel, and must be by Ca handle clip foreign material modification technology, make the inclusion morphology nodularization and be evenly distributed, reduce it toughness and corrupting influence.
Niobium Nb: in micro-alloyed steel, improve the effective elements of recrystallize final temperature,, can effectively reduce mill load in conjunction with two stage rolling technologies, fairly obvious to the effect of grain refining.At the recrystallize rolling sequence, the Nb that strain inducing is separated out hinders the austenitic answer of deformation, recrystallize, improves the recrystallize final temperature, and wideer texturing temperature scope is provided for non-recrystallize is rolling; In the rolling and controlled chilling stage at non-recrystallize, the deformation austenite structure changes tiny phase-change product into when phase transformation, and effective crystal grain thinning is so that steel plate has high strength and high tenacity; In the fast cold stage, the Nb of solid solution can effectively postpone ferrite transformation, promotes bainite transformation; In the slow cooling stage, the Nb of solid solution separates out with the form disperse of NbC, improves intensity and does not lose toughness.Too low Nb is not obvious to recrystallize control and precipitation effect, can't bring into play the effect of crystal grain thinning, precipitation strength, in addition owing to be subjected to the restriction of C content and the influence of Heating temperature, too high Nb solid solution fully, do not bring into play effect equally, and the increase manufacturing cost, so Nb content is controlled at 0.051%～0.110% among the present invention.
Titanium Ti: be strong solid N element, the stoichiometric ratio of Ti/N is 3.42, utilizes the Ti fixing following N of 60ppm in the steel just about 0.02%, can form the TiN precipitated phase of tiny high-temperature stable when sheet billet continuous casting.Austenite crystal when this tiny TiN particle can hinder the slab reheat is effectively grown up, and helps to improve the solid solubility of Nb in austenite, simultaneously the impelling strength of improving welded heat affecting zone is had obvious effect.
Chromium Cr: therefore the important element of the hardening capacity of raising steel needs to add higher Cr and improves hardening capacity to remedy the loss of strength that thickness brings, the homogeneity of performance on the improved strength thickness direction of raising steel for the pipe line steel of thick specification; And Cr content can improve the corrosion resistance nature of steel 0.20% when above; But too high chromium and manganese add in the steel simultaneously, can cause low melting point Cr-Mn composite oxides to form, and form surface crack in hot procedure, simultaneously can the severe exacerbation welding property.Therefore Cr content should be limited to 0.20%～0.60% among the present invention.
Molybdenum Mo: improve the element of hardening capacity, effect is only second to Mn, therefore can effectively improve the strength of materials; Add a spot of Mo in this external low alloy steel and can prolong pearlitic incubation period, reduce transformation temperature, reduce the critical cooling rate of bainite transformation, help in the cooling rate scope of broad, promoting bainite transformation, make material have Technological adaptability preferably, can effectively improve the stability of armor plate strength performance, improve lumber recovery; But Mo is too high, increases manufacturing cost.Mo content is controlled in 0.14% among the present invention.
Copper, nickel (Cu, Ni): can improve the intensity of steel by the solution strengthening effect, Cu also can improve the solidity to corrosion of steel simultaneously, and the adding of Ni mainly is to improve the red brittleness that Cu easily causes in steel, and useful to toughness.Among the present invention Cu, Ni content range be controlled to be respectively≤0.30% ,≤0.20%.
Al aluminium: be the element that adds for deoxidation in the steel, add an amount of Al and help crystal grain thinning, improve the toughness and tenacity of steel, too low Al content deoxidation effect is not obvious, too high Al content can produce and be mingled with, so the content range of Al is 0.01～0.04%.
Calcium Ca: handle the form that to control sulfide by Ca, improve the anisotropy of steel plate, improve low-temperature flexibility, its content is less than at 0.001 o'clock does not have effect, surpass 0.006 and then can produce many CaO, CaS, and form large-scale inclusion, the toughness of steel is caused damage, even influence the welding property of steel.So regulation Ca content range is 0.001～0.006%, preferred 0.001%～0.004%.
Nitrogen N:N is a harmful element, and N can form thick AlN, TiN particle with elements such as Al, Ti greater than 0.008% o'clock, worsens hot workability, and simultaneously too high N is unfavorable to the timeliness impact property, so the limited field of N is≤0.008%.
Silicon Si:Si is the element that adds for steel is carried out deoxidation, has stronger solid solution strengthening effect simultaneously, the too low deoxidation of Si content is incomplete, and the Si too high levels can cause weldability and welding heat influence area toughness to worsen, thereby the scope of qualification Si is 0.10～0.35%.
The production method of the thick intensity pipe line steel with a high standard of X80 level of the present invention, process for making adopts the Clean Steel smelting technology of inclusion morphology control; Hot rolling technology adopts the hot mechanical treatment of controlled rolling and controlled cooling; Without thermal treatment.
Course of hot rolling adopts the technology of controlled rolling controlled chilling, main operational path is: slab reheat → austenite recrystallization district is rolling → treat the non-recrystallization zone of temperature → austenite rolling → controlled chilling → air cooling, comprise particularly: the hot rolling technology Heating temperature: 1100～1200 ℃, recrystallization zone rolling temperature scope: 1170～940 ℃, 910 ℃～740 ℃ of non-recrystallization zone rolling temperature scopes, finish rolling compression ratio 〉=3T (T: finished product thickness), 15 ℃/s of speed of cooling stops 400～600 ℃ of cooling temperatures.
The reheat temperature of slab is: 1100 ℃～1200 ℃, help the abundant solid solution of Nb element in the heating of this temperature range, and austenite crystal can not grow up fast, and preferred range is 1120 ℃～1170 ℃;
Austenite recrystallization district rolling temperature scope: 1170 ℃～940 ℃, in the rolling austenite generation dynamic recrystallization district that helps of this temperature range, abundant refine austenite grain-size, 1050～960 ℃ of preferred recrystallization zone rolling temperature scopes;
Warm slab thickness (finish rolling compression ratio) is treated in the centre: 3T～8T (T: finished product thickness), treat that by in the middle of controlling warm steel plate thickness helps controlling the rolling pass deformation in non-recrystallization zone, austenite is fully deformed, increase phase deformed nucleus point, refinement phase transformation grain-size, preferred centre treats that warm slab thickness is 4T～6T;
The non-recrystallization zone of austenite rolling temperature scope: 910 ℃～740 ℃, fully deform at the direct rolling austenite crystal that makes of this temperature, increase phase deformed nucleus point, have suitable resistance to deformation simultaneously, preferred non-is 860 ℃～770 ℃ in crystallizing field rolling temperature scope;
Speed of cooling is that span of control is 15～30 ℃/s, and the control cooling rate can effectively suppress granular ferrite and change in this scope, promotes bainite transformation, improves the obdurability of steel plate, and preferred cooling rate span of control is 20～25 ℃/s;
Stopping the cooling temperature span of control is 400～600 ℃, the termination cooling temperature is controlled at this temperature range and helps forming the acicular ferrite microstructure, suppress to organize thick upper bainite and lower bainite to form, help improving the obdurability of material, preferred cooling temperature span of control is 450～550 ℃.
The thick intensity pipe line steel with a high standard of X80 level of the present invention is to adopt C-Mn-Nb-Cr composition system, and its alloying constituent is simple, and with short production cycle, production method is simple owing to adopt hot rolling TMCP mode to produce, steel product cost is lower.The steel plate that obtains like this has thick specification, high strength, good low-temperature impact toughness and weldability, can be used for making oil and gas and carries and use longitudinal welded pipe.
The present invention compared with prior art, its advantage is:
(1) mainly based on C, Mn, Nb and Cr alloy, add a spot of Mo to improve the stability of strength property, add a spot of Cu and Ni to improve toughness and solidity to corrosion, can reach the obdurability requirement of thick specification X80 pipeline steel plate, production cost is lower.
(2) the thick specification X80 steel plate of the present invention's production has excellent mechanical property:
Yield strength: 550～690MPa;
Tensile strength: 625～825MPa;
Low-temperature impact toughness :-20 ℃ of following A
Kv＞220J, FA% is greater than 90%;
The DWTT performance :-15 ℃ of following SA% are greater than 85%;
(3) the present invention can produce thicker X80 steel plate, and thickness reaches more than the 20mm, can be used for making the heavy caliber straight-line joint submerged arc welding tube, is mainly used in population inhabitation compact district or city and passes through the district;
(4) steel of the present invention has lower Pcm (welding crack sensibility coefficient) index, and welding property is very good, helps the enforcement of tubulation straight weld and site girth welding.
Embodiment
Learn the composition requirement according to tempering of the present invention, design 7 kinds of different chemical ingredientss, and in conjunction with suitable production technique, to make different thickness specification X80 pipe line steel slab, concrete Chemical Composition sees Table 1.
Table 1 embodiments of the invention chemical ingredients
| Classification | ??C | ??Mn | ??Si | ??S | ??P | ??Nb | ??Ti | ??Cu | ??Ni | ??Mo | ??Cr | ??Ca | ??Alt | ??N |
| Example 1 | ??0.040 | ??2.15 | ??0.250 | ??0.0030 | ??0.0090 | ??0.091 | ??0.015 | ??0.13 | ??0.18 | ??0.13 | ??0.55 | ??0.0023 | ??0.035 | ??0.0060 |
| Example 2 | ??0.031 | ??2.28 | ??0.260 | ??0.0030 | ??0.0090 | ??0.108 | ??0.012 | ??0.24 | ??0.16 | ??0.14 | ??0.22 | ??0.0015 | ??0.020 | ??0.0070 |
| Example 3 | ??0.062 | ??1.73 | ??0.320 | ??0.0020 | ??0.0120 | ??0.064 | ??0.025 | ??0.18 | ??0.10 | ??0.08 | ??0.42 | ??0.0030 | ??0.040 | ??0.0040 |
| Example 4 | ??0.076 | ??1.65 | ??0.230 | ??0.0034 | ??0.0110 | ??0.053 | ??0.017 | ??0.28 | ??0.14 | ??0.05 | ??0.25 | ??0.0023 | ??0.030 | ??0.0040 |
| Example 5 | ??0.055 | ??1.93 | ??0.160 | ??0.0020 | ??0.0080 | ??0.075 | ??0.015 | ??0.21 | ??0.15 | ??0.12 | ??0.32 | ??0.0018 | ??0.026 | ??0.0040 |
| Example 6 | ??0.052 | ??1.83 | ??0.250 | ??0.0030 | ??0.0070 | ??0.095 | ??0.032 | ??- | ??0.12 | ??0.10 | ??0.46 | ??0.0038 | ??0.025 | ??0.0030 |
| Example 7 | ??0.045 | ??1.87 | ??0.280 | ??0.0012 | ??0.0120 | ??0.055 | ??0.016 | ??0.20 | ??- | ??0.14 | ??0.30 | ??0.0023 | ??0.012 | ??0.0040 |
Production technique: slab reheat temperature: 1100～1200 ℃, recrystallization zone rolling temperature scope: 1170～940 ℃, 910 ℃～740 ℃ of non-recrystallization zone rolling temperature scopes, the finish rolling compression ratio is 3T～6T (T: finished product thickness), 15～30 ℃/s of speed of cooling stops 400～600 ℃ of cooling temperatures.
Embodiment 1:
Being used to make the thickness specification is the thick X80 level pipe line steel Wide and Thick Slab of 32.0mm.The hot rolling technology Heating temperature: 1170 ± 20 ℃, 1130～980 ℃ of recrystallization zone rolling temperature scopes, temperature thickness 144mm is treated in the centre, 890～750 ℃ of non-recrystallization zone temperature ranges.Stop 450～550 ℃ of cooling temperatures.15～20 ℃/s of speed of cooling.
Embodiment 2:
Being used to make the thickness specification is the thick X80 level pipe line steel Wide and Thick Slab of 27.5mm.The hot rolling technology Heating temperature: 1150 ± 20 ℃, 1110～950 ℃ of recrystallization zone rolling temperature scopes, temperature thickness 155mm is treated in the centre, 860～780 ℃ of non-recrystallization zone temperature ranges.Stop 450～550 ℃ of cooling temperatures.15～25 ℃/s of speed of cooling.
Embodiment 3:
Being used to make the thickness specification is the thick X80 level pipe line steel Wide and Thick Slab of 22.0mm.The hot rolling technology Heating temperature: 1130 ± 20 ℃, 1100～940 ℃ of recrystallization zone rolling temperature scopes, temperature thickness 99mm is treated in the centre, 860～780 ℃ of non-recrystallization zone temperature ranges.Stop 500～580 ℃ of cooling temperatures.20～30 ℃/s of speed of cooling.
Embodiment 4:
Being used to make the thickness specification is the thick X80 level pipe line steel Wide and Thick Slab of 22.0mm.The hot rolling technology Heating temperature: 1130 ± 20 ℃, 1100～940 ℃ of recrystallization zone rolling temperature scopes, temperature thickness 132mm is treated in the centre, 860～780 ℃ of non-recrystallization zone temperature ranges.Stop 450～540 ℃ of cooling temperatures.15～25 ℃/s of speed of cooling.
Embodiment 5:
Being used to make the thickness specification is the thick X80 level pipe line steel Wide and Thick Slab of 26.0mm.The hot rolling technology Heating temperature: 1150 ± 20 ℃, 1110～950 ℃ of recrystallization zone rolling temperature scopes, temperature thickness 130mm is treated in the centre, 860～780 ℃ of non-recrystallization zone temperature ranges.Stop 500～580 ℃ of cooling temperatures.15～25 ℃/s of speed of cooling.
Result of implementation
Adopt above-mentioned different implementing process to be rolled, and to production board carry out bar-shaped stretching (Φ 10mm) ,-20 ℃ down full-scale Charpy-V impact powers (10 * 10 * 55mm) and-15 ℃ of service checks such as full thickness of slab Drop-Weight Tear Test (DWTT) down, the results of property that obtains is as shown in table 2.
Wherein, bar-shaped stretching (Φ 10mm) test is to adopt ASTM A 370 touchstones (steel products mechanical test method and definition) to carry out.
The full-scale summer is to adopt ASTM A 370 touchstones (steel products mechanical test method and definition) to carry out than impacting shock test.
Full thickness of slab Drop-Weight Tear Test (DWTT) is to adopt APIRP 5L3 (pipeline steel block hammer tear test operational method) touchstone to carry out.
In the table 2, Rt0.5 is a yield strength, and Rm is a tensile strength, and A50.8% is unit elongation (gauge length is 50.8mm), A
KvBe full-scale Charpy-V impact power, FA% is a fiber area of fracture percentage ratio, and SA% is the shear fracture area percent, and DWTT is full thickness of slab Drop-Weight Tear Test (DWTT) performance.
As seen, above-mentioned performance all satisfies the requirement of X80 level pipe line steel.
The steel of steel of the present invention and documents 1～6 compares and the results are shown in Table 3.
Table 3
By finding with the documents comparison shown in the table 3, steel of the present invention adopts economical composition design and heavy plate rolling manufacturing process, and without thermal treatment, can produce have high intensity, the thickness of good low-temperature impact toughness and good welding property (low Pcm index) is greater than the X80 level pipe line steel Wide and Thick Slab of 20mm, exist than big difference in composition design or technological design with prior art.Plate property of the present invention satisfies the intensity and the toughness reguirements of X80 grade of steel, and simultaneously lower crackle Sensitivity Index guarantees that steel of the present invention has good welding property, for the welding and the site operation welding of tubulation moulding process provides good condition.The X80 pipe line steel Wide and Thick Slab that the present invention produces all has excellent mechanical property, can be used for making heavy caliber X80 longitudinal welded pipe, has broad application prospects.
More than by embodiment the present invention has been carried out comparatively detailed explanation, but be not limited only to these embodiment, without departing from the inventive concept of the premise, more changeableization or improved embodiment can also be arranged, and these variations and change and all to belong to the scope of the invention.
Claims (11)
1. X80 pipe line steel Wide and Thick Slab, the chemical ingredients of its weight percent meter is: 0.03≤C≤0.08,0.10≤Si≤0.35,1.65≤Mn≤2.30, P≤0.015, S≤0.050,0.010≤Ti≤0.035,0.20≤Cr≤0.60, Mo≤0.14, Cu≤0.30, Ni≤0.20,0.01≤Al≤0.04,0.001≤Ca≤0.004, N≤0.008,0.051≤Nb≤0.110, surplus are Fe and inevitable other impurity element.
2. X80 pipe line steel Wide and Thick Slab as claimed in claim 1 is characterized in that its thickness is greater than 20mm, and width is greater than 2m.
3. X80 pipe line steel Wide and Thick Slab as claimed in claim 2 is characterized in that its thickness is 20～35mm.
4. as arbitrary described X80 pipe line steel Wide and Thick Slab in the claim 1～3, it is characterized in that,
Yield strength: 550～690MPa;
Tensile strength: 625～825MPa;
Low-temperature impact toughness :-20 ℃ of following A
Kv＞220J, FA% is greater than 90%;
The DWTT performance :-15 ℃ of following SA% are greater than 85%.
5. the manufacture method of an X80 pipe line steel usefulness Wide and Thick Slab is characterized in that,
Process for making adopts the Clean Steel smelting technology of inclusion morphology control;
Hot rolling technology adopts the hot mechanical treatment of controlled rolling and controlled cooling;
Wherein, the reheat temperature of hot rolling technology slab: 1100～1200 ℃, austenite recrystallization district rolling temperature scope: 1170～940 ℃, 910 ℃～740 ℃ of the non-recrystallization zone of austenite rolling temperature scopes, warm slab thickness 〉=3T is treated in the centre, T is a finished product thickness, and speed of cooling 〉=15 ℃/s stop 400～600 ℃ of cooling temperature scopes.
6. X80 pipe line steel Wide and Thick Slab manufacture method as claimed in claim 5 is characterized in that, the reheat temperature range of hot rolling technology slab is 1120 ℃～1170 ℃.
7. as claim 5 or 6 described X80 pipe line steel Wide and Thick Slab manufacture method, it is characterized in that austenite recrystallization district rolling temperature scope: 1050～960 ℃.
8. as arbitrary described X80 pipe line steel Wide and Thick Slab manufacture method in the claim 5～7, it is characterized in that warm slab thickness: 3T～8T is treated in the centre, T is a finished product thickness, and preferred centre treats that warm slab thickness is 4T～6T.
9. as arbitrary described X80 pipe line steel Wide and Thick Slab manufacture method in the claim 5～8, it is characterized in that non-recrystallization zone rolling temperature scope is 860 ℃～770 ℃.
10. as arbitrary described X80 pipe line steel Wide and Thick Slab manufacture method in the claim 5～9, it is characterized in that stopping the cooling temperature span of control is 450～550 ℃.
11., it is characterized in that described speed of cooling is 15～30 ℃/s, preferred 20～25 ℃/s as the described X80 pipe line steel Wide and Thick Slab manufacture method of claim 5～10.
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