CN102203301A - Method for manufacturing steel plate and steel pipe for ultrahigh-strength line pipe - Google Patents
Method for manufacturing steel plate and steel pipe for ultrahigh-strength line pipe Download PDFInfo
- Publication number
- CN102203301A CN102203301A CN2009801434240A CN200980143424A CN102203301A CN 102203301 A CN102203301 A CN 102203301A CN 2009801434240 A CN2009801434240 A CN 2009801434240A CN 200980143424 A CN200980143424 A CN 200980143424A CN 102203301 A CN102203301 A CN 102203301A
- Authority
- CN
- China
- Prior art keywords
- steel plate
- steel
- line
- superstrength
- manufacture method
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
- Granted
Links
Images
Classifications
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K9/00—Arc welding or cutting
- B23K9/18—Submerged-arc welding
-
- B—PERFORMING OPERATIONS; TRANSPORTING
- B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
- B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
- B23K9/00—Arc welding or cutting
- B23K9/02—Seam welding; Backing means; Inserts
- B23K9/025—Seam welding; Backing means; Inserts for rectilinear seams
- B23K9/0253—Seam welding; Backing means; Inserts for rectilinear seams for the longitudinal seam of tubes
-
- 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
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
-
- F—MECHANICAL ENGINEERING; LIGHTING; HEATING; WEAPONS; BLASTING
- F16—ENGINEERING ELEMENTS AND UNITS; GENERAL MEASURES FOR PRODUCING AND MAINTAINING EFFECTIVE FUNCTIONING OF MACHINES OR INSTALLATIONS; THERMAL INSULATION IN GENERAL
- F16L—PIPES; JOINTS OR FITTINGS FOR PIPES; SUPPORTS FOR PIPES, CABLES OR PROTECTIVE TUBING; MEANS FOR THERMAL INSULATION IN GENERAL
- F16L9/00—Rigid pipes
- F16L9/02—Rigid pipes of metal
Landscapes
- Engineering & Computer Science (AREA)
- Mechanical Engineering (AREA)
- Chemical & Material Sciences (AREA)
- Physics & Mathematics (AREA)
- Metallurgy (AREA)
- Organic Chemistry (AREA)
- Materials Engineering (AREA)
- Plasma & Fusion (AREA)
- General Engineering & Computer Science (AREA)
- Heat Treatment Of Steel (AREA)
- Arc Welding In General (AREA)
- Metal Rolling (AREA)
- Butt Welding And Welding Of Specific Article (AREA)
- Heat Treatment Of Articles (AREA)
Abstract
Disclosed is a method for manufacturing a steel plate for an ultrahigh-strength line pipe, whereby: steel comprised of 0.03-0.08% C, 0.01-0.50% Si, 1.5-2.5% Mn, 0.01% or less P, 0.0030% or less S, 0.0001-0.20% Nb, 0.0005-0.03% Al, 0.003-0.030% Ti, less than 0.0003% B, 0.0010-0.0050% N, 0.0050% or less O, in terms of mass%, with the remainder being iron and unavoidable impurities, is shaped into ingots; this steel is cast into billets; these billets are hot-rolled to form a steel plate; water cooling to a prescribed temperature higher than the MS point is performed, after which a heat-recovery process is repeated at least one or more times to cool the surface of the aforementioned steel plate; and a final water-cooling is performed to cool the surface of the aforementioned steel plate to a temperature that is at or below the MS point.
Description
Technical field
The tensile strength (TS) that the present invention relates to the circumferential direction of steel pipe reach above energy of deformation of 625MPa and excellent in low temperature toughness superstrength line-pipes steel plate manufacture method and adopt the manufacture method of the superstrength line-pipes steel pipe that this steel plate makes.Particularly can use the steel pipe that obtains by manufacture method of the present invention as Sweet natural gas, Crude Oil Transportation line pipe widely.
The application is willing to 2008-285612 number and advocates its right of priority based on the Japanese patent application laid that on November 6th, 2008 proposed, and quotes its content here.
Background technology
In recent years, as the long-distance delivery method of crude oil, Sweet natural gas, the importance of line pipe is surging all the more.Now, carry the main line line pipe of usefulness as long distance, API (API) standard x 65 becomes the basic of design, and the actual usage quantity of the line pipe of X65 also is in the great majority overwhelmingly., for the raising of the transport efficiency of (1) high-pressure trend, and (2) improve site operation efficient by external diameter, the weight that lowers line pipe, expect more high-intensity line pipe.Up to now, until the line pipe of X120 (tensile strength is more than the 915MPa) practicability.
On the other hand, in recent years, the thinking of the design of line pipe is changing.In the past, be the design (" stress based design ") that makes the unified line pipe of stress.But, recently, line pipe applied distortion also do not destroy the such design (" strain based design ") of also can not buckling of the circumference weld part of steel pipe or steel pipe itself even adopt.Up to now, about the double-strength pipe spool more than the X80, studied the flexible chemical ingredients of the low-temperature flexibility that is used to guarantee mother metal and welded heat affecting zone and created conditions.But, under the situation of " strain based design ", also require the energy of deformation after the application of the energy of deformation of mother metal or steel pipe.If do not solve the problem of these relevant toughness and energy of deformation, then the manufacturing of the line-pipes steel pipe more than the X80 of " strain based design " usefulness is impossible.In the superstrengthization of line pipe, need be used for one side and guarantee the anti-body disruptiveness etc. of balance, welding metal toughness and welded heat affecting zone (HAZ) toughness of the intensity of mother metal and low-temperature flexibility, site welding, the anti-joint property of softening, bursting test, one side is made creating conditions of the good steel pipe of mother metal energy of deformation.Therefore, the above superstrength thick-walled tube spool of X80 of these properties of steel pipes is satisfied in expectation exploitation always.
Up to now, about the manufacture method of line-pipes steel pipe,, for example, following method has been proposed in order to improve above-mentioned properties of steel pipes.In patent documentation 1 and patent documentation 2, in order to improve the energy of deformation of steel pipe, proposed all steel plate to be carried out slow cooling at leading portion to 500～600 ℃, the back segment thereafter carries out the refrigerative method with the speed of cooling faster than leading portion.In the method, can control the microstructure of steel plate and steel pipe.Moreover, in patent documentation 3 and patent documentation 4, in order to improve the anti-bending of steel pipe, all cool off, to make the thick steel plate of 16mm with the above certain speed of cooling of 15 ℃/s.
The look-ahead technique document
Patent documentation
Patent documentation 1: TOHKEMY 2004-131799 communique
Patent documentation 2: TOHKEMY 2003-293089 communique
Patent documentation 3: Japanese kokai publication hei 11-279700 communique
Patent documentation 4: TOHKEMY 2000-178689 communique
Summary of the invention
Invent problem to be solved
But in the disclosed method, the deviation that the water-cooled of invar plate stops temperature is big in patent documentation 1 and patent documentation 2, thereby has the big problem of deviation of steel plate material.In addition, in patent documentation 3 and patent documentation 4 in the disclosed method, also to stop the deviation of temperature big for the water-cooled of invar plate, except the deviation of armor plate strength is big, also becoming big problem aspect the energy of deformation of guaranteeing steel plate.
The invention provides intensity, low-temperature flexibility and the energy of deformation of mother metal good and easily the tensile strength of site welding be the superstrength line-pipes steel plate of 625MPa above (the API standard x is more than 80) and the manufacture method of steel pipe.
Be used to solve the means of problem
It is that the above and ultrahigh-strength steel plates of excellent in low temperature toughness of 625MPa and the steel plate and the creating conditions of steel pipe of steel pipe have been carried out research with great concentration that the inventor just is used to obtain tensile strength.Consequently, so that the new manufacture method of having invented superstrength line-pipes steel plate and superstrength line-pipes steel pipe.Main idea of the present invention is as follows.
(1) a kind of manufacture method of superstrength line-pipes steel plate, wherein, melting in quality % contain C:0.03～0.08%, Si:0.01～0.50%, Mn:1.5～2.5%, below the P:0.01%, below the S:0.0030%, Nb:0.0001～0.20%, Al:0.0001～0.03%, Ti:0.003～0.030%, B: be lower than 0.0003%, N:0.0010～0.0050%, below the O:0.0050%, remainder comprises the steel of iron and unavoidable impurities; Cast this steel to form steel billet; This steel billet is implemented hot rolling to form steel plate; Compare M until reaching carrying out water-cooled
SAfter putting high specified temperature, the processing of the heat exchange that will reflux repeats more than 1 time at least, cools off the surface of described steel plate; By carrying out final water-cooled, with the surface cool of described steel plate to M
SThe temperature that point is following.
Here,
M
S＝545-330[C]+2[Al]-14[Cr]-13[Cu]-23[Mn]-5[Mo]-4[Nb]-13[Ni]-7[Si]+3[Ti]+4[V]
Wherein, [C], [Al], [Cr], [Cu], [Mn], [Mo], [Nb], [Ni], [Si], [Ti], [V] are respectively the content (%) of C, Al, Cr, Cu, Mn, Mo, Nb, Ni, Si, Ti, V.
(2) according to the manufacture method of above-mentioned (1) described superstrength line-pipes steel plate, described steel also can further contain in Mo:0.01～1.0%, Cu:0.01～1.5%, Ni:0.01～5.0%, Cr:0.01～1.5%, V:0.01～0.10%, W:0.01～1.0%, Zr:0.0001～0.050%, Ta:0.0001～0.050% at least a kind in quality %.
(3) according to the manufacture method of above-mentioned (1) described superstrength line-pipes steel plate, described steel also can further contain in Mg:0.0001～0.010%, Ca:0.0001～0.005%, REM:0.0001～0.005%, Y:0.0001～0.005%, Hf:0.0001～0.005%, Re:0.0001～0.005% at least a kind in quality %.
(4), reach martensitic transformation from initial water-cooled to surface of steel plate and begin temperature (M according to the manufacture method of above-mentioned (1) described superstrength line-pipes steel plate
SAverage cooling rate point) (℃/s) also can be V
C90Below.
Here,
M
S＝545-330[C]+2[Al]-14[Cr]-13[Cu]-23[Mn]-5[Mo]-4[Nb]-13[Ni]-7[Si]+3[Ti]+4[V]
V
C90＝10
(3.69-0.75β)
β＝2.7[C]+0.4[Si]+[Mn]+0.45([Ni]+[Cu])+0.8[Cr]+2[Mo]
Wherein, [C], [Al], [Cr], [Cu], [Mn], [Mo], [Nb], [Ni], [Si], [Ti], [V] are respectively the content (%) of C, Al, Cr, Cu, Mn, Mo, Nb, Ni, Si, Ti, V.
(5) according to the manufacture method of above-mentioned (1) described superstrength line-pipes steel plate, the speed of described water-cooled and described final water-cooled also can be V
C90More than.
(6) according to the manufacture method of above-mentioned (1) described superstrength line-pipes steel plate, in described hot rolling, the reheat temperature of described steel billet also can be for more than 950 ℃, and depressing of the non-recrystallization humidity province of described steel billet can be for more than 3 than also.
(7) according to the manufacture method of above-mentioned (1) described superstrength line-pipes steel plate, also can begin to cool down since the cooling temperature below 800 ℃.
(8) a kind of manufacture method of superstrength line-pipes steel pipe, wherein, to be configured as tubulose by the UO tubing with the steel plate of the manufacture method manufacturing of above-mentioned (1) described superstrength line-pipes steel plate, use welding wire from interior outside and burn till type or fusion solder flux, union-melt weld is carried out in docking section to described steel plate, carries out expander then.
(9) according to the manufacture method of above-mentioned (8) described superstrength line-pipes steel pipe, also can be after having carried out described union-melt weld, and before carrying out described expander, weld part is heat-treated.
(10) according to the manufacture method of above-mentioned (8) described superstrength line-pipes steel pipe, also can under 200 ℃～500 ℃ temperature, heat-treat described weld part.
The effect of invention
According to the present invention, behind the hot-rolled steel plate that will define chemical ingredients,, improve the steel plate before and after the strain aging and the energy of deformation of steel pipe while, can reduce the strength variance of steel plate and steel pipe by repeating water-cooled and the backflow heat exchange is cooled off.Consequently, the security with respect to line pipe is greatly improved.
Description of drawings
Figure 1A is the sketch chart of Hardness Distribution of the thickness of slab direction of the steel plate made.
Figure 1B is the sketch chart of temperature distribution of the thickness of slab direction of the steel plate in the cooling.
Fig. 2 is the sketch chart of an example of relation of the transformation curve of expression cooling figure of surface of steel plate and steel.
Embodiment
Below, content of the present invention is elaborated.
The present invention relates to have the invention of the superstrength line pipe of above tensile strength (TS) of 625MPa and excellent in low temperature toughness.The superstrength line pipe of this intensity level is compared with the X65 of main flow in the past, but about 1.2～2.0 times pressure of the Chinese People's Anti-Japanese Military and Political College is therefore availablely carried more gas with identical in the past size.When using X65, need the wall thickness of extra strong pipe spool with higher pressure.Therefore, materials cost, transport charge, site welding construction cost improve, and line pipe is laid expense and risen significantly.Therefore, lay expense, need have the above tensile strength (TS) of 625MPa and the superstrength line pipe of excellent in low temperature toughness in order to cut down line pipe.On the other hand, when the intensity of desired steel pipe increased, it is very difficult that the manufacturing of steel pipe becomes.Particularly, when requiring " strain based design ", not only need to obtain intensity and the balance of low-temperature flexibility and the toughness of seam weldering portion of mother metal, and must also be comprised the target property of the energy of deformation behind the strain aging.But it is very difficult satisfying these all characteristics.
In the line pipe that requires " strain based design ", the intensity of the welding metal between the pipe connecting spool (intensity of circumference weld part) must be higher than the intensity of the length direction (tube axial direction of line pipe) of mother metal (being the part of the steel plate of steel plate or steel pipe).In using the environment of line pipe, frozen soil dissolved or generated frozen soil winter once more summer sometimes.In this case, line pipe produces distortion, ruptures from the circumference weld part.Particularly the intensity at the circumference weld part is under the situation of low strong coupling, then to rupture under littler distortion with respect to strength of parent.Therefore, need make the intensity of the length direction of mother metal be lower than the intensity of circumference weld part, according to the difference of the intensity of circumference weld part and to the intensity capping of the length direction of mother metal.Particularly, because each grade of line pipe has strength range, therefore according to the difference of this upper limit, the intersity limitation of mother metal that will be used to make line pipe is in narrow scope.Therefore, require stably to make line pipe and the mother metal thereof that has suppressed strength variance.
For the tensile strength with the mother metal of line pipe is limited in more than the 625MPa and is limited in narrow scope, the contriver has carried out research with great concentration.Consequently, understood fully as steel plate and adopted soft steel that the cooling conditions optimization when making the hot rolling of steel plate is very important.For example, if the C amount surpasses 0.08%, then hardenability is too high, thereby changes greatly in the central part and the surface strength of steel plate.Therefore, adopt soft steel as steel plate.In addition, for example,, cool off,, or generate martensite or do not generate martensite then according to the difference of the method for cooling of surface of steel plate if do not limit the cooling conditions of surface of steel plate fully even C amount is below 0.08%.At this moment, between the thickness direction central part (steel plate inside) of surface of steel plate and steel plate, produce difference of hardness, or in a block plate or between the steel plate of making, produce strength variance, therefore, can not make the line pipe of intensity with narrow range.
Adopt Figure 1A and Figure 1B that the deviation of above-mentioned intensity is described.Figure 1A is the sketch chart of Hardness Distribution of the thickness of slab direction of the steel plate made, and Figure 1B is the sketch chart of temperature distribution of the thickness of slab direction of the steel plate in the cooling.In Figure 1A and Figure 1B, dotted line is represented the center of thickness of slab, and long and short dash line (a) expression utilizes the result of the simple cooling (for example cooling conditions of the dotted line among Fig. 2 (i) expression) of water-cooled, and the result of cooling conditions of the present invention is adopted in solid line (b) expression.Shown in the long and short dash line (a) of Figure 1A, do not cool off not limiting the cooling conditions of surface of steel plate fully under the situation of (simple cooling), between the thickness of slab direction central part (steel plate inside) of surface of steel plate and steel plate, produce difference of hardness.This difference of hardness results from the temperature distribution of thickness of slab direction of the steel plate in the cooling shown in Figure 1B.Surface of steel plate directly contacts with water during water-cooled, therefore is cooled easily.But in steel plate inside, because of the speed of cooling domination that is subjected to conduct heat, so steel plate inside is compared with surface of steel plate and is not easy to be cooled.Therefore, in surface of steel plate and steel plate inside, can obtain the different tissue of hardness respectively.Therefore, in simple cooling,, in the steel plate of making, produce Hardness Distribution according to the difference of the temperature distribution in the steel plate in the cooling.Such Hardness Distribution is not limited to the thickness of slab direction, can be created in the place arbitrarily in the steel plate according to the unequal ununiformity of the refrigerative water yield.Strength variance in such steel plate may cause becoming problem aspect the surface imperfection such as wrinkle or crackle when the manufacturing of the steel pipe of surface of steel plate generation stress concentration.In addition, in simple cooling, the temperature that stops the steel plate water-cooled often changes in each is made batch, therefore is easy to generate strength variance between the steel plate of making.
In order to suppress the deviation of such intensity, not once to make the surface of steel plate cooling but repeat water-cooled and backflow heat exchange described later is cooled off on one side, successfully suppressed in the block plate thus and the deviation of the intensity between the steel plate of manufacturing.So-called backflow heat exchange refers to by water-cooled is stopped the specified time, makes heat pass to surface of steel plate (from the heat transfer of high-temperature portion to low-temp. portion) from steel plate inside, thus the processing that after water-cooled, improves the temperature of surface of steel plate (low-temp. portion) immediately.Under the effect of this backflow heat exchange, steel plate temperature head inner and surface of steel plate reduces, and the temperature distribution in the steel plate becomes even.In addition, even different manufacturing batch, also controlled temperature process equably.But, in the present invention,, the most important thing is beginning temperature (M than martensitic transformation in order to obtain bainite/ferrite mixed structure
SPoint) under the high specified temperature surface of steel plate carried out water-cooled after, reflux more than the processing of heat exchange repeats once to the major general, so cool off.Moreover, begin temperature (M if will reach martensitic transformation up to surface of steel plate from water-cooled (initial water-cooled)
SThe average cooling rate of surface of steel plate point) is set at below the critical speed of cooling that obtains 90% martensitic stucture, then inhibition strength deviation more.In addition, also can heat exchange reflux by regulating cooling water inflow (for example reducing the water yield).In addition, the heat exchange that also can after having carried out final water-cooled, reflux.In this case, water-cooled stops temperature sometimes also above M
SThe point.
Below, the reason that limits steel plate of the present invention (mother metal) composition is described.In addition, about chemical ingredients of the present invention, % represents quality %.
C is indispensable as the basic element that improves strength of parent.Therefore, need the C of interpolation more than 0.03%.If surpass the superfluous C of interpolation in 0.08% ground, then the weldability of steel or toughness reduce.Therefore, the upper limit with the addition of C is defined as 0.08%.
Si is necessary as the deoxidant element in when steel-making.For deoxidation, need in steel, add the Si more than 0.01%.But, add Si if surpass 0.50% ground, then the HAZ toughness of steel reduces.Therefore, the upper limit with the addition of Si is defined as 0.50%.
Mn is necessary element for the intensity of guaranteeing mother metal and toughness.But if the Mn amount surpasses 2.5%, then the HAZ toughness of mother metal significantly reduces.Be lower than at 1.5% o'clock in the Mn amount, it is difficult that the intensity of mother metal is guaranteed to become, and therefore the scope dictates with the Mn amount is 1.5～2.5%.
P is the element that the toughness to steel exerts an influence.If the P amount surpasses 0.01%, then not only the toughness of the toughness of mother metal but also HAZ also significantly reduces.Therefore, the upper limit with the P amount is defined as 0.01%.
0.0030% ground is superfluous to be added if S surpasses, and then generates thick sulfide.This thick sulfide reduces toughness, and therefore the upper limit with the S amount is defined as 0.0030%.
Nb has the element that improves the effect of intensity by formation carbide, nitride.But, when the Nb that adds below 0.0001%, do not have its effect.In addition, when interpolation surpasses 0.20% Nb, cause toughness to reduce.Therefore, the scope dictates with the Nb amount is 0.0001～0.20%.
Al adds as deoxidation material usually.In the present invention, add Al, then do not generate the oxide compound of Ti main body if surpass 0.03% ground.Therefore, the upper limit with the Al amount is defined as 0.03%.In addition, in order to reduce the oxygen amount in the molten steel, need to add the Al more than 0.0001%.Therefore, the undergage with the Al amount is decided to be 0.0001%.
Ti is as deoxidation material, the other element of bringing into play effect as nitride forming element in the miniaturization of crystal grain.But the significant toughness that the interpolation of a large amount of Ti brings carbide to form and causes reduces, and therefore the upper limit of Ti amount need be defined in 0.030%.But,, need to add the Ti more than 0.003% for the effect that obtains stipulating.Therefore, the scope dictates with the Ti amount is 0.003～0.030%.
B generally makes hardenability increase by being solid-solubilized in the steel, significantly suppress the element that ferrite generates.Therefore, the B gauge is decided to be is lower than 0.0003%.
N separates out TiN imperceptibly, is necessary for making the miniaturization of austenite particle diameter.In the N amount is 0.0010% o'clock, and miniaturization is insufficient, and therefore the undergage with the N amount is decided to be 0.0010%.In addition, if the N amount surpasses 0.0050%, then solid solution N amount increases, and makes the low-temperature flexibility deterioration of mother metal, and therefore the upper limit with the N amount is defined as 0.0050%.
0.0050% ground is superfluous to be added if O surpasses, and then generates thick oxide compound, and the toughness of mother metal is reduced.Therefore, the upper limit with the O amount is defined as 0.0050%.
Contain above element, remainder comprises that the steel of iron (Fe) and unavoidable impurities is the preferred essentially consist as steel plate of the present invention and steel pipe employing.
In addition, in the present invention, can as improving intensity and flexible element, can from Mo, Cu, Ni, Cr, V, Zr, Ta, select to add at least a kind of element as required.
Mo is when improving hardenability, forms carbide and nitride to improve the element of intensity.In order to obtain its effect, need to add the Mo more than 0.01%.But, the interpolation that surpasses a large amount of Mo of 1.0% make the intensity of mother metal be increased to required more than, toughness is significantly reduced.Therefore, the scope dictates with the Mo amount is 0.01～1.0%.
Cu is for to gain in strength under the flexible situation be effective elements not reducing.But being lower than at 0.01% o'clock in Cu amount does not have its effect, if the Cu amount surpasses 1.5%, and generation crackle easily when steel billet heat or during welding then.Therefore, the content with the Cu amount is defined as 0.01～1.5%.
Ni is an effective elements for improving toughness and intensity.In order to obtain its effect, need to add the Ni more than 0.01%.But, surpassing under the situation of adding Ni in 5.0% ground, weldability reduces.Therefore, the upper limit with the Ni amount is defined as 5.0%.
Cr is the element that improves the intensity of steel by precipitation strength.Therefore, need the Cr of interpolation more than 0.01%.But, if add Cr in large quantities, then, hardenability generates martensitic stucture because of increasing, toughness is reduced.Therefore, the upper limit with the Cr amount is defined as 1.5%.
V has by forming the element that carbide and nitride improve the effect of intensity.But, when adding the V below 0.01%, then do not have its effect.In addition, when interpolation surpasses 0.10% V, cause toughness to reduce.Therefore, the scope dictates with the V amount is 0.01～0.10%.
W is when improving hardenability, forms carbide and nitride to improve the element of intensity.In order to obtain its effect, need to add the W more than 0.01%.But, the interpolation that surpasses a large amount of W of 1.0% make the intensity of mother metal be increased to required more than, and toughness is significantly reduced.Therefore, the scope dictates with the W amount is 0.01～1.0%.
Zr and Ta are also same with Nb, are to have by forming the element that carbide and nitride improve the effect of intensity.But, when adding below 0.0001%, do not have its effect.In addition, when add surpassing 0.050% Zr or Ta, cause toughness to reduce.Therefore the scope dictates with the amount of Zr or Ta is 0.0001～0.050%.
In addition, in the present invention, as required, pinning effect or anti-lamellar tearing in order to improve oxide compound can add at least a kind of element among Mg, Ca, REM, Y, Hf, the Re.
Mg adds mainly as deoxidation material.But, add Mg if surpass 0.010% ground, then generate thick oxide compound easily, mother metal and HAZ toughness reduce.In addition, when the interpolation that is lower than 0.0001% Mg, can not fully expect generation as intracrystalline phase transformation and the necessary oxide compound of pinning particle.Therefore the interpolation scope dictates with Mg is 0.0001～0.010%.
Ca and REM, Y, Hf, Re suppress easily generation to the MnS of rolling direction elongation by generating sulfide, improve the characteristic of the thickness of slab direction of steel, particularly anti-lamellar tearing.All be lower than at 0.0001% o'clock at Ca and REM, Y, Hf, Re, can not obtain this effect.Therefore, the undergage with the amount of Ca and REM, Y, Hf, Re is decided to be 0.0001%.On the contrary, if Ca and REM, Y, Hf, Re surpass 0.0050%, then the number of the oxide compound of Ca and REM, Y, Hf, Re increases, and the ultramicrofine number that contains the Mg oxide compound reduces.Therefore, the upper limit with the amount of Ca and REM, Y, Hf, Re is defined as 0.0050%.
By the steel making working procedure melting after containing the steel of mentioned component, wait by continuous casting and to cast, thereby form steel billet (strand).This steel billet is implemented hot rolling (in that steel billet heating back is rolling), thereby form steel plate.At this moment, this steel billet is heated to A
C3The temperature (reheat temperature) that point is above makes the depressing than being more than 2 of recrystallization temperature district thereby be rolled, the depressing than being more than 3 of non-recrystallization humidity province.The average original austenite particle diameter of the steel plate that consequently, obtains is below the 20 μ m.
The reheat temperature of above-mentioned steel billet (strand) is preferably more than 950 ℃.In addition, if the reheat temperature is too high, then therefore thickization of γ crystal grain when heating preferably be defined as the reheat temperature below 1250 ℃.
About the ratio of depressing in recrystallization temperature district, if depress, then can not fully produce recrystallize than being lower than 2, therefore preferably will depress than being defined as more than 2.
If with depressing than being defined as more than 3 of non-recrystallization humidity province, then the average original austenite particle diameter of steel plate can reach below the 20 μ m.Therefore, preferred depressing with the non-recrystallization humidity province than being defined as more than 3.More preferably, the non-recrystallization humidity province depresses than being more than 4.In such cases, the average original austenite particle diameter that can make steel plate is below 10 μ m.
Temperature (water-cooled begins temperature) about the beginning water-cooled preferably begins steel plate is cooled off since the water-cooled temperature below 800 ℃.That is to say, from A
E3The cooling of the following beginning of some steel plate.In such cases, because by producing the yield ratio that ferrite transformation reduces steel plate, so the energy of deformation of steel plate becomes good.
About method of cooling, the most important thing is to reach martensitic transformation and begin temperature, thereby surface of steel plate is cooled off by water-cooled and backflow heat exchange being repeated to surface of steel plate.By this method of cooling, can suppress the strength variance of above-mentioned steel plate.Moreover, reach martensitic transformation from water-cooled (initial water-cooled) up to surface of steel plate and begin temperature (M if make
SThe average cooling rate of surface of steel plate point) (℃/s) for obtaining the critical speed of cooling V of 90% martensitic stucture
C90(℃/s) below, further inhibition strength deviation then.In addition, in following note formula (1) and formula (2) and the formula (3) M is shown respectively
SPoint and V
C90Calculating formula.
M
S＝545-330[C]+2[Al]-14[Cr]-13[Cu]-23[Mn]-5[Mo]-4[Nb]-13[Ni]-7[Si]+3[Ti]+4[V] (1)
V
C90＝10
(3.69-0.75β) (2)
β＝2.7[C]+0.4[Si]+[Mn]+0.45([Ni]+[Cu])+0.8[Cr]+2[Mo](3)
Wherein, [C], [Al], [Cr], [Cu], [Mn], [Mo], [Nb], [Ni], [Si], [Ti], [V] in above-mentioned formula (1)～formula (3) is respectively the content (%) of C, Al, Cr, Cu, Mn, Mo, Nb, Ni, Si, Ti, V.
In addition, about the temperature of surface of steel plate, measure the central part of the width of steel plate.
Backflow heat exchange among the present invention is described.Backflow heat exchange among the present invention is when cooling metal sheets, by a water-cooled surface of steel plate is being cooled to compare M
SAfter putting high specified temperature, water-cooled is stopped certain hour, thereby after water-cooled, improve the operation of the temperature of surface of steel plate immediately.That is to say, compare M until reaching carrying out water-cooled
SAfter putting high specified temperature, the heat exchange that repeats more than at least 1 time to reflux is handled, thus the cooling metal sheets surface.Then, carry out last water-cooled (final water-cooled), surface of steel plate is cooled to M
SThe temperature that point is following.Heat exchange once more also can reflux after this final water-cooled.When carrying out this backflow heat exchange, final cooling temperature is the temperature after the last backflow heat exchange.In addition, in order to prevent the deviation of the intensity in the steel plate, the backflow heat exchange number of times of the steel plate before the final water-cooled is preferably more than 2 times.In addition, in order to ensure productivity, the speed of water-cooled and final water-cooled is preferably V
C90More than.In the refrigerating unit that the present invention adopts, can reach the place (being called the zone) that nozzle that identical mode controls concentrates with water yield density has several.In the present invention, for example, these zones are divided into water-cooled zone of carrying out water-cooled and the backflow heat exchange zone of not carrying out water-cooled.That is to say that carrying out water-cooled with first area (water-cooled zone), when carrying out water-cooled, about the surface temperature of steel plate, the temperature of the outlet of second area is higher than the temperature of the outlet of first area without second area (backflow heat exchange zone).Moreover if carry out water-cooled with the 3rd zone (water-cooled zone), then the surface temperature of steel plate descends.Like this, by repeating the surface temperature that water-cooled zone and backflow heat exchange zone reduce steel plate gradually.The zone (backflow heat exchange zone) of not carrying out water-cooled can be by considering the arbitrary decisions such as cooling situation of steel plate.Finally, surface of steel plate is cooled to M in final water-cooled zone
SThe temperature that point is following.
Followingly carry out specific description under above-mentioned cooling conditions, carrying out the refrigerative reason with reference to Fig. 2.Fig. 2 is the example of relation of the transformation curve of expression cooling figure of surface of steel plate and steel.The dotted line of Fig. 2 (i) expression is with speed of cooling V
C90Cooling figure when steel plate is cooled off.In this cooling figure, steel plate about 90% is a martensitic stucture.As the dotted line of Fig. 2 (ii) shown in, at the average cooling rate of surface of steel plate greater than speed of cooling V
C90Situation under, surface of steel plate is roughly martensitic stucture.Therefore, even when the backflow heat exchange of carrying out surface of steel plate, the toughness of surface of steel plate also significantly reduces, and often produces surface imperfection such as surface crack when making steel pipe on steel plate.On the other hand, shown in the solid line of Fig. 2 (iii) reaches (iv), at the average cooling rate of surface of steel plate less than speed of cooling V
C90Situation under, steel plate is roughly bainite of the present invention/ferrite mixed structure.In addition, by heat exchange that surface of steel plate is refluxed, can make the steel plate that the steel plate interior tissue is even, strength variance is little.
Stop temperature about cooling,, then generate the defective that is considered to result from hydrogen at the thickness of slab central part of steel plate if stopping last water-cooled (final water-cooled) below 200 ℃.Therefore, the undergage that preferably cooling is stopped temperature being decided to be 200 ℃.
Then, to adopting the superstrength line-pipes steel plate of making by above-mentioned manufacture method, the method for making line pipe by UO technology (UO tubing) describes.After having made thickness of slab and being the steel plate of 12～25mm, be configured as tubulose by UO tubing (C extruding, U extruding, O extruding).Then, will be configured as the end butt joint of piped steel plate respectively, position weldering.In this tack welding, adopt MAG welding or MIG welding.Behind tack welding, carry out submerged arc welding from the inside and outside docking section that is configured as the piped steel plate of facing.In this submerged arc welding, adopt welding wire and burn till type or fusion solder flux.At last, carry out expander, thereby produce steel pipe.
In the manufacture method of superstrength line-pipes steel pipe of the present invention, preferably after the submerged arc welding of having carried out above-mentioned interior outside, and before carrying out expander, weld part (seam welding portion) is implemented thermal treatment.In addition, as the heat-treat condition of this steel pipe, preferably under 200 ℃～500 ℃ temperature, weld part is implemented thermal treatment.By this thermal treatment, can lower result from weld part (welding metal) to the deleterious MA of toughness (austenite and martensitic mixed structure).If under 200 ℃～500 ℃ temperature weld part is heated, then the thick MA that generates along original austenite crystal prevention resolves into fine cementite.But, when being lower than 200 ℃, weld part being implemented under the heat treated situation, thick MA can not resolve into cementite.Therefore, the following of the thermal treatment temp of weld part is limited to 200 ℃.In addition, if surpass 500 ℃ of ground weld part is heat-treated, then the toughness deterioration of weld part.Therefore, the thermal treatment temp of weld part on be limited to 500 ℃.
Embodiment
Then, embodiments of the invention are described.
At the thickness of the chemical ingredients that will have table 1 is after the steel billet of 240mm is heated to 1000～1210 ℃, to carry out hot rolling in the recrystallization temperature district more than 950 ℃, reaches 70～100mm up to the thickness (handover thickness) of steel billet.And then carry out hot rolling in the non-recrystallization humidity province of 880～750 ℃ scope, reach 12～25mm up to the thickness (thickness of slab) of steel billet.Then, since the cooling (initial water-cooled) of 650～795 ℃ temperature steel plates, carrying out water-cooled to than M
SAfter putting high specified temperature, the processing of the heat exchange that will reflux repeats more than 1 time at least, so cools off.Then, stop cooling (final water-cooled) 300～470 ℃ temperature.In addition, in the table 1, as a reference, also show carbon equivalent C
EqAnd welding crack sensibility indices P
Cm
For yield strength and tensile strength to each steel plate of making are estimated, take total thickness test film from each steel plate according to the API5L standard, carry out tension test at normal temperatures.About taking direction, take these total thickness test films in the length direction of the total thickness test film mode consistent with the width of steel plate.In addition, the position of taking of total thickness test film is in the length direction of the steel plate position from steel plate top ends and steel plate terminal part 1m.Take 2 total thickness test films in both sides from the wide central part of the plate of these locational steel plates.
Then, by the UO tubing with this steel formability after, by carbon dioxide-shielded welding the docking section of steel plate is positioned weldering.Then, adopt welding wire and melt flux, utilize the seam weldering of union-melt weld from the interior outside of the docking section of steel plate, thereby form steel pipe.The average line energy of seam weldering is 2.0～5.0kJ/mm.In addition, to the part steel pipe, butt seam welding portion implements 250～450 ℃ thermal treatment.Creating conditions of steel plate and steel pipe sees Table 2.
Estimate for yield strength and tensile strength, take the API test film, carry out tension test from each steel pipe to each steel pipe of making.About taking direction, take these API test films in the length direction of the API test film mode consistent with the tube axial direction of steel pipe.In addition, about taking the position, with these API test films with the vertical cut surface of tubular axis in, be the center with position from 1/4 week of seam weldering portion of each steel pipe, respectively take 2 in its both sides.In addition, as a reference,,,, carry out tension test from respectively taking 2 API test films with above-mentioned same position under 210 ℃ these steel pipes being heat-treated (air cooling after keeping 5 minutes) in order to estimate the energy of deformation behind the strain aging.Tension test is carried out according to API standard 2000.In addition, in order to estimate the toughness of steel pipe, summer coomb's test Coomb (Charpy test) when having implemented-30 ℃ and DWT test.Summer coomb's test Coomb and DWT test are also carried out according to API standard 2000.About summer coomb's test Coomb sheet and DWT test film, in the length direction of the test film mode consistent with the circumferential direction of steel pipe, with the vertical cut surface of tubular axis in, take with position from 1/2 week of seam weldering portion of steel pipe.About the DWT test film, respectively take 2 from each steel pipe, as summer coomb's test Coomb sheet, respectively take 3 from the wall thickness central part of each steel pipe.
Moreover, the HAZ toughness of each steel pipe of making is estimated.About being used to estimate HAZ flexible test film, take near the welded heat affecting zone (HAZ) the seam weldering portion of steel pipe, form breach at FL+1mm (is the position of 1mm apart from HAZ portion with the border of stitching weldering portion in HAZ portion side).As these test films, respectively take 3 from each steel pipe.Summer coomb's test Coomb to these test films during all by-30 ℃ is estimated.
These tests the results are shown in Table 3.In addition, tensile strength not only is shown in the table 3 as a reference, but also yield strength and yield ratio are shown.
Steel 1～22 expression embodiments of the invention.Shown by table 3: these steel plates and steel pipe have the above tensile strength of X80, and the strength variance in steel plate and the steel pipe also is suppressed in below the 60MPa.In addition, the Xia Shi of steel pipe can be for more than the 200J, and DWTT plastic fracture rate is more than 85%, and the Xia Shi of welded heat affecting zone absorbs and can (HAZ toughness) surpass 50J.Like this, the steel pipe in the embodiments of the invention has high toughness.Steel 23～35 expressions are less than the comparative example of creating conditions of unabridged version invention.That is to say that in steel 23, the C amount in the steel is less than scope of the present invention, so tensile strength and insufficient.In steel 24～29, at least a kind of element in basal component and the selection element is exceeded scope of the invention ground to be added in the steel, so toughness of the mother metal of steel pipe (Xia Shi energy) or HAZ toughness and insufficient.On the other hand, in steel 30～35, owing to do not reflux heat exchange surface of steel plate is not cooled off, so the deviation of the intensity of steel plate and steel pipe is greatly to more than the 100MPa.In addition, under 210 ℃, carried out the yield strength of the steel pipe after the thermal treatment and compared, increased more than the 200MPa with the yield strength of steel plate.That is to say, owing to do not reflux heat exchange surface of steel plate is not cooled off, thereby the energy of deformation behind the strain aging is reduced greatly.
Utilizability on the industry
Intensity, low-temperature flexibility and the deformation energy pipe for ultrahigh-strength line steel plate good and that the easy tensile strength of Site Welding is (the API standard x is more than 80) more than the 625MPa of mother metal and the manufacture method of steel pipe can be provided.
Claims (10)
1. the manufacture method of a superstrength line-pipes steel plate is characterized in that:
Melting in quality % contain C:0.03～0.08%, Si:0.01～0.50%, Mn:1.5～2.5%, below the P:0.01%, below the S:0.0030%, Nb:0.0001～0.20%, Al:0.0001～0.03%, Ti:0.003～0.030%, B: be lower than 0.0003%, N:0.0010～0.0050%, below the O:0.0050%, remainder comprises the steel of iron and unavoidable impurities;
Cast this steel to form steel billet;
This steel billet is implemented hot rolling to form steel plate;
Compare M until reaching carrying out water-cooled
SAfter putting high specified temperature, the processing of the heat exchange that will reflux repeats more than 1 time at least, cools off the surface of described steel plate;
By carrying out final water-cooled, with the surface cool of described steel plate to M
SThe temperature that point is following;
M
S＝545-330[C]+2[Al]-14[Cr]-13[Cu]-23[Mn]-5[Mo]-4[Nb]-13[Ni]-7[Si]+3[Ti]+4[V]
Wherein, [C], [Al], [Cr], [Cu], [Mn], [Mo], [Nb], [Ni], [Si], [Ti], [V] are respectively the degree of C, Al, Cr, Cu, Mn, Mo, Nb, Ni, Si, Ti, V.
2. the manufacture method of superstrength line-pipes steel plate according to claim 1 is characterized in that, described steel further contains in quality %:
Mo：0.01～1.0％、
Cu：0.01～1.5％、
Ni：0.01～5.0％、
Cr：0.01～1.5％、
V：0.01～0.10％、
W：0.01～1.0％、
Zr：0.0001～0.050％、
In Ta:0.0001～0.050% at least a kind.
3. the manufacture method of superstrength line-pipes steel plate according to claim 1 is characterized in that, described steel further contains in quality %:
Mg：0.0001～0.010％、
Ca：0.0001～0.005％、
REM：0.0001～0.005％、
Y：0.0001～0.005％、
Hf：0.0001～0.005％、
In Re:0.0001～0.005% at least a kind.
4. the manufacture method of superstrength line-pipes steel plate according to claim 1 is characterized in that: reach martensitic transformation to begin temperature be M from initial water-cooled to surface of steel plate
SThe average cooling rate of point is V
C90Below, the unit of described average cooling rate is ℃/s;
M
S＝545-330[C]+2[Al]-14[Cr]-13[Cu]-23[Mn]-5[Mo]-4[Nb]-13[Ni]-7[Si]+3[Ti]+4[V]
V
C90＝10
(3.69-0.75β)
β＝2.7[C]+0.4[Si]+[Mn]+0.45([Ni]+[Cu])+0.8[Cr]+2[Mo]
Wherein, [C], [Al], [Cr], [Cu], [Mn], [Mo], [Nb], [Ni], [Si], [Ti], [V] are respectively the degree of C, Al, Cr, Cu, Mn, Mo, Nb, Ni, Si, Ti, V.
5. the manufacture method of superstrength line-pipes steel plate according to claim 1 is characterized in that: the speed of described water-cooled and described final water-cooled is V
C90More than.
6. the manufacture method of superstrength line-pipes steel plate according to claim 1 is characterized in that: in described hot rolling, the reheat temperature of described steel billet is more than 950 ℃, the depressing than being more than 3 of the non-recrystallization humidity province of described steel billet.
7. the manufacture method of superstrength line-pipes steel plate according to claim 1 is characterized in that: begin to cool down since the cooling temperature below 800 ℃.
8. the manufacture method of a superstrength line-pipes steel pipe is characterized in that:
To be configured as tubulose by the UO tubing with the steel plate of the manufacture method manufacturing of the described superstrength line-pipes of claim 1 steel plate;
Use welding wire and burn till type or fusion solder flux from interior outside, union-melt weld is carried out in the docking section of described steel plate;
Carry out expander then.
9. the manufacture method of superstrength line-pipes steel pipe according to claim 8 is characterized in that: after having carried out described union-melt weld and carrying out before the described expander weld part being heat-treated.
10. the manufacture method of superstrength line-pipes steel pipe according to claim 9 is characterized in that: under 200 ℃～500 ℃ temperature described weld part is heat-treated.
Applications Claiming Priority (3)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2008-285612 | 2008-11-06 | ||
| JP2008285612 | 2008-11-06 | ||
| PCT/JP2009/005929 WO2010052926A1 (en) | 2008-11-06 | 2009-11-06 | Method for manufacturing steel plate and steel pipe for ultrahigh-strength line pipe |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| CN102203301A true CN102203301A (en) | 2011-09-28 |
| CN102203301B CN102203301B (en) | 2013-06-12 |
Family
ID=42152739
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN200980143424.0A Active CN102203301B (en) | 2008-11-06 | 2009-11-06 | Method for manufacturing steel plate and steel pipe for ultrahigh-strength line pipe |
Country Status (5)
| Country | Link |
|---|---|
| JP (1) | JP4819185B2 (en) |
| CN (1) | CN102203301B (en) |
| BR (1) | BRPI0921686B1 (en) |
| RU (1) | RU2461636C1 (en) |
| WO (1) | WO2010052926A1 (en) |
Cited By (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103320701A (en) * | 2012-03-23 | 2013-09-25 | 宝山钢铁股份有限公司 | Ferrite bainite advanced high strength steel plate and manufacturing method thereof |
| CN103468905A (en) * | 2013-09-06 | 2013-12-25 | 鞍钢股份有限公司 | 485MPa grade pipeline steel hot-rolled coil plate and manufacturing method thereof |
| CN103882312A (en) * | 2014-03-04 | 2014-06-25 | 南京钢铁股份有限公司 | Low-cost high-toughness steel plate used at low temperature of minus 140 DEG C and manufacturing method thereof |
| CN105555983A (en) * | 2013-12-25 | 2016-05-04 | 新日铁住金株式会社 | Electric resistance welded steel pipe for oil well |
| CN117144253A (en) * | 2023-09-07 | 2023-12-01 | 中信金属股份有限公司 | Niobium microalloyed hot rolled ribbed steel bar and production method thereof |
| WO2023231981A1 (en) * | 2022-05-30 | 2023-12-07 | 宝山钢铁股份有限公司 | High-strength petroleum pipe casing and manufacturing method therefor |
Families Citing this family (12)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP5625694B2 (en) * | 2010-09-30 | 2014-11-19 | Ｊｆｅスチール株式会社 | High-strength, high-toughness thick-walled steel plate with excellent material uniformity in the steel plate and method for producing the same |
| CN103069020B (en) * | 2011-04-19 | 2017-03-15 | 新日铁住金株式会社 | Oil well electric welded steel pipe and the manufacture method of oil well electric welded steel pipe |
| MX2013009560A (en) | 2011-09-27 | 2013-09-06 | Nippon Steel & Sumitomo Metal Corp | Hot coil for line pipe and manufacturing method therefor. |
| RU2544326C1 (en) * | 2014-01-09 | 2015-03-20 | Публичное акционерное общество "Северсталь" (ПАО "Северсталь") | Manufacturing method of low alloyed steel plates with increased corrosion resistance |
| CN103952641B (en) * | 2014-04-10 | 2016-10-05 | 日照钢铁控股集团有限公司 | The corroded pipeline of resistance to SCC steel and manufacturing process thereof |
| CN105088096B (en) * | 2015-08-31 | 2017-04-19 | 山东钢铁股份有限公司 | X80 pipeline steel with high stress ratio and high arrest toughness and preparation method and application of X80 pipeline steel |
| JP6642118B2 (en) * | 2016-03-02 | 2020-02-05 | 日本製鉄株式会社 | Sour-resistant steel plate |
| MX2018015659A (en) * | 2016-06-22 | 2019-03-14 | Jfe Steel Corp | Hot-rolled steel sheet for thick high strength line pipes, welded steel pipe for thick high strength line pipes, and manfuacturing method therefor. |
| RU2632496C1 (en) * | 2016-11-28 | 2017-10-05 | Акционерное общество "Выксунский металлургический завод" | Method of electric arc multi-electrode welding under flux of longitudinal joints of thick-walled large-diameter pipes |
| RU2653384C1 (en) * | 2017-10-04 | 2018-05-08 | Юлия Алексеевна Щепочкина | Die steel |
| RU2657392C1 (en) * | 2017-11-20 | 2018-06-13 | Юлия Алексеевна Щепочкина | Steel |
| KR102119975B1 (en) * | 2018-11-29 | 2020-06-08 | 주식회사 포스코 | High strength thick steel plate for linepipe having excellent low temperature toughness and ductility as well as low yield ratio |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH07284836A (en) * | 1994-04-18 | 1995-10-31 | Nippon Steel Corp | Method for cooling steel plate at high temperature |
| JP2003277829A (en) * | 2002-03-26 | 2003-10-02 | Jfe Steel Kk | Method of producing high toughness, high tensile strength steel |
| JP2008240097A (en) * | 2007-03-28 | 2008-10-09 | Jfe Steel Kk | Method for producing hot-rolled steel sheet excellent in surface quality and ductile crack propagation characteristics |
Family Cites Families (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP4119676B2 (en) * | 2002-05-01 | 2008-07-16 | 株式会社神戸製鋼所 | Low yield ratio type high strength steel plate excellent in bending workability and manufacturing method thereof |
| JP3968011B2 (en) * | 2002-05-27 | 2007-08-29 | 新日本製鐵株式会社 | High strength steel excellent in low temperature toughness and weld heat affected zone toughness, method for producing the same and method for producing high strength steel pipe |
| JP2004010971A (en) * | 2002-06-07 | 2004-01-15 | Nippon Steel Corp | Method for producing steel sheet having excellent strength and toughness and satisfactory flatness at high efficiency |
| RU2331698C2 (en) * | 2003-12-19 | 2008-08-20 | Ниппон Стил Корпорейшн | Steel sheets for ultrahigh-strength header pipes and ultrahigh-strength header pipes possessing excellent low temperature impact resistance and methods of their fabrication |
| JP4687122B2 (en) * | 2004-01-30 | 2011-05-25 | Ｊｆｅスチール株式会社 | Manufacturing method of steel with excellent strength uniformity in the thickness direction and fatigue crack propagation characteristics |
| RU2270873C1 (en) * | 2005-03-15 | 2006-02-27 | Федеральное Государственное Унитарное Предприятие "Центральный Научно-Исследовательский Институт Конструкционных Материалов "Прометей" (Фгуп "Цнии Км "Прометей") | Method of production of skelp steel for pipes of underwater sea gas pipe lines of high parameters |
| JP5251089B2 (en) * | 2006-12-04 | 2013-07-31 | 新日鐵住金株式会社 | Welded steel pipe for high-strength thick-walled line pipe excellent in low-temperature toughness and manufacturing method |
| JP2009084598A (en) * | 2007-09-27 | 2009-04-23 | Nippon Steel Corp | Method for manufacturing steel sheet superior in deformability and low-temperature toughness for ultrahigh-strength line pipe, and method for manufacturing steel pipe for ultrahigh-strength line pipe |
-
2009
- 2009-11-06 CN CN200980143424.0A patent/CN102203301B/en active Active
- 2009-11-06 RU RU2011119110/02A patent/RU2461636C1/en not_active IP Right Cessation
- 2009-11-06 WO PCT/JP2009/005929 patent/WO2010052926A1/en active Application Filing
- 2009-11-06 BR BRPI0921686-3A patent/BRPI0921686B1/en active IP Right Grant
- 2009-11-06 JP JP2010536699A patent/JP4819185B2/en active Active
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH07284836A (en) * | 1994-04-18 | 1995-10-31 | Nippon Steel Corp | Method for cooling steel plate at high temperature |
| JP2003277829A (en) * | 2002-03-26 | 2003-10-02 | Jfe Steel Kk | Method of producing high toughness, high tensile strength steel |
| JP2008240097A (en) * | 2007-03-28 | 2008-10-09 | Jfe Steel Kk | Method for producing hot-rolled steel sheet excellent in surface quality and ductile crack propagation characteristics |
Cited By (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN103320701A (en) * | 2012-03-23 | 2013-09-25 | 宝山钢铁股份有限公司 | Ferrite bainite advanced high strength steel plate and manufacturing method thereof |
| CN103320701B (en) * | 2012-03-23 | 2016-08-03 | 宝山钢铁股份有限公司 | A kind of ferrite-bainite AHSS plate and manufacture method thereof |
| CN103468905A (en) * | 2013-09-06 | 2013-12-25 | 鞍钢股份有限公司 | 485MPa grade pipeline steel hot-rolled coil plate and manufacturing method thereof |
| CN103468905B (en) * | 2013-09-06 | 2016-03-02 | 鞍钢股份有限公司 | A kind of 485MPa level line steel hot rolling roll bending and manufacture method thereof |
| CN105555983A (en) * | 2013-12-25 | 2016-05-04 | 新日铁住金株式会社 | Electric resistance welded steel pipe for oil well |
| CN103882312A (en) * | 2014-03-04 | 2014-06-25 | 南京钢铁股份有限公司 | Low-cost high-toughness steel plate used at low temperature of minus 140 DEG C and manufacturing method thereof |
| CN103882312B (en) * | 2014-03-04 | 2016-04-27 | 南京钢铁股份有限公司 | The manufacture method of low-cost high-toughness-140 DEG C of Steel Plates For Low Temperature Service |
| WO2023231981A1 (en) * | 2022-05-30 | 2023-12-07 | 宝山钢铁股份有限公司 | High-strength petroleum pipe casing and manufacturing method therefor |
| CN117144253A (en) * | 2023-09-07 | 2023-12-01 | 中信金属股份有限公司 | Niobium microalloyed hot rolled ribbed steel bar and production method thereof |
| CN117144253B (en) * | 2023-09-07 | 2024-04-30 | 中信金属股份有限公司 | Niobium microalloyed hot rolled ribbed steel bar and production method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| BRPI0921686A2 (en) | 2016-02-16 |
| RU2461636C1 (en) | 2012-09-20 |
| CN102203301B (en) | 2013-06-12 |
| JPWO2010052926A1 (en) | 2012-04-05 |
| JP4819185B2 (en) | 2011-11-24 |
| WO2010052926A1 (en) | 2010-05-14 |
| BRPI0921686B1 (en) | 2018-01-02 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN102203301B (en) | Method for manufacturing steel plate and steel pipe for ultrahigh-strength line pipe | |
| CN102203303B (en) | Method for manufacturing steel plate and steel pipe for ultrahigh-strength line pipe | |
| CN102203302B (en) | Method for manufacturing steel plate and steel pipe for ultrahigh-strength line pipe | |
| KR101668546B1 (en) | High strength steel plate having low yield ratio excellent in terms of strain ageing resistance, method for manufacturing the same and high strength welded steel pipe made of the same | |
| CN103334053B (en) | Manufacturing method for high-strength steel tube for low-temperature use with superior buckling resistance and toughness in weld heat-affected areas | |
| KR101668545B1 (en) | High strength steel plate having low yield ratio excellent in terms of strain ageing resistance, method for manufacturing the same and high strength welded steel pipe made of the same | |
| JP5176271B2 (en) | Method for producing high-strength steel sheet for line pipe with tensile strength of 760 MPa or higher with suppressed increase in yield strength after heating by coating treatment, and method for producing high-strength steel pipe for line pipe using the same | |
| JP5055774B2 (en) | A steel plate for line pipe having high deformation performance and a method for producing the same. | |
| JP5499734B2 (en) | Ultra-thick high-tensile hot-rolled steel sheet excellent in low-temperature toughness and method for producing the same | |
| JP2009057629A (en) | High strength steel pipe for low temperature use having excellent buckling resistance and weld heat-affected zone toughness, and method for producing the same | |
| JP5991175B2 (en) | High-strength steel sheet for line pipes with excellent material uniformity in the steel sheet and its manufacturing method | |
| JP5401863B2 (en) | Manufacturing method for thick-walled high-tensile hot-rolled steel sheet with excellent low-temperature toughness | |
| JP3941211B2 (en) | Manufacturing method of steel plate for high-strength line pipe with excellent HIC resistance | |
| JP2007138289A (en) | Thick high strength hot rolled steel plate and its production method | |
| JP4341395B2 (en) | High strength steel and weld metal for high heat input welding | |
| JP5151034B2 (en) | Manufacturing method of steel plate for high tension line pipe and steel plate for high tension line pipe | |
| JP5157387B2 (en) | Method for manufacturing thick-walled, high-strength, high-toughness steel pipe material with high deformability | |
| JP5991174B2 (en) | High-strength steel sheet for sour-resistant pipes with excellent material uniformity in the steel sheet and its manufacturing method | |
| JP4523908B2 (en) | Steel sheet for high strength line pipe having excellent tensile strength of 900 MPa class or more excellent in low temperature toughness, line pipe using the same, and production method thereof | |
| JP2009084598A (en) | Method for manufacturing steel sheet superior in deformability and low-temperature toughness for ultrahigh-strength line pipe, and method for manufacturing steel pipe for ultrahigh-strength line pipe | |
| JP2007169747A (en) | Method for producing high-strength and high-toughness steel plate excellent in strength and deformability in middle temperature zone | |
| JP4105990B2 (en) | High strength welded structural steel with excellent low temperature toughness of large heat input weld HAZ and method for producing the same | |
| KR100268841B1 (en) | The manufacturing method for erw pipe used hot rolling steel sheet | |
| CN111655872B (en) | Steel material for line pipe, method for producing same, and method for producing line pipe | |
| JPH0673450A (en) | Production of high strength steel sheet excellent in hydrogen induced cracking resistance |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| ASS | Succession or assignment of patent right |
Owner name: NIPPON STEEL + SUMITOMO METAL CORPORATION Free format text: FORMER OWNER: SHIN NIPPON STEEL LTD. Effective date: 20130325 |
|
| C41 | Transfer of patent application or patent right or utility model | ||
| TA01 | Transfer of patent application right |
Effective date of registration: 20130325 Address after: Tokyo, Japan Applicant after: Nippon Steel Corporation Address before: Tokyo, Japan Applicant before: Nippon Steel Corporation |
|
| C14 | Grant of patent or utility model | ||
| GR01 | Patent grant | ||
| CP01 | Change in the name or title of a patent holder |
Address after: Tokyo, Japan Patentee after: Nippon Iron & Steel Corporation Address before: Tokyo, Japan Patentee before: Nippon Steel Corporation |
|
| CP01 | Change in the name or title of a patent holder |