CN100543167C - Thick seamless steel pipe for line pipe and manufacture method thereof - Google Patents
Thick seamless steel pipe for line pipe and manufacture method thereof Download PDFInfo
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- CN100543167C CN100543167C CNB2006800098840A CN200680009884A CN100543167C CN 100543167 C CN100543167 C CN 100543167C CN B2006800098840 A CNB2006800098840 A CN B2006800098840A CN 200680009884 A CN200680009884 A CN 200680009884A CN 100543167 C CN100543167 C CN 100543167C
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- 239000012535 impurity Substances 0.000 claims abstract description 26
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Classifications
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
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- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B19/00—Tube-rolling by rollers arranged outside the work and having their axes not perpendicular to the axis of the work
- B21B19/02—Tube-rolling by rollers arranged outside the work and having their axes not perpendicular to the axis of the work the axes of the rollers being arranged essentially diagonally to the axis of the work, e.g. "cross" tube-rolling ; Diescher mills, Stiefel disc piercers or Stiefel rotary piercers
- B21B19/04—Rolling basic material of solid, i.e. non-hollow, structure; Piercing, e.g. rotary piercing mills
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B21—MECHANICAL METAL-WORKING WITHOUT ESSENTIALLY REMOVING MATERIAL; PUNCHING METAL
- B21B—ROLLING OF METAL
- B21B23/00—Tube-rolling not restricted to methods provided for in only one of groups B21B17/00, B21B19/00, B21B21/00, e.g. combined processes planetary tube rolling, auxiliary arrangements, e.g. lubricating, special tube blanks, continuous casting combined with tube rolling
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- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/10—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies
Abstract
A kind of pipe for line weldless steel tube and manufacture method thereof as thick walled steel tube, high strength and tenacity excellent is provided.This steel pipe contains that C:0.03～0.08%, Si:0.25% are following, among Mn:0.3～2.5%, Al:0.001～0.10%, Cr:0.02～1.0%, Ni:0.02～1.0%, Mo:0.02～1.2%, Ti:0.004～0.010%, N:0.002～0.008% and Ca, Mg and the REM add up to 0.0002～0.005% more than a kind or 2 kinds, V:0～0.08%, Nb:0～0.05%, Cu:0～1.0%, surplus is made of Fe and impurity, P in the impurity is below 0.05%, and S is below 0.005%.Among the above-mentioned composition, also can contain 0.0003～0.01% B.The manufacture method of this steel pipe with the casting sheet speed of cooling, the heating condition that is used to bore a hole and tubulation after heat-treat condition be feature.
Description
Technical field
The present invention relates to the thick seamless steel pipe for line pipe and the manufacture method thereof of intensity, toughness, welding property excellent.So-called thick-walled seamless steel pipes, the meaning are that wall thickness is the above weldless steel tube of 25mm.Weldless steel tube of the present invention, be the above intensity of X70 with API (API) specification defined, be exactly intensity specifically with X70 (more than the yield strength 482MPa), X80 (more than the yield strength 551MPa), X90 (more than the board with yield strength of 620 MPa), X100 (more than the yield strength 689MPa), X120 (more than the yield strength 827MPa), have the high-intensity high-tenacity thick-walled seamless steel pipes of good flexible pipe for line concurrently, be particularly suitable for seabed lead line (flow line) and use.
Background technology
The oil, the natural gas source that are positioned at the oil field in land and shallow sea are exhausted in recent years, and the exploitation of the submarine oil field at deep-sea comes to life.In the oil field, deep-sea, need to use lead line and standpipe (riser) that crude oil and Sweet natural gas near coal-minely are transported to marine platform from what be arranged at submarine oil well, gas well.
The inside of the pipeline of the lead line of in constituting the deep-sea, being laid, bearing the highly compressed internal fluid pressure of the depths reservoir pressure that superposeed, in addition, pipeline also can be subjected to the alternate strain that causes because of wave and when operation stops from the influence of the sea pressure at deep-sea.Therefore, as the pipeline that is used on this purposes, under the high strength prerequisite, also wish it is the thick walled steel tube of high tenacity.
The weldless steel tube of high-intensity high-tenacity, it is made always is with behind the perforated steel billit of drilling/rolling machine to heat, is rolled, extends, and is configured as the pipe shape of goods, implements thermal treatment thereafter.Yet, from viewpoint energy-conservation and that technical process is simplified, use online thermal treatment in recent years so that the problem that manufacturing process flow is simplified obtains research.Particularly be conceived to the heat that after hot-work, effectively utilizes former material to possess, do not make it cool to room temperature at once, but import the quenching technology flow process.According to this method, can reach the significantly saving of the energy and the efficient activity of manufacturing process flow, thereby can significantly cut down manufacturing cost.
Steel pipe by the online thermal treatment process flow process of direct quenching after the finish to gauge is made as in the past, because be to be cooled to room temperature at once after rolling, then is not reheated, so without the process of phase transformation and reverse transformation.Therefore, easy thickization of crystal grain is difficult for guaranteeing toughness and erosion resistance.For at this problem, proposing has the following technology: even make fine technology of the crystal grain of the steel pipe after the finish to gauge and crystal grain is not too little, but still can guarantee the technology of toughness and erosion resistance.
For example, disclosed technology is in patent documentation 1 (spy opens the 2001-240913 communique), uses reheating furnace after finish to gauge, adjusts the time from finish to gauge to the reheating furnace of packing into, realizes the miniaturization of crystal grain thus.In addition, disclosed technology is in patent documentation 2 (spy opens the 2000-104117 communique), is adjusted to be grouped into, and the content of Ti and S particularly still has a good performance even crystal grain is bigger.
Yet, the steel pipe of the high-strength thick of using for the submarine oil field of making the big degree of depth that demand in recent years increases to some extent is not corresponding in the disclosed technology in described patent documentation 1.For example, if become thick walled steel tube, then the temperature of finish to gauge becomes high temperature, and the reheating furnace that reaches target is packed the temperature needs into for a long time, and production efficiency significantly reduces.In addition, the method described in the described patent documentation 2 also is difficult to be applicable to the heavy wall material.Under the situation of heavy wall material, because the speed of cooling during online thermal treatment diminishes, so even use the steel of patent documentation 2 disclosed compositions, still flexible reduces such problem.
[patent documentation 1] spy opens the 2001-240913 communique
[patent documentation 2] spy opens the 2000-104117 communique
Summary of the invention
The present invention is a problem to solve the above problems, and its purpose is, a kind of particularly still have under the prerequisite of the thick steel pipe of wall thickness high strength and stable flexible pipe for line weldless steel tube and manufacture method thereof are provided.
1. basic research and conclusion
At first, the flexible factor of domination heavy-walled weldless steel tube is analyzed.Its result distinguish following some.
(1) molten steel when solidifying and solidify after cooling conditions toughness is had a significant impact.If speed of cooling is little, then toughness reduces, and therefore need cool off more than certain speed of cooling.
(2) in addition, steel ingot is heated to high-temperature area and carries out hot worked split rolling method technical process, can good influence not arranged toughness.
(3) reason that reduces of above-mentioned toughness is, during the separating out form and be subjected to solidifying of Ti carbonitride and the influence of the speed of cooling after solidifying.For anti-toughness here reduces, the Ti carbonitride is separated out imperceptibly.
(4) precipitation strength can make intensity and flexible balance worsen concerning online heat-treated wood.To obtaining high strength is disadvantageous, but does not do one's utmost to use precipitation strength, but the method for applying flexibly phase transformation strengthening and solution strengthening is being preferred when obtaining high tenacity.
(5) in order to obtain the metal structure of homogeneous, need prevent the martensitic generation of retained austenite and low temperature phase change.
(6) as alloy composition, be to reduce Si preferred the composition, reduces P and S again, and Nb and V control in the mode that is no more than certain upper limit, and contain in right amount among an amount of Ti and Ca, Mg and the REM more than a kind.Thus, the toughness of heavy wall material significantly improves.
(7) obtaining of the conclusion of above-mentioned (1)～(6) is prerequisite with online thermal treatment.But,, then can obtain better toughness if being applied to off-line implements heat treated steel.Also can utilize above-mentioned conclusion when therefore, making the high strength material with off-line thermal treatment.
2. basic test and result thereof
In the online thermal treatment because the crystal grain micro-gasification process flow process that does not exist " phase transformation-reverse transformation " in the off-line thermal treatment to bring, so the crystal grain itself need make rolling the end time with regard to miniaturization, thereby guarantee toughness.
Usually, the crystal grain under the curdled appearance is thick, but by reheat and implement split rolling method, can make crystal grain become fine.Therefore, the chamber of experimentizing experiment is studied the optimizing of the split rolling method technical process of online heat-treated wood.It found that following tendency: in the online heat-treated wood, need not the split rolling method condition, also can not make crystal grain fine even if implement the method for split rolling method, toughness improves.That is, distinguished that above-mentioned existing general general knowledge may not be correct.
In order to understand the outer result of this anticipation, simulation test has been implemented in the chamber by experiment again.At first, as the technical process of having passed through the cogging operation, be will casting ingot casting be heated to 1250 ℃, carry out hot-work and make briquet, reheat to 1250 ℃ is by hot rolling and water-cooled simulation perforation procedure and online heat treatment step.
As the technical process of not passing through the cogging operation, be from the ingot casting of casting, to downcut and the unidimensional briquet of making by above-mentioned hot-work of briquet with mechanical workout, this briquet is heated to 1250 ℃, by hot rolling and water-cooled simulation perforation procedure and online heat treatment step.
The result of above-mentioned these two kinds of tests is that the crystal grain of not implementing split rolling method is inundatory fine, the toughness raising.
, when implementing same trial-production, but distinguish the effect that does not obtain expectation with real machine.Therefore, in above-mentioned simulation test, investigate the reason that crystal grain directly has a great difference.Its result as can be known, in split rolling method simulation test material, the Ti of interpolation almost all separates out as the Ti carbonitride, the grain that the heating in split rolling method when simulation and hot-work cause the Ti carbonitride is grown up, the precipitation particles number reduces thus.If precipitation particles reduces, then the ability of the crystal grain-growth of anchoring (pinning) parent phase reduces, and when the briquet heating that is used for perforation simulation test thereafter, can not suppress thickization of crystal grain.
On the other hand, in the technical process of not implementing the split rolling method simulation test, at first, carbonitride in the ingot casting is not separated out, when the heating of the simulation test that is used for perforation procedure, the Ti carbonitride is separated out imperceptibly, the crystal grain-growth of this Ti carbonitride pinning parent phase, and hence one can see that, and crystal grain significantly diminishes.
Also have, even when real machine is manufactured experimently, omit the split rolling method operation, crystal grain does not almost still just become fine, find when investigating with regard to its reason, this is because the speed of cooling in when casting is fully inadequately big, so had the Ti carbonitride to separate out in the casting stage, the non-existent reason of the Ti of solid solution condition.
The Ti carbonitride of separating out during casting is because at high temperature separate out, so easy thickization separated out number and reduced.Therefore, the ability of the crystal grain of pinning parent phase reduces.On the other hand, if when casting the Ti carbonitride separate out fewly, fully guaranteed solid solution Ti amount, then after trasistor manufacture process in the steel billet heating time because the Ti carbonitride is separated out under the low temperature, so can separate out imperceptibly, the change of precipitation particles number is many.If the precipitation particles number is many, then the effect of the crystal grain of pinning parent phase is big, and thickization of the crystal grain of parent phase is inhibited.Therefore, the speed of cooling of suitably controlling in the casting process flow process is very important.
Particularly, if the speed of cooling after solidifying is slow, then the high-temperature area in cooling way just has the Ti carbonitride and separates out, because be that so karyogenesis point less, each thickization of precipitate becomes thick dispersion state the separating out of the fewer austenite territory of dislocation.If in case separate out thickly, then the Ti carbonitride is difficult to dissolve in solid phase, therefore can not fine dispersion.
On the other hand, the speed of cooling after solidifying is in the time of can not separating out the speed of Ti carbonitride, not have the Ti carbonitride in the steel billet of casting, and Ti exists with solid solution condition.When the hot worked heating that is used for thereafter, the Ti carbonitride is separated out under lower temperature.Under the situation that heating the time is separated out,,, can fine dispersion separate out so karyogenesis point is many because be that low temperature in the many bainite structures of dislocation is separated out.Also have,, then separate out and be in high-temperature area, also be difficult to carry out fine separating out as can be known if rate of heating is big.
The Ti carbide is fine fully separates out in order to make, also effective in the processing of suitable temperature province enforcement soaking in the heating way.If in a single day the Ti carbonitride is separated out imperceptibly, then be difficult to thickization, even under the situation of having implemented split rolling method, still can give play to thickization of crystal grain inhibition effect.But, because some thickization have taken place in the Ti carbonitride when split rolling method, so can make the solid solution Ti when solidifying exist manyly when not implementing split rolling method.
Because the precipitation strength that utilizes V and Nb to bring obtains high strength easily, high strength, weldability were had in the steel of requirement so this precipitation strength is useful in the past mostly.Yet, in the online heat-treated wood of heavy-walled, because above-mentioned precipitation strength meeting reduces toughness greatly, so be the obsolete method of trying one's best.Particularly, need to set the strict upper limit sometimes so contain because Nb can make the toughness of online heat-treated wood significantly reduce.Though unlike Nb, also want capping about V,, guarantee the alloy designs of intensity based on phase transformation strengthening and solution strengthening.
In addition,, then be difficult to obtain the metal structure of homogeneous by the quench treatment of heat treated fs if become the heavy wall material, thus the tendency that flexible reduces.Reduce because of speed of cooling during for the heavy wall material, so it is very difficult to become the phase-change organization of homogeneous.That is, martensite and bainite phase transformation successively during cooling, if but speed of cooling is little, C can spread to a certain extent, then C can be concentrated in the austenite of not phase transformation, and this part becomes high martensite of C content and bainite after final phase transformation, become the high retained austenite of C content.Therefore, preferred speed of cooling is set greatly as far as possible, forces to cool off until the low temperature of trying one's best.
Yet, under the situation of thick walled steel tube, on the increasing speed of cooling, have limit.Therefore, even study in order to leave the technology that still becomes the tissue of homogeneous under the speed of cooling that in the heavy wall material, also can reach.It found that, by suppressing spissated element, promptly reduces the content of C, also suppresses the content of Si simultaneously, can reduce C concentrating to second phase.
Based on above discovery, the basic thought of clear and definite following alloy designs and manufacturing process flow, thus finish the present invention.Below, be " quality % " about " % " of component content meaning.
At first, C content is limited in below 0.08%.In addition, be limited on the Si below 0.25%, more preferably below 0.15%, more preferably below 0.10%.Ti does not separate out when solidifying, and does when the heating of thereafter steel billet that fine Ti carbonitride is separated out and be suitable content, it need be controlled at 0.004～0.010% narrow range.In addition, under the online heat treated situation, the Nb interpolation can make toughness reduce, and becomes the essential factor of strength variance simultaneously, therefore do not add Nb, and its upper limit as impurity is preferably below 0.005%.Because V also can make toughness reduce, so also need be below 0.08% even do not add or contain.
Other elements are adjusted from high strength and good flexible equilibrated viewpoint.For bring dysgenic P and S to set allowable upper limit value respectively to toughness.Mn, Cr, Ni, Mo and Cu then need to consider toughness and weldability, and select and adjust according to target strength.In addition, add the needed Al of deoxidation.Also adding more than a kind among selection Ca, Mg and the REM, to guarantee the characteristic of casting, it is also effective in the raising making toughness.In addition, separate out, N content need be controlled at narrow scope in order to make stable Ti carbonitride.
Secondly,, at first suppress separating out of Ti carbonitride as manufacturing process flow, obtain guaranteeing having solid solution Ti to solidify steel ingot very important.The present inventor finds, if as the content of above-mentioned C, Ti and N, then being right after does not have the Ti carbonitride to separate out after solidifying, but if speed of cooling thereafter is little, then thick Ti carbonitride is separated out, and therefore, need cool off more than specific speed after solidifying.
Ideal casting is to be continuously cast into round base (cross section is the steel billet of circle), but also can take in the quadrate casting mold continuous casting and as the ingot casting casting, and cogging becomes the technology of circle base more thereafter.But in this case, more strictly control the speed of cooling after the casting, separate out, guarantee that fully the solid solution Ti of amount is very important to suppress thick TiN.
Circle base reheat is to can hot worked temperature, implements perforation, extends, setting is rolling.If the Ti of solid solution condition fully exists, then the Ti carbonitride is separated out during reheat, because it is lower to separate out temperature, so compare with solidifying situation about separating out when the cooling back, can separate out especially fine Ti carbonitride.The fine Ti carbonitride number of separating out is many, and the crystal boundary the when heating that can suppress steel billet keeps moves, and prevents thickization of crystal grain.If heat rapidly, then fine the separating out low temperature under can not be carried out, and can not get the effect that the thick chemoprevention of crystal grain is ended, if therefore heating slowly or keep at middle temperature area, separating out of then fine Ti carbonitride obtains promotion.
In the thermal treatment behind tubulation, the tissue that obtains homogeneous is to guarantee the flexible needs.For this reason, use the steel of having adjusted chemical constitution, make and force the cooling end temp to become the low temperature of trying one's best, cooling is by very important fully.In view of the above, can prevent the C multiviscosisty of part ground phase transformation strengthening tissue and the generation of retained austenite, thereby the toughness raising.
Abideing by the present invention of above basic thought, is main idea with the manufacture method of the pipe for line weldless steel tube of the pipe for line weldless steel tube of following (1) and (2) and (3)～(6).
(1) a kind of high strength, the thick seamless steel pipe for line pipe that toughness is good, wherein, contain C:0.03～0.08%, below the Si:0.25%, Mn:0.3～2.5%, Al:0.001～0.10%, Cr:0.02～1.0%, Ni:0.02～1.0%, Mo:0.02～1.2%, Ti:0.004～0.010%, N:0.002～0.008%, and Ca, add up to 0.0002～0.005% more than a kind or 2 kinds among Mg and the REM, V:0～0.08%, Nb:0～0.05%, Cu:0～1.0%, surplus is made of Fe and impurity, P in the impurity is below 0.05%, and S is below 0.005%.
(2) a kind of high strength, the good thick seamless steel pipe for line pipe of toughness among the above-mentioned composition, contain the part that 0.0003～0.01% B substitutes Fe.
(3) manufacture method of the good thick seamless steel pipe for line pipe of a kind of high strength, toughness, its operation with following (a)～(e) is a feature.
(a) will have the molten steel of above-mentioned (1) or (2) described chemical constitution, make it to be frozen into the operation of cross section for circular steel billet by continuous casting.
(b) making the average cooling rate between 1400 ℃～1000 ℃ is more than 6 ℃/minute, with the operation of above-mentioned steel billet cool to room temperature.
(c) making the average rate of heating between 550 ℃～900 ℃ is to be heated to below 15 ℃/minute after 1150～1280 ℃, by the operation of perforation and rolling manufacturing weldless steel tube.
(d) carry out soaking with 850～1000 ℃ at once behind the tubulation after, perhaps cooling at once behind the tubulation, after then being heated to 850～1000 ℃, perhaps making the average cooling rate between 800 ℃～500 ℃ behind the tubulation at once is the operation of forcing continuously more than 8 ℃/second to be cooled to below 100 ℃.
(e) carry out the tempered operation under the temperature in 500～690 ℃ scope.
(4) manufacture method of the good thick seamless steel pipe for line pipe of a kind of high strength, toughness, its operation with following (a)～(f) is a feature.
(a) will have the molten steel of above-mentioned (1) or (2) described chemical constitution, make it to be frozen into the operation that the cross section is quadrate cogged ingot (bloom) or slab (slab) by continuous casting.
(b) making the average cooling rate between 1400 ℃～1000 ℃ is more than 8 ℃/minute, with the operation of above-mentioned cogged ingot or slab cool to room temperature.
(c) making the average rate of heating between 550 ℃～900 ℃ is to be heated to below 15 ℃/minute after 1150～1280 ℃, by forging or/and rolling making cross section be the steel billet of circle and the operation of cool to room temperature.
(d) above-mentioned steel billet is heated to after 1150～1280 ℃, by the operation of perforation and rolling manufacturing weldless steel tube.
(e) carry out soaking with 850～1000 ℃ at once behind the tubulation after, perhaps cooling earlier behind the tubulation, after then being heated to 850～1000 ℃, perhaps and then making the average cooling rate between 800 ℃～500 ℃ behind the tubulation is the operation of forcing continuously more than 8 ℃/second to be cooled to below 100 ℃.
(f) carry out the tempered operation under the temperature in 500～690 ℃ scope.
(5) manufacture method of the good thick seamless steel pipe for line pipe of a kind of high strength, toughness, its operation with following (a)～(e) is a feature.
(a) will have the molten steel of above-mentioned (1) or (2) described chemical constitution, make it to be frozen into the operation of cross section for circular steel billet by continuous casting.
(b) making the average cooling rate between 1400 ℃～1000 ℃ is more than 6 ℃/minute, with the operation of above-mentioned steel billet cool to room temperature.
(c) carry out 550 ℃～1000 ℃ soaking more than 15 minutes under the temperature province, be heated to after 1150～1280 ℃, by the operation of perforation and rolling manufacturing weldless steel tube.
(d) carry out soaking with 850～1000 ℃ at once behind the tubulation after, perhaps cooling earlier behind the tubulation, after then being heated to 850～1000 ℃, perhaps making the average cooling rate between 800 ℃～500 ℃ behind the tubulation at once is the operation of forcing continuously more than 8 ℃/second to be cooled to below 100 ℃.
(e) carry out the tempered operation under the temperature in 500～690 ℃ scope.
(6) manufacture method of the good thick seamless steel pipe for line pipe of a kind of high strength, toughness, its operation with following (a)～(f) is a feature.
(a) will have the molten steel of above-mentioned (1) or (2) described chemical constitution, make it to be frozen into the operation that the cross section is quadrate cogged ingot or slab by continuous casting.
(b) making the average cooling rate between 1400 ℃～1000 ℃ is more than 8 ℃/minute, with the operation of above-mentioned cogged ingot or slab cool to room temperature.
(c) carry out 550 ℃～1000 ℃ soaking more than 15 minutes under the temperature province, be heated to after 1150～1280 ℃, by forging or/and rolling making cross section be the steel billet of circle and the operation of cool to room temperature.
(d) above-mentioned steel billet is heated to after 1150～1280 ℃, by the operation of perforation and rolling manufacturing weldless steel tube.
(e) carry out soaking with 850～1000 ℃ at once behind the tubulation after, perhaps cooling at once behind the tubulation, after then being heated to 850～1000 ℃, perhaps being right after and making the average cooling rate between 800 ℃～500 ℃ behind the tubulation is the operation of forcing continuously more than 8 ℃/second to be cooled to below 100 ℃.
(f) carry out the tempered operation under the temperature in 500～690 ℃ scope.
Embodiment
1. the chemical constitution of steel pipe of the present invention
At first, the reason that the chemical constitution that makes steel pipe among the present invention is limited is in the above described manner carried out following elaboration.Also have as described above, the % of expression chemical composition content (concentration) is the meaning of quality %.
C：0.03～0.08％
C is the important element that is used to guarantee the intensity of steel.Obtain full intensity in order to improve hardenability in the heavy wall material, needing it is more than 0.03%.On the other hand, if surpass 0.08%, then toughness reduces, so C is 0.03～0.08%.
Below the Si:0.25%
Si has the effect as the reductor in the steel-making, but does not advocate the method for doing one's utmost to add.Its reason is because Si especially can make the toughness of heavy wall material significantly reduce.If the content of Si surpasses 0.25%, then the toughness of heavy wall material significantly reduces, even its content also is below 0.25% when therefore adding as reductor.If further improve with the next flexible that can obtain 0.15%.Most preferably suppress for being lower than 0.10%.Extreme reduction is very difficult on process for making as the Si of impurity, but if limit to such an extent that be lower than 0.05%, then can access extremely good toughness.
Mn：0.3～2.5％
In order to improve hardenability,, need contain than relatively large Mn even the heavy wall material also can be enhanced to the center and improve toughness simultaneously.Its content is lower than at 0.3% o'clock and can not get these effects, reduce if surpass 2.5% anti-HIC characteristic, so Mn is 0.3～2.5%.
Al：0.001～0.10％
Al adds as the reductor in the steel-making.In order to obtain this effect, need make its content be 0.001% with on add.On the other hand, if the content of Al surpasses 0.10%, then inclusion becomes (cluster) shape and makes the toughness deterioration, adds surface imperfection pilosity in man-hour at the oblique angle of pipe end face (bevel) in addition.Therefore Al is 0.001～0.10%.From preventing the viewpoint of surface imperfection, preferably limit its upper limit, be limited to 0.03% on preferred, be limited to 0.02% on preferred.Also have, in steel pipe of the present invention, because can not expect to add the huge deoxidation effect that brings, so preferred the following of Al content is limited to 0.010% in order fully to carry out deoxidation by Si.
Cr：0.02～1.0％
Cr improves hardenability, is the element that makes the intensity raising of steel in the heavy wall material.It significantly is to contain 0.02% when above that this effect will become.But if its content surplus, then toughness reduces on the contrary, is below 1.0% therefore.
Ni：0.02～1.0％
Ni improves hardenability, is the element that makes the intensity raising of steel in the heavy wall material.Its effect becomes remarkable when above containing 0.02%.Yet Ni is expensive element, and to make it to contain its effect also just saturated in addition superfluously, therefore with its upper limit as 1.0%.
Mo：0.02～1.2％
Mo is the element that the intensity of steel is improved by phase transformation strengthening and solution strengthening.Its effect becomes remarkable when above containing 0.02%.But reduce if add then toughness superfluously, therefore with its upper limit as 1.2%.
Ti：0.004～0.010％
As the appropriate content of Ti, can not separate out when being the cooling when solidifying, and the content that when the heating of thereafter steel billet, the Ti carbonitride is separated out, need be controlled in 0.004～0.010% the narrow range.When containing when being lower than 0.004%, then can not guarantee the number of the Ti carbonitride of separating out, if surpass 0.010%, then can thick separating out during the cooling after solidifying.Therefore the content of Ti is advisable with 0.004～0.010%.
N：0.002～0.008％
Need contain N more than 0.002% in order to ensure fine dispersive Ti carbonitride.On the other hand,, thick Ti carbonitride is separated out, therefore need be controlled in 0.002～0.008% the narrow range if N surpasses 0.008%.
V：0～0.08％
V is the element that determines content according to the balance of strength and toughness.In the time just can obtaining abundant intensity by other alloying elements, the method for not adding just can access good toughness.When doing the interpolation of intensity raising element, be preferably the content more than 0.02%.On the other hand, reduce greatly if surpass 0.08% toughness, its upper content limit is 0.08% when therefore adding.
Nb：0～0.05％
During off-line thermal treatment, Nb suppresses thickization of crystal grain when the heating that is used to quench effect is remarkable.In order to obtain this effect, preferably contain more than 0.005%.But if the content of Nb surpasses 0.05%, then thick carbonitride is separated out and the toughness reduction, so is limited to 0.05% on it.
During online treatment, the Nb carbonitride is separated out unevenly, and toughness is reduced, and strength variance is big simultaneously, therefore the method for preferably not adding Nb basically.Strength variance becomes significantly and the problem that becomes in the manufacturing is to surpass at 0.005% o'clock at its content, when therefore using online treatment, should allow the upper limit as 0.005%.
Cu：0～1.0％
Cu can not add yet, but because it has the effect that improves anti-HIC characteristic (anti-hydrogen is induced the crackle characteristic), so can add when improving anti-HIC characteristic yet.Showing anti-HIC characteristic, to improve the minimized content of effect be 0.02%.On the other hand, even because it also is saturated surpassing 1.0% effect, so its content is preferably 0.02～1.0% when adding.
Ca, Mg, REM:1 kind or add up to 0.0002～0.005% more than 2 kinds
The purpose that these elements add is that the geat when improving toughness, erosion resistance and suppressing casting by the form of control inclusion stops up to improve the casting characteristic.Add up to more than 0.0002% in order to obtain these effects, need to contain more than a kind or 2 kinds.On the other hand, if a kind of content surpass 0.005% or the total content more than 2 kind surpass 0.005%, then above-mentioned effect is saturated, not only higher effect can not get performance, and inclusion groupization easily also, toughness, anti-HIC characteristic reduce on the contrary.Therefore, when adding above-mentioned element separately, its content is 0.0002～0.005%, and when adding more than 2 kinds, the content of total is 0.0002～0.005%.Also have, so-called REM is a lanthanon, 17 elements of Y and Sc
B：0.0003～0.01％
B can not add yet, even but if add trace hardenability is improved, therefore if more add effectively during high strength at needs.In order to obtain above-mentioned effect, preferably contain more than 0.0003%.But, because add superfluously toughness is reduced, so its content is below 0.01% when adding B.
Pipe for line steel pipe of the present invention, except mentioned component, surplus is made of Fe and impurity.Wherein, P in the impurity and S need the upper limit of inhibition content as following.
Below the P:0.05%
P is the impurity element that toughness is reduced, and its content is preferably few as much as possible.If its content surpasses 0.05%, then toughness significantly reduces, and therefore allows to be limited to 0.05%.Be preferably below 0.02%, more preferably below 0.01%.
S is below 0.005%
S also is the impurity element that toughness is reduced, and is preferably the least possible.If content surpasses 0.005%, then toughness significantly reduces, and therefore allows to be limited to 0.005%.Be preferably below 0.003%, more preferably below 0.001%.
2. about manufacture method
Next, about manufacture method of the present invention, just suitable creating conditions describes.
(1) cast and solidify after cooling
At first, by refining such as the above-mentioned steel of forming such as converters, cast and obtain the casting sheet that makes it to solidify.At this moment, be inhibited the Ti carbonitride separate out to solidify steel ingot very important.As described above, if C, the Ti of regulation and the content of N, then the Ti carbonitride can not separated out basically when solidifying.Yet if speed of cooling thereafter is little, thick Ti carbonitride is separated out, and therefore need cool off more than specific speed.
As manufacturing process flow, be continuously cast into comparatively ideal of round base shape.But, also can adopt and in the quadrate casting mold, cast continuously and cast, and then cogging becomes the technical process of circle base as ingot casting.At this moment will more strictly control the speed of cooling after the casting, it is very important to suppress separating out of thick TiN.
As speed of cooling, be at the average cooling rate that is solidifying 1400～1000 ℃ the temperature province that back Ti carbonitride generates easily, need the speed of cooling more than 6 ℃/minute when being cast into round base, need the speed of cooling more than 8 ℃/minute when implementing split rolling method.More preferably, when being cast into round base the average cooling rate more than 8 ℃/minute, when implementing split rolling method the average cooling rate more than 10 ℃/minute.Also having, all is that average cooling rate is big more more for preferred in any case, so the not restriction of its upper limit.
Difference also can take place according to the position of casting sheet in the speed of cooling of casting sheet, but when in the casting mold of circle, casting continuously, according to the distance center only the speed of cooling of the distance of 1/2 radius control, when in the quadrate casting mold, casting continuously, on the line parallel with long limit, control according to the speed of cooling at place in the middle of center of gravity and the surface by dimetric center of gravity.The mensuration of temperature can be installed thermopair and carried out, but also can be undertaken by the numerical experiments of corrigendum according to the temperature history on surface.
(2) processing of steel billet or steel ingot
Circle base reheat arrives and can hot worked temperature also implement to bore a hole, extend, formalize rolling.In addition, when being cast as the cross section and being quadrate cogged ingot or slab, behind the reheat by forging or/and rollingly become round base, and implement perforation, extend, setting is rolling.
When it was lower than 1150 ℃, it is big that the thermal distortion impedance becomes as the reheat temperature, and increasing of flaw therefore need be for more than 1150 ℃.On the other hand, if surpass 1280 ℃, then because the heating fuel consumption rate becomes excessive, the oxide skin loss becomes big and yield rate reduces, and the lifetime of process furnace is uneconomical etc., is limited to 1280 ℃ on therefore.Reduce Heating temperature, it is fine more that crystal grain just becomes, and toughness is good more, and therefore preferred Heating temperature is below 1200 ℃.
If the Ti of solid solution condition fully exists, then the Ti carbonitride is separated out during reheat.But this separate out with solidify after cooling in separate out differently, it is lower to separate out temperature.Therefore, with solidify after cooling the time situation about separating out compare, can separate out very fine Ti carbonitride.The Ti carbonitride number of separating out imperceptibly is many, can suppress the crystal boundary of steel billet when heating keeps and move, and prevents thickization of crystal grain.But, if heat rapidly, then can not carry out fine the separating out under the low temperature, therefore can not get the thick effect that prevents of crystal grain.In order to promote fine the separating out under the low temperature, when effectively the practice was reheat, making the average cooling rate between 500 ℃～900 ℃ was below 15 ℃/minute, perhaps implemented the equal thermal treatment more than 15 minutes between 550 ℃～1000 ℃.
The rolling enforcement of creating conditions according to common weldless steel tube of boring a hole, extend and formalize gets final product.
3. the thermal treatment behind the tubulation
In the thermal treatment behind tubulation, the tissue that need obtain homogeneous is to guarantee toughness.Quench treatment is a cool to room temperature at once not after hot rolling, but serve as basic with the online thermal treatment of implementing to quench, if but at cooling back reheat at once and implement quenching, then crystal grain becomes finer, and toughness further improves.As online heat treating method, after hot-work finishes, if, then can access the little steel pipe of strength variance to implement quenching after the soaking pit heating again.
Strengthen the speed of cooling when quenching, with regard to easy more high strength, the high tenacity of obtaining in the heavy wall material, approaching more theoretic critical cooling rate can obtain high strength, high tenacity more.Necessary speed of cooling is more than 8 ℃/second at 800 ℃～500 ℃ average cooling rate.More preferably more than 10 ℃/second, most preferably more than 15 ℃/second.
Toughness about excellence guarantees that except speed of cooling, the cooling end temp is also very important.The steel of chemical constitution has been adjusted in employing, and cooling is that alap temperature below 100 ℃ is very important by the end of forcing the cooling end temp.Proceed to force cooling, preferably reach below 80 ℃, more preferably reach below 50 ℃, most preferably reach below 30 ℃.In view of the above, can prevent the phase transformation strengthening tissue of portion C multiviscosisty and the generation of retained austenite, toughness is improved significantly.
After the quenching, carry out tempering with the temperature in 500 ℃～700 ℃ the scope.The tempered purpose is that the adjustment and the flexible of intensity improves.The suitable decisions such as wall thickness of hold-time under the tempering temperature according to steel pipe gets final product, and is set in usually about 10 minutes～120 minutes.
[embodiment]
With the steel of the chemical constitution shown in the converter melting table 1,, adopt the method for in the continuous casting casting mold of cross section, casting and in case in the quadrate casting mold, after the casting, make the method for round base by split rolling method for circle as the manufacture method of circle base.Creating conditions when casting in the continuous casting casting mold of circle is presented in table 2 and the table 3.The solidifying process flow process is expressed as " RCC ".The technical process of casting in the quadrate casting mold is expressed as " BLCC ", and its manufacturing is presented in table 4 and the table 5.
With the heating condition of tubulation shown in table 2～table 5 heating circle base, use the tilting roller tapping machine to obtain the hollow shell.Use mandrel mill (mandrel mill) and grading machine (sizer) that this hollow shell is carried out finish rolling, obtain the steel pipe of wall thickness 30mm～50mm.Afterwards, cool off by the described quenching conditions of table 2～table 5.Promptly implement following method: implement the refrigerative method behind the tubulation immediately; Pack at once behind the tubulation reheating furnace and carry out soaking after the method for chilling again; At once carry out reheat and refrigerative method behind the cool to room temperature.By table 2～table 5 described condition implement tempering and become goods thereafter.
Extract No. 12 tension test sheets of JIS from the steel pipe that obtains, measure tensile strength (TS), yield strength (YS) as tension test.Also have, tension test is carried out according to JISZ 2241.The shock test sheet is tested from the length direction extraction 10mm * 10mm of wall thickness central authorities, the test film of 2mmV type otch according to No. 4 test films of JISZ 2202.
In the test number 1 of table 2, record 2 examples of branch's numbering 1 and 2.1-1 and 1-2 use invention steel A, and creating conditions of 1-1 is in the scope of invention regulation, can obtain good toughness.On the other hand, its rate of heating that is used for tubulation of test number 1-2 is excessive, has broken away from the manufacturing process of the present invention's regulation, can't obtain good toughness.Below, for test number 2～24 branch's numbering 1 and 2 is arranged respectively also, in same test number, use same steel grade.Branch is numbered 1 create conditions and be in the scope of invention regulation, can obtain good toughness.On the other hand, for branch numbers the manufacturing process that then broke away from the present invention's regulation at 2 o'clock, can not get good toughness.
Table 4 and table 5 use same steel grade too in the test number, branch's numbering 1 can access good toughness for the manufacturing process in the scope of the present invention's regulation.On the other hand, branch's numbering 2 is because broken away from the manufacturing process of the present invention's regulation, so can not get good toughness.
Also have, test number 25～30th, the alloy composition scope has broken away from the embodiment of the steel (comparative steel) of the present invention's regulation.Toughness is all insufficient, has its performance of line pipe of high tenacity insufficient as requiring under the heavy wall prerequisite.
Utilize possibility on the industry
According to the present invention, by chemical composition and the manufacture method thereof of regulation seamless steel pipe, can make Go out a kind of pipe for line seamless steel pipe, particularly in the thick steel pipe of wall thickness, have yield stress to be X70 (more than the yield strength 482MPa), X80 (more than the yield strength 551MPa), X90 (bend Take more than the intensity 620MPa), X100 (more than the yield strength 689MPa), X120 (yield strength More than the 827MPa) intensity, and tenacity excellent. Seamless steel pipe of the present invention can be used as the seabed Flow line usefulness is the steel pipe that can be laid in the more harsh deep-sea. Therefore, the present invention is right Energy stabilizing is supplied with the invention that major contribution is arranged.
Claims (8)
1. the manufacture method of the good thick seamless steel pipe for line pipe of high strength and toughness is characterized in that, comprises the operation of following (a)～(e),
(a) making the molten steel solidification with following chemical constitution become the cross section by continuous casting is the operation of the steel billet of circle,
Described molten steel contains C:0.03～0.08% in quality %, below the Si:0.25%, Mn:0.3～2.5%, Al:0.001～0.10%, Cr:0.02～1.0%, Ni:0.02～1.0%, Mo:0.02～1.2%, Ti:0.004～0.010%, N:0.002～0.008%, and Ca, add up to 0.0002～0.005% more than a kind or 2 kinds among Mg and the REM, V:0～0.08%, Nb:0～0.05%, Cu:0～1.0%, surplus is made of Fe and impurity, P in the impurity is below 0.05%, S is below 0.005%
(b) average cooling rate between 1400 ℃～1000 ℃ is decided to be more than 6 ℃/minute, with the operation of described steel billet cool to room temperature,
(c) the average rate of heating between 550 ℃～900 ℃ is decided to be below 15 ℃/minute, is heated to after 1150～1280 ℃, by the operation of perforation and rolling manufacturing weldless steel tube,
(d) directly carry out soaking behind the tubulation with 850～1000 ℃ after, perhaps cooling earlier behind the tubulation, after then being heated to 850～1000 ℃, perhaps directly the average cooling rate between 800 ℃～500 ℃ being decided to be behind the tubulation more than 8 ℃/second and forcing to be cooled to operation below 100 ℃ continuously
(e) temperature in 500～690 ℃ scope is carried out the tempered operation.
2. the manufacture method of the good thick seamless steel pipe for line pipe of high strength and toughness is characterized in that, comprises the operation of following (a)～(f),
(a) making the molten steel solidification with following chemical constitution become the cross section by continuous casting is the operation of quadrate cogged ingot or slab,
Described molten steel contains C:0.03～0.08% in quality %, below the Si:0.25%, Mn:0.3～2.5%, Al:0.001～0.10%, Cr:0.02～1.0%, Ni:0.02～1.0%, Mo:0.02～1.2%, Ti:0.004～0.010%, N:0.002～0.008%, and Ca, add up to 0.0002～0.005% more than a kind or 2 kinds among Mg and the REM, V:0～0.08%, Nb:0～0.05%, Cu:0～1.0%, surplus is made of Fe and impurity, P in the impurity is below 0.05%, S is below 0.005%
(b) average cooling rate between 1400 ℃～1000 ℃ is decided to be more than 8 ℃/minute, with the operation of described cogged ingot or slab cool to room temperature,
(c) the average rate of heating between 550 ℃～900 ℃ is decided to be below 15 ℃/minute, is heated to after 1150～1280 ℃, by forging or/and rolling making cross section be the steel billet of circle and the operation of cool to room temperature,
(d) described steel billet is heated to 1150～1280 ℃, by the operation of perforation and rolling manufacturing weldless steel tube,
(e) directly carry out soaking behind the tubulation with 850～1000 ℃ after, perhaps cooling earlier behind the tubulation, after then being heated to 850～1000 ℃, perhaps directly the average cooling rate between 800 ℃～500 ℃ being decided to be behind the tubulation more than 8 ℃/second and forcing to be cooled to operation below 100 ℃ continuously
(f) temperature in 500～690 ℃ scope is carried out the tempered operation.
3. the manufacture method of the good thick seamless steel pipe for line pipe of high strength and toughness is characterized in that, comprises the operation of following (a)～(e),
(a) making the molten steel solidification with following chemical constitution become the cross section by continuous casting is the operation of the steel billet of circle,
Described molten steel contains C:0.03～0.08% in quality %, below the Si:0.25%, Mn:0.3～2.5%, Al:0.001～0.10%, Cr:0.02～1.0%, Ni:0.02～1.0%, Mo:0.02～1.2%, Ti:0.004～0.010%, N:0.002～0.008%, and Ca, add up to 0.0002～0.005% more than a kind or 2 kinds among Mg and the REM, V:0～0.08%, Nb:0～0.05%, Cu:0～1.0%, surplus is made of Fe and impurity, P in the impurity is below 0.05%, S is below 0.005%
(b) average cooling rate between 1400 ℃～1000 ℃ is decided to be more than 6 ℃/minute, with the operation of described steel billet cool to room temperature,
(c) carry out the soaking more than 15 minutes of 550 ℃～1000 ℃ temperature province, be heated to after 1150～1280 ℃, by the operation of perforation and rolling manufacturing weldless steel tube,
(d) directly carry out soaking behind the tubulation with 850～1000 ℃ after, perhaps cooling earlier behind the tubulation, after then being heated to 850～1000 ℃, perhaps directly the average cooling rate between 800 ℃～500 ℃ being decided to be behind the tubulation more than 8 ℃/second and forcing to be cooled to operation below 100 ℃ continuously
(e) temperature in 500～690 ℃ scope is carried out the tempered operation.
4. the manufacture method of the good thick seamless steel pipe for line pipe of high strength and toughness is characterized in that, comprises the operation of following (a)～(f),
(a) making the molten steel solidification with following chemical constitution become the cross section by continuous casting is the operation of quadrate cogged ingot or slab,
Described molten steel contains C:0.03～0.08% in quality %, below the Si:0.25%, Mn:0.3～2.5%, Al:0.001～0.10%, Cr:0.02～1.0%, Ni:0.02～1.0%, Mo:0.02～1.2%, Ti:0.004～0.010%, N:0.002～0.008%, and Ca, add up to 0.0002～0.005% more than a kind or 2 kinds among Mg and the REM, V:0～0.08%, Nb:0～0.05%, Cu:0～1.0%, surplus is made of Fe and impurity, P in the impurity is below 0.05%, S is below 0.005%
(b) average cooling rate between 1400 ℃～1000 ℃ is decided to be more than 8 ℃/minute, with the operation of described cogged ingot or slab cool to room temperature,
(c) carry out the soaking more than 15 minutes of 550 ℃～1000 ℃ temperature province, be heated to after 1150～1280 ℃, by forging or/and rolling making cross section be the steel billet of circle and the operation of cool to room temperature,
(d) described steel billet is heated to after 1150～1280 ℃, by the operation of perforation and rolling manufacturing weldless steel tube,
(e) directly carry out soaking behind the tubulation with 850～1000 ℃ after, perhaps cooling earlier behind the tubulation, after then being heated to 850～1000 ℃, be the operation of forcing continuously more than 8 ℃/second to be cooled to below 100 ℃ directly behind the tubulation perhaps with the average cooling rate between 800 ℃～500 ℃
(f) carry out the tempered operation under the temperature in 500～690 ℃ scope.
5. the manufacture method of the good thick seamless steel pipe for line pipe of high strength and toughness is characterized in that, comprises the operation of following (a)～(e),
(a) making the molten steel solidification with following chemical constitution become the cross section by continuous casting is the operation of the steel billet of circle,
Described molten steel contains C:0.03～0.08% in quality %, below the Si:0.25%, Mn:0.3～2.5%, Al:0.001～0.10%, Cr:0.02～1.0%, Ni:0.02～1.0%, Mo:0.02～1.2%, Ti:0.004～0.010%, N:0.002～0.008%, B:0.0003～0.01%, and Ca, add up to 0.0002～0.005% more than a kind or 2 kinds among Mg and the REM, V:0～0.08%, Nb:0～0.05%, Cu:0～1.0%, surplus is made of Fe and impurity, P in the impurity is below 0.05%, S is below 0.005%
(b) average cooling rate between 1400 ℃～1000 ℃ is decided to be more than 6 ℃/minute, with the operation of described steel billet cool to room temperature,
(c) the average rate of heating between 550 ℃～900 ℃ is decided to be below 15 ℃/minute, is heated to after 1150～1280 ℃, by the operation of perforation and rolling manufacturing weldless steel tube,
(d) directly carry out soaking behind the tubulation with 850～1000 ℃ after, perhaps cooling earlier behind the tubulation, after then being heated to 850～1000 ℃, perhaps directly the average cooling rate between 800 ℃～500 ℃ being decided to be behind the tubulation more than 8 ℃/second and forcing to be cooled to operation below 100 ℃ continuously
(e) temperature in 500～690 ℃ scope is carried out the tempered operation.
6. the manufacture method of the good thick seamless steel pipe for line pipe of high strength and toughness is characterized in that, comprises the operation of following (a)～(f),
(a) making the molten steel solidification with following chemical constitution become the cross section by continuous casting is the operation of quadrate cogged ingot or slab,
Described molten steel contains C:0.03～0.08% in quality %, below the Si:0.25%, Mn:0.3～2.5%, Al:0.001～0.10%, Cr:0.02～1.0%, Ni:0.02～1.0%, Mo:0.02～1.2%, Ti:0.004～0.010%, N:0.002～0.008%, B:0.0003～0.01%, and Ca, add up to 0.0002～0.005% more than a kind or 2 kinds among Mg and the REM, V:0～0.08%, Nb:0～0.05%, Cu:0～1.0%, surplus is made of Fe and impurity, P in the impurity is below 0.05%, S is below 0.005%
(b) average cooling rate between 1400 ℃～1000 ℃ is decided to be more than 8 ℃/minute, with the operation of described cogged ingot or slab cool to room temperature,
(c) the average rate of heating between 550 ℃～900 ℃ is decided to be below 15 ℃/minute, is heated to after 1150～1280 ℃, by forging or/and rolling making cross section be the steel billet of circle and the operation of cool to room temperature,
(d) described steel billet is heated to 1150～1280 ℃, by the operation of perforation and rolling manufacturing weldless steel tube,
(e) directly carry out soaking behind the tubulation with 850～1000 ℃ after, perhaps cooling earlier behind the tubulation, after then being heated to 850～1000 ℃, perhaps directly the average cooling rate between 800 ℃～500 ℃ being decided to be behind the tubulation more than 8 ℃/second and forcing to be cooled to operation below 100 ℃ continuously
(f) temperature in 500～690 ℃ scope is carried out the tempered operation.
7. the manufacture method of the good thick seamless steel pipe for line pipe of high strength and toughness is characterized in that, comprises the operation of following (a)～(e),
(a) making the molten steel solidification with following chemical constitution become the cross section by continuous casting is the operation of the steel billet of circle,
Described molten steel contains C:0.03～0.08% in quality %, below the Si:0.25%, Mn:0.3～2.5%, Al:0.001～0.10%, Cr:0.02～1.0%, Ni:0.02～1.0%, Mo:0.02～1.2%, Ti:0.004～0.010%, N:0.002～0.008%, B:0.0003～0.01%, and Ca, add up to 0.0002～0.005% more than a kind or 2 kinds among Mg and the REM, V:0～0.08%, Nb:0～0.05%, Cu:0～1.0%, surplus is made of Fe and impurity, P in the impurity is below 0.05%, S is below 0.005%
(b) average cooling rate between 1400 ℃～1000 ℃ is decided to be more than 6 ℃/minute, with the operation of described steel billet cool to room temperature,
(c) carry out the soaking more than 15 minutes of 550 ℃～1000 ℃ temperature province, be heated to after 1150～1280 ℃, by the operation of perforation and rolling manufacturing weldless steel tube,
(d) directly carry out soaking behind the tubulation with 850～1000 ℃ after, perhaps cooling earlier behind the tubulation, after then being heated to 850～1000 ℃, perhaps directly the average cooling rate between 800 ℃～500 ℃ being decided to be behind the tubulation more than 8 ℃/second and forcing to be cooled to operation below 100 ℃ continuously
(e) temperature in 500～690 ℃ scope is carried out the tempered operation.
8. the manufacture method of the good thick seamless steel pipe for line pipe of high strength and toughness is characterized in that, comprises the operation of following (a)～(f),
(a) making the molten steel solidification with following chemical constitution become the cross section by continuous casting is the operation of quadrate cogged ingot or slab,
Described molten steel contains C:0.03～0.08% in quality %, below the Si:0.25%, Mn:0.3～2.5%, Al:0.001～0.10%, Cr:0.02～1.0%, Ni:0.02～1.0%, Mo:0.02～1.2%, Ti:0.004～0.010%, N:0.002～0.008%, B:0.0003～0.01%, and Ca, add up to 0.0002～0.005% more than a kind or 2 kinds among Mg and the REM, V:0～0.08%, Nb:0～0.05%, Cu:0～1.0%, surplus is made of Fe and impurity, P in the impurity is below 0.05%, S is below 0.005%
(b) average cooling rate between 1400 ℃～1000 ℃ is decided to be more than 8 ℃/minute, with the operation of described cogged ingot or slab cool to room temperature,
(c) carry out the soaking more than 15 minutes of 550 ℃～1000 ℃ temperature province, be heated to after 1150～1280 ℃, by forging or/and rolling making cross section be the steel billet of circle and the operation of cool to room temperature,
(d) described steel billet is heated to after 1150～1280 ℃, by the operation of perforation and rolling manufacturing weldless steel tube,
(e) directly carry out soaking behind the tubulation with 850～1000 ℃ after, perhaps cooling earlier behind the tubulation, after then being heated to 850～1000 ℃, be the operation of forcing continuously more than 8 ℃/second to be cooled to below 100 ℃ directly behind the tubulation perhaps with the average cooling rate between 800 ℃～500 ℃
(f) carry out the tempered operation under the temperature in 500～690 ℃ scope.
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2005095240A JP4792778B2 (en) | 2005-03-29 | 2005-03-29 | Manufacturing method of thick-walled seamless steel pipe for line pipe |
| JP095240/2005 | 2005-03-29 |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN101151387A CN101151387A (en) | 2008-03-26 |
| CN100543167C true CN100543167C (en) | 2009-09-23 |
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| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CNB2006800098840A Expired - Fee Related CN100543167C (en) | 2005-03-29 | 2006-03-09 | Thick seamless steel pipe for line pipe and manufacture method thereof |
Country Status (10)
| Country | Link |
|---|---|
| US (2) | US20080047635A1 (en) |
| EP (1) | EP1876254B1 (en) |
| JP (1) | JP4792778B2 (en) |
| CN (1) | CN100543167C (en) |
| AR (1) | AR052706A1 (en) |
| AU (1) | AU2006229079C1 (en) |
| BR (1) | BRPI0608953B8 (en) |
| CA (1) | CA2602526C (en) |
| NO (1) | NO340772B1 (en) |
| WO (1) | WO2006103894A1 (en) |
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-
2005
- 2005-03-29 JP JP2005095240A patent/JP4792778B2/en active Active
-
2006
- 2006-03-09 AU AU2006229079A patent/AU2006229079C1/en not_active Ceased
- 2006-03-09 EP EP06728830.8A patent/EP1876254B1/en active Active
- 2006-03-09 CN CNB2006800098840A patent/CN100543167C/en not_active Expired - Fee Related
- 2006-03-09 CA CA2602526A patent/CA2602526C/en not_active Expired - Fee Related
- 2006-03-09 WO PCT/JP2006/304613 patent/WO2006103894A1/en active Application Filing
- 2006-03-09 BR BRPI0608953A patent/BRPI0608953B8/en not_active IP Right Cessation
- 2006-03-17 AR ARP060101061A patent/AR052706A1/en active IP Right Grant
-
2007
- 2007-08-21 NO NO20074257A patent/NO340772B1/en not_active IP Right Cessation
- 2007-08-23 US US11/895,131 patent/US20080047635A1/en not_active Abandoned
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- 2010-06-01 US US12/791,486 patent/US20100236670A1/en not_active Abandoned
Also Published As
| Publication number | Publication date |
|---|---|
| EP1876254A4 (en) | 2012-08-01 |
| EP1876254B1 (en) | 2014-11-12 |
| BRPI0608953A2 (en) | 2010-02-17 |
| JP4792778B2 (en) | 2011-10-12 |
| US20080047635A1 (en) | 2008-02-28 |
| WO2006103894A1 (en) | 2006-10-05 |
| AR052706A1 (en) | 2007-03-28 |
| AU2006229079C1 (en) | 2011-03-17 |
| CA2602526A1 (en) | 2006-10-05 |
| NO340772B1 (en) | 2017-06-19 |
| AU2006229079B2 (en) | 2009-04-09 |
| EP1876254A1 (en) | 2008-01-09 |
| BRPI0608953B1 (en) | 2016-10-11 |
| CN101151387A (en) | 2008-03-26 |
| JP2006274350A (en) | 2006-10-12 |
| US20100236670A1 (en) | 2010-09-23 |
| CA2602526C (en) | 2011-08-16 |
| AU2006229079A1 (en) | 2006-10-05 |
| NO20074257L (en) | 2007-12-20 |
| BRPI0608953B8 (en) | 2017-03-21 |
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