CN102124133A - High-tensile strength steel and manufacturing method thereof - Google Patents
High-tensile strength steel and manufacturing method thereof Download PDFInfo
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- 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
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- 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
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
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- 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
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
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- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
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- 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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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C2202/00—Physical properties
Abstract
Disclosed are a high-tensile strength steel wherein the base material has excellent strength and ductility, as well as excellent ductility in welding heated parts, even in thick high-strength steel plates, and a manufacturing method thereof. More specifically, disclosed is a high-tensile strength steel comprising, in mass%, C: 0.03-0.10%, Si: 0.30% or less, Mn: 1.60-2.30%, P: 0.015% or less, S: 0.005% or less, Al: 0.005-0.06%, Nb: 0.004-0.05%, Ti: 0.005-0.02%, N: 0.001-0.005%, Ca: 0.0005-0.003%, as well as Ca, S, and O in the following formula (1): (1) wherein the content (mass%) of each element Ca, S, and O is satisfied, and the remainder of which comprises Fe and unavoidable impurities.
Description
Technical field
The present invention relates at boats and ships (ship) or marine structures (marine structure), pipeline steel pipe (line pipe), high-strength steel (high-tensilestrength steels) and the manufacture method thereof used in the pressurized vessels (pressure vessel) etc. relate in particular to yielding stress (YS (yield stress)) for more than the 460MPa, and not only the intensity (strength) of mother metal (base material) and toughness (toughness) are good but also also good high-strength steel and the manufacture method thereof of the toughness of weld part (weld zone) (CTOD (crack tip openingdisplacement) characteristic).
Background technology
The steel that uses in boats and ships or marine structures etc. generally is processed into the structure etc. of desired shape by welded joint (weldingjoint).For this reason, in these steel, viewpoint from the security (safety) of guaranteeing structure etc., the intensity of mother metal self and good-toughness are indispensable, and (toughness of welding metal (weld metal) and heat affected zone (heat-affected zone) is also good also to require the weld part of welding joint (weld joint).
As the flexible metewand (evaluation standards) of steel, the main in the past absorption energy (absorbed energy) that records by Charpy impact test (Charpy impact test) that adopts.But, in recent years,, adopt crack tip opening displacement test (Crack Tip Opening Displacement Test, below brief note is " CTOD test ") in order further to improve reliability (reliability) more.The generation resistance (occurrence resistance) of brittle rupture (brittle fracture) is estimated in this test by the amount of opening (value of opening displacement) (amount of plastic deformation (value of plastic deformation)) that makes flexible evaluation portion produce the test film generation three-point bending (three-point bending) of prefabricating fatigue crack (fatigue precrack) and the crackle bottom (bottom of crack) that mensuration ruptures preceding.
But, usually can implement multilayer welding (multi-pass welding) by thicker steel to the thickness of slab that uses in the such use, in such welding, because heat affected zone bears complicated thermal history (thermal history), therefore exist and be easy to generate the local embrittlement zone, especially the problem that reduces greatly of toughness of hot again portion of welded bonds portion (bond) (border of welding metal and mother metal) and two-phase zone (inter-criticallyreheated zone) (in first circulation of welding, become coarse grain, in second circulation, be heated to form the zone in the two-phase zone of α and γ).This be because, welded bonds portion is exposed to the open air to be pressed on towards under the high temperature of fusing point, thereby makes thickization of austenite crystal (austenite grain), then becomes fragile upper bainite tissue (upper bainiticstructure) easily mutually by cooling off.In addition, owing to generate Widmannstatten structure (Widmannstattenstructure), island martensite body (island martensite in welded bonds portion, M-A constituent) and so on embrittlement tissue (embrittlement structure), so toughness further reduces.
As the countermeasure of reply the problems referred to above, for example, suppress the technology of thickization of austenite crystal or the technology of utilizing ferrite transformation nuclear (nucleus of ferritetransformation) practicability by fine dispersion TiN in steel.In addition, following technology is disclosed in special fair 03-053367 communique of Japan or Japanese kokai publication sho 60-184663 communique: by (REM (rare-earth metal) also is dispersed in the steel minuteness particle with the compound interpolation rare earth element of Ti, can suppress the austenite crystal growth, improve the toughness of weld part.In addition, also proposed to make the technology that oxide compound (oxide) dispersive technology, the combination ferrite generative capacity of BN and the oxide compound of Ti disperse and add Ca or REM control the form (shape) of sulfide (sulfide) thus improve the flexible technology.
On the other hand, the hot again portion in above-mentioned two-phase zone, promptly, when initial welding, expose the zone under the high temperature that is pressing on towards fusing point to the open air, also be the zone that becomes ferrite and austenitic two-phase zone by the reheat in follow-up when welding, its most crisp reason is: the reheat during by the later welding of second passage, and carbon enrichment is at austenite region, it generates the fragility that comprises the island martensite body in process of cooling bainite structure reduces toughness.Therefore, as its countermeasure, following technology being disclosed: suppresses the generation of island martensite body by low C, low Siization, and then guarantee strength of parent (for example with reference to Japanese kokai publication hei 05-186823 communique) by adding Cu.
In addition, the method that suppresses the generation of embrittlement tissue as above-mentioned reheat by when welding, following technology is disclosed in TOHKEMY 2007-231312: the addition of the Ca that adds for the form of controlling sulfide is controlled at suitable scope, on this basis, improve the toughness (CTOD characteristic) of welding heat affected zone by interpolation Ni.
Yet the problems referred to above that the toughness of heat affected zone reduces are though compare the improvement of making to a certain degree with above-mentioned prior art, the still residual problems that have some needs to solve.For example, in utilizing the technology of TiN, this acts in the welded bonds portion of the temperature range that is heated to TiN fusion and disappears, not only so, because flexible takes place and significantly reduces in the embrittlement of the matrix that solid solution Ti and solid solution N cause sometimes.In addition, in the technology of the oxide compound that utilizes Ti, exist the oxide compound can not fine full and uniformly dispersive problem.And then, along with the maximization of boats and ships, marine structures etc., further require high strength, wall thickening in recent years for the steel that in them, use.In order to satisfy these requirements, opposite with the technology of Japanese kokai publication hei 05-186823 communique, it is effective adding a large amount of alloying elements.But the heavy addition of alloying element, causes the problem of the toughness reduction of welding heat affected zone at the generation of the embrittlement tissue that the reheat when exist promoting by welding causes.In addition, in the disclosed technology, as the countermeasure that is used to tackle high strength and wall thickening, need to add the effective Ni of high malleableize (effect of solid solution Ni) to matrix among the TOHKEMY 2007-231312, the costliness that becomes aspect cost becomes problem.
Therefore, in order to solve the problems referred to above that prior art has, the objective of the invention is to, a kind of high-strength steel and preferred manufacture method thereof are provided, even this high-strength steel is under the situation of the heavy-walled high tensile steel plate of the addition that increases alloying element for having to, the intensity of mother metal and toughness are also good, and the toughness of welding heat affected zone is also good.
Summary of the invention
The present invention is a kind of high-strength steel, it is characterized in that, having following one-tenth is grouped into: contain C:0.03～0.10 quality %, below the Si:0.30 quality %, Mn:1.60～2.30 quality %, below the P:0.015 quality %, below the S:0.005 quality %, Al:0.005～0.06 quality %, Nb:0.004～0.05 quality %, Ti:0.005～0.02 quality %, N:0.001～0.005 quality %, Ca:0.0005～0.003 quality %, and, Ca, the content of S and O satisfies following (1) formula, surplus is made up of Fe and unavoidable impurities
0＜(Ca-(0.18+130×Ca)×O)/1.25/S＜1 …(1)
Wherein, Ca, S and O represent the content (quality %) of each element.
In addition, high-strength steel of the present invention, it is characterized in that, on the basis that mentioned component is formed, also contain and be selected from that B:0.0003～0.0025 quality %, V:0.2 quality % are following, Cu:1 quality % is following, Ni:2 quality % is following, Cr:0.7 quality % is following and Mo:0.7 quality % one or more in following.
In addition, the invention allows for a kind of manufacture method of high-strength steel, it is characterized in that, after steel billet is heated to 1050～1200 ℃, the rolling rate of accumulation that is applied in the temperature range more than 950 ℃ is more than 30%, the rolling rate of accumulation in being lower than 950 ℃ temperature range is 30～70% hot rolling, then, carry out leading portion cooling and back segment cooling, the leading portion cooling stops temperature from the hot rolling end temp with 5～45 ℃ of/second coolings that are cooled between 600～450 ℃, back segment cooling from described leading portion cooling stop temperature with more than 1 ℃/second and 5 ℃ of/second coolings that are cooled to below 450 ℃ of less than stop temperature, wherein, described steel billet has following one-tenth and is grouped into: contain C:0.03～0.10 quality %, below the Si:0.30 quality %, Mn:1.60～2.30 quality %, below the P:0.015 quality %, below the S:0.005 quality %, Al:0.005～0.06 quality %, Nb:0.004～0.05 quality %, Ti:0.005～0.02 quality %, N:0.001～0.005 quality %, Ca:0.0005～0.003 quality %, and, Ca, the content of S and O satisfies following (1) formula, surplus is made up of Fe and unavoidable impurities
0＜(Ca-(0.18+130×Ca)×O)/1.25/S＜1 …(1)
Wherein, Ca, S and O represent the content (quality %) of each element.
In addition, manufacture method of the present invention, it is characterized in that, described high-strength steel also contains and is selected from that B:0.0003～0.0025 quality %, V:0.2 quality % are following, Cu:1 quality % is following, Ni:2 quality % is following, Cr:0.7 quality % is following and Mo:0.7 quality % one or more in following on the basis that mentioned component is formed.
In addition, manufacture method of the present invention is characterized in that, the cooled steel of back segment is implemented 450～650 ℃ temper.
Can make yielding stress according to the present invention at an easy rate and be the high strength more than the 460MPa and the also good high-strength steel of toughness (CTOD characteristic) of the heat affected zone after good-toughness and the welding with mother metal, therefore, the maximization contribution for boats and ships, marine structures etc. is very big.
Description of drawings
Fig. 1 is the figure that the leading portion speed of cooling of expression after the hot rolling (stopping the speed of cooling of temperature from the cooling between rolling end temp to 600～450 ℃) given the influence that the mother metal characteristic brings.
Embodiment
The contriver furthers investigate for the strength of parent that can improve the heavy-walled high-strength steel and toughness and the flexible method that can improve welding heat affected zone.It found that, because the toughness of welding heat affected zone reduces the generation that causes the embrittlement tissue, therefore, when having suppressed welding for the toughness that improves this welding heat affected zone on the basis of thickization of the austenite crystal in the zone of heat, and then the ferrite transformation during for the cooling after promoting to weld and phase transformation nuclear is evenly disperseed imperceptibly is effective.
Therefore, the inventor further studies the method for the generation that suppresses above-mentioned embrittlement tissue, found that, it is effectively that the addition of the Ca that adds for the form of controlling sulfide is controlled at proper range, and to add Mn for the toughness (CTOD characteristic) that improves welding heat affected zone be effective.
In addition, study for the intensity of mother metal and the influence that toughness is brought for rolling condition, found that, if with the cooling setpoint after rolling is to cool off, also suitably control speed of cooling separately by two stages that the big back segment that leading portion cools off and speed of cooling the is little cooling of speed of cooling is formed, then the steel plate tissue becomes the tissue that acicular ferrite is a main body, can produce the intensity of mother metal and the high-strength steel of good-toughness.And then, in order further to improve the intensity and the toughness of mother metal, importantly effectively utilize the big Nb of effect that in austenitic low temperature range, forms non-recrystallization zone (nonrecrystallization zone).And, by these technology of appropriate combination, finished the present invention first.
Below basic technological thought of the present invention is described.
Of the present invention first is characterised in that, in order to improve the toughness of welding heat affected zone (welded heataffected zone), effectively utilizing morphology Control (shapecontrol) with sulfide (sulfide) is the crystallization (crystallization) of the compound (CaS) of the Ca that adds of purpose.Compare this CaS with oxide compound crystallization takes place at low temperatures, therefore can fine equably dispersion (finedispersion).And, by with the addition of CaS and the dissolved oxygen amount (dissolved oxygen amount) in the molten steel (molten steel) when adding be controlled at proper range, even behind the CaS crystallization, also can guarantee solid solution S, form complex sulfide (complex sulfide) thereby therefore on the surface of CaS, separate out MnS.Known this MnS has ferrite core generative capacity (potential for ferrite nucleus), and then, around the MnS that separates out, can form the dilution band (Mn depleted zone) of Mn, therefore more can promote ferrite transformation (ferritetransformation).By increasing the Mn addition in the steel, thereby more effectively embody the effect of this Mn dilution band.And, on the MnS that separates out, also separate out ferrite product nucleus such as TiN, BN, AlN, therefore can further promote ferrite transformation.
In addition, by increasing the Mn addition, can not improve strength of parent effectively at a large amount of island martensite bodies that generate as the embrittlement tissue of welding heat affected zone.This be because, by increasing the Mn addition, the island martensite body that generates in the process of cooling after welding resolves into cementite easily, thus the minimizing of the island martensite body in the heat affected zone tissue.The result of these effects can guarantee the toughness of welding heat affected zone and need not to add Ni.
By above-mentioned technology, the ferrite transformation product nucleus that at high temperature also can not fuse is disperseed imperceptibly, make the miniaturization of organizing of welding heat affected zone, and, by suppressing island martensite body (island martensite as far as possible, M-A constituent) generation can access high toughness.In addition, thermal cycling (heat cycle) during by multilayer welding (multilayer welding), even in the zone that is reheated into the two-phase zone, also the tissue owing to initial welding heat affected zone is made that by miniaturization the toughness of phase change region does not improve, and then the also miniaturization of the austenite crystal of phase transformation again, thereby the flexible reduction can be suppressed at lesser extent.
Of the present invention second is characterised in that, the cooling after the Steel Rolling is divided into leading portion cooling and back segment two stages of cooling, and is controlled to leading portion refrigerative speed of cooling greater than back segment refrigerative speed of cooling.Below, based on experimental result this feature is described.
With basal component is after the steel billet of C:0.08 quality %, Si:0.2 quality %, Mn:1.8 quality % is heated to 1150 ℃, be 40% in the rolling rate of the accumulation more than 950 ℃, be lower than that 950 ℃ the rolling rate of accumulation is 50%, rolling end temp is after 850 ℃ the hot rolling, enforcement with 5～45 ℃/second, more preferably 5～20 ℃/second speed of cooling (cooling rate) from rolling end temp be cooled to 500 ℃ leading portion cooling and and then be cooled to 350 ℃ back segment cooling with 3 ℃/second speed of cooling, air cooling then makes the Plate Steel of thickness of slab 10～50mm.For this Plate Steel, tensile strength characteristics and the property of toughness under-40 ℃ (summer absorbs energy than impacting) have been measured.
Fig. 1 gives the figure of the influence that strength of parent and toughness brings for show the leading portion speed of cooling based on the said determination result, as seen, be controlled in 5～45 ℃/second the scope by being cooled to 500 ℃ leading portion refrigerative speed of cooling, can access yielding stress and be the above high strength of 460MPa, vE-40 and ℃ be the above intensity-good steel plate of tough sexual balance (balance) of 200J from rolling end temp.
In addition, also become the tissue of acicular ferrite (acicularferrite) as can be known based on above-mentioned speed of cooling refrigerative steel plate.Usually, under the situation that will obtain high-strength steel, if become the thicker upper bainite tissue that contains island martensite body etc. between lath (lath), then toughness reduces widely.Therefore, in order to take into account high strength and high tenacity, need make fine acicular ferrite structure by consideration rolling condition etc.But, the contriver finds: by the cooling after rolling being divided into the back segment cooling slower than the leading portion cooling of leading portion cooling and speed of cooling, and suitable control speed of cooling separately, can make the tissue that acicular ferrite is a main body, and obtain having good intensity-toughness equilibrated steel plate.This be because: by accelerating the speed of cooling of leading portion, can improve phase transformation karyogenesis density (nucleation density), make microstructure after phase transformation become fine and close acicular ferrite structure but not thick bainite structure.And then find: compare with the speed of cooling of leading portion when too fast when the speed of cooling of back segment, generate the island martensite body, and make the toughness variation of mother metal, on the other hand, cross when slow when the speed of cooling of back segment, cause the intensity of mother metal to reduce, therefore it need be controlled in the suitable scope.
The present invention is based on above-mentioned opinion and finishes.
Below the one-tenth that should have high-strength steel of the present invention be grouped into and describe.
C:0.03～0.10 quality %
C is the element to the intensity effect maximum of steel, in order to ensure using the required intensity (YS 〉=460MPa), need contain more than the 0.03 quality % of steel as constructing.But on the contrary, if when the content of C is too much, therefore the cold cracking in the time of then can causing the reduction of base metal tenacity or welding, is limited to 0.10 quality % on the C content.
Below the Si:0.30 quality %
Si is as deoxidation material and the composition that adds in order to make the steel high strength.In order to obtain this effect, preferably add the above Si of 0.01 quality %.But, when the content of Si surpasses 0.30 quality %, the toughness of mother metal and weld part is reduced, therefore, it need be controlled at below the 0.30 quality %.Be preferably the scope of 0.01～0.20 quality %.
Mn:1.60～2.30 quality %
Mn is effective elements in order to ensure the intensity of mother metal, in the present invention, be in order to promote the miniaturization of organizing of welding heat affected zone, and suppress the formation of embrittlement tissue as far as possible, thereby improve the toughness (CTOD characteristic) of welding heat affected zone and the important element that adds.In order to obtain this effect, need to add the above Mn of 1.60 quality %.On the other hand, when the content of Mn surpasses 2.30 quality %, can significantly reduce the toughness of mother metal and weld part, therefore it is controlled at below the 2.30 quality %.Be preferably the scope of 1.65～2.15 quality %.
Below the P:0.015 quality %
P is the impurity of sneaking into inevitably, when the content of P surpasses 0.015 quality %, can reduce the toughness of mother metal and weld part, therefore it is controlled at below the 0.015 quality %.Be preferably below the 0.010 quality %.
Below the S:0.005 quality %
S is the impurity of sneaking into inevitably, when the content of S surpasses 0.005 quality %, can reduce the toughness of mother metal and weld part, therefore it is controlled at below the 0.005 quality %.Be preferably below the 0.0035 quality %.
Al:0.005～0.06 quality %
Al is the element that adds in order to make deoxidation of molten steel (deoxidation), need contain more than the 0.005 quality %.On the other hand, when adding the Al that surpasses 0.06 quality %, can reduce the toughness of mother metal, and owing to the caused dilution of welding is blended into welding metal portion, thereby toughness is reduced, therefore it need be controlled at below the 0.06 quality %.Be preferably 0.010～0.055 quality %.
Nb:0.004～0.05 quality %
Because Nb forms non-recrystallization zone (non-recrystallzation zone) in austenitic temperature range, therefore rolling by enforcement in this temperature range, can realize the miniaturization and the high tenacity of mother metal tissue.In addition, by implementing temper, can realize precipitation strength (precipitation strengthening) in rolling and cooling back.Therefore, from the viewpoint of the reinforcement that realizes steel, Nb is important interpolation element.In order to obtain above-mentioned effect, need to add the above Nb of 0.004 quality %.But, when excessively adding Nb, make the toughness variation of weld part to surpass 0.05 quality %, therefore, its upper limit is controlled at 0.05 quality %.
Ti:0.005～0.02 quality %
Because Ti form with TiN when molten steel solidification is separated out, suppress austenitic thickization in the weld part, and become ferritic phase transformation nuclear, therefore, help the high tenacityization of weld part.In order to obtain this effect, need to add the above Ti of 0.005 quality %.But when the Ti that adds was lower than 0.005 quality %, this effect was little, on the other hand, when the Ti that adds surpasses 0.02 quality %, thickization of TiN particle, the flexible that can't obtain mother metal and weld part improves effect.Therefore, the addition of Ti is controlled to be the scope of 0.005～0.02 quality %.
N:0.001～0.005 quality %
N is the required element of TiN for thickization that forms the tissue that suppresses weld part, needs to add more than the 0.001 quality %.On the other hand, when the N that adds surpassed 0.005 quality %, because solid solution N can significantly reduce the toughness of mother metal and weld part, therefore, its upper limit was controlled to be 0.005 quality %.In addition, in order in the pinning (pinning) of thickization that suppresses tissue, to form the TiN of q.s, preferably N is controlled to be the scope of 0.003～0.005 quality %.
Ca:0.0005～0.003 quality %
Ca improves the flexible element by fixing S.In order to embody this effect, need to add the Ca of at least 0.0005 quality %.But when the content of Ca surpassed 0.003 quality %, this effect was saturated, and therefore, the Ca of interpolation is limited to the scope of 0.0005～0.003 quality %.
0＜(Ca-(0.18+130×Ca)×O)/1.25/S＜1
In order to make the fine dispersion of ferrite transformation product nucleus CaS of at high temperature also not fusing, the content of Ca, S and O need satisfy the relation of following (1) formula.Wherein, Ca, S, O represent the content (quality %) of each element.
0＜(Ca-(0.18+130×Ca)×O)/1.25/S＜1 …(1)
In the above-mentioned formula (Ca-(0.18+130 * Ca) * O)/(1.25/S) be the value of expression to the ratio of the atomic percent of effective Ca of the morphology Control of sulfide and S, can infer the form of sulfide by this value and (hold field etc., " iron と Steel ", Japan iron and steel institute, the 66th year (1980), the 3rd phase, P.354～362).
That is, in that (((value of 0.18+130 * Ca) * O)/1.25/S) is under the situation below 0 to Ca-, non-crystallizableization of CaS.Therefore, S separates out with the independent form of MnS, thus can't realize as the main starting point of the present invention, the ferrite product nucleus is in the fine dispersion of welding heat affected zone.In addition, the MnS that separates out separately is elongated when steel plate rolling, causes that the toughness of mother metal reduces.
On the other hand, in that (((value of 0.18+130 * Ca) * O)/1.25/S) is under the situation more than 1 to Ca-, S is fixed by Ca fully, can not separate out the MnS that works as the ferrite product nucleus on CaS, thereby can not give full play to the function of complex sulfide as the ferrite product nucleus.
Relative therewith, satisfy at Ca, S, O under the situation of above-mentioned (1) formula, on CaS, separate out MnS and form complex sulfide, can bring into play effect effectively as the ferrite product nucleus.In addition, (((value of 0.18+130 * Ca) * O)/1.25/S) is preferably 0.2～0.8 scope to Ca-.
In order to improve intensity and toughness, high-strength steel of the present invention on the basis of above-mentioned essential composition, can also further contain be selected among B, V, Cu, Ni, Cr and the Mo more than a kind or 2 kinds.
B:0.0003～0.0025 quality %
B is to the austenite grain boundary segregation, suppresses the ferrite transformation that is caused by crystal boundary and improves the percentage of bainite structure, thereby have the effect that makes the steel high strength.This effect obtains by the B that adds more than the 0.0003 quality %.But when the B ultrasonic that adds was crossed 0.0025 quality %, toughness reduced on the contrary.The preferred scope of B is 0.0005～0.002 quality %.
Below the V:0.2 quality %
V improves effective elements to the intensity of mother metal and flexible, and, the element of still separating out and working as the ferrite product nucleus with the form of VN.In order to obtain this effect, preferably add the above V of 0.01 quality %.But, when addition surpasses 0.2 quality %, can cause toughness to reduce on the contrary, the therefore preferred following V of 0.2 quality % that adds.More preferably below the 0.15 quality %.
Below the Cu:1 quality %
Cu is the element with effect of the intensity that improves steel.In order to obtain this effect, preferably add the above Cu of 0.05 quality %.But, when the content of Cu surpasses 1 quality %, can produce red brittleness and make the surface texture variation of steel plate, therefore, preferably add the Cu of the following scope of 1 quality %.More preferably below the 0.8 quality %.
Below the Ni:2 quality %
Ni is the CTOD characteristic effective elements to intensity that improves steel and raising welding heat affected zone.In order to obtain this effect, preferably add the above Ni of 0.05 quality %.But because Ni is expensive element, therefore, its upper limit is preferably 2.0 quality %.Add under the situation of the Mn more than 1.6% like this in the application, from the viewpoint that reduces cost, the content of Ni more preferably is lower than 0.3%.
Below the Cr:0.7 quality %
Cr is the high strength effective elements to mother metal.In order to obtain this effect, preferably add the above Cr of 0.05 quality %.But if heavy addition Cr can cause detrimentally affect to toughness on the contrary, therefore, its upper limit is preferably 0.7 quality %.More preferably below the 0.5 quality %.
Below the Mo:0.7 quality %
Same with Cr, Mo is the high strength effective elements to mother metal.In order to obtain this effect, preferably add the above Mo of 0.05 quality %.But if heavy addition Mo causes detrimentally affect to toughness on the contrary, therefore, its upper limit is preferably 0.7 quality %.More preferably below the 0.5 quality %.
Then, the tissue to high-strength steel of the present invention describes.
The tissue of high-strength steel of the present invention is that acicular ferrite is the tissue of main body, and its preferred area occupation ratio is more than 60%, more preferably more than 70%.The area occupation ratio of acicular ferrite is lower than at 60% o'clock, and thick upper bainite tissue increases, thereby toughness reduces.In addition, the upper limit of area occupation ratio has no particular limits.In addition, the acicular ferrite structure of high-strength steel of the present invention is bainite ferrite form, that intragranular dislocation desity is high (bainetic ferrite) with fine acicular or lath-shaped, and they are different with polygonal ferrite (polygonal ferrite) and thick upper bainite tissue (coarse upper bainite).
Then, the manufacture method to high-strength steel of the present invention describes.
High-strength steel of the present invention is preferably made in the following manner: be adjusted to the above-mentioned molten steel that one-tenth of the present invention is grouped into that is fit to by the usual method melting of using converter, electric furnace, vacuum melting stove etc., then, make the former material of steel such as steel billet through common operations such as continuous casting or ingot casting-split rolling methods after, the former material of this steel is carried out hot rolling, thereby produce thick high-strength steel.The Heating temperature of the former material of steel that carried out before hot rolling at this moment, need be 1050～1200 ℃ scope.Heating temperature is that the reason more than 1050 ℃ is, the casting flaw that positively exists in the former material of pressure welding steel by hot rolling.But, when being heated to when surpassing 1200 ℃ temperature, thickization of when solidifying, separating out of TiN, the toughness of mother metal and weld part reduces, thereby Heating temperature need be limited in below 1200 ℃.
Afterwards, the rolling rate of accumulation that the former material of the steel that is heated to said temperature is implemented in the temperature range more than 950 ℃ is more than 30%, be 30～70% hot rolling in the rolling rate of accumulation that is lower than 950 ℃ temperature range, makes the high-strength steel with predetermined thickness of slab.The rolling rate of accumulation that is implemented in the temperature range more than 950 ℃ is that the hot rolled reason more than 30% is, by being controlled at more than 30% in the rolling rate of the accumulation in this temperature range, austenite crystal generation recrystallize, organize miniaturization thereby can make, when the rolling rate of accumulation is lower than 30%, the unusual thick grain that generates during heating is residual, brings detrimentally affect for the toughness of mother metal.
In addition, the rolling rate of accumulation (cumulative draft) that is implemented in the temperature range that is lower than 950 ℃ is that 30～70% hot rolled reason is, because rolling austenite crystal recrystallize fully not in this temperature range, thereby the austenite crystal after rolling is in and is deformed into flat state, becomes the high steel of internal strain (internal strain) that inside comprises a large amount of deformation bands defectives such as (deformation band).And, its internal energy of accumulating as after ferrite transformation motivating force and play a role, promote ferrite transformation.But rolling rate is lower than at 30% o'clock, and the above-mentioned internal energy of being accumulated is insufficient, therefore, is difficult to take place ferrite transformation, and base metal tenacity reduces.On the other hand, when rolling rate surpasses 70%, can promote the generation of polygonal ferrite on the contrary, suppress the generation of acicular ferrite, become and to take into account high strength and high tenacity.
Cooling after follow-up hot rolling finishes is divided into leading portion cooling and back segment cooling, and the speed of cooling that makes the former is relatively greater than the latter's speed of cooling, promptly, in the leading portion cooling, need be with 5～45 ℃/second, preferred 5～20 ℃/second, more preferably 6～16 ℃/second speed of cooling, be cooled to from the hot rolling end temp that cooling between 600～450 ℃ stops temperature, the cooling that preferably is cooled between 580～480 ℃ from the hot rolling end temp stops temperature; After back segment cooling in, need be with more than 1 ℃/second and be lower than 5 ℃/second, more preferably 2～4.5 ℃/second speed of cooling, stop temperature from the leading portion refrigerative and be cooled to back segment cooling below 450 ℃ and stop temperature, preferably stop the cooling that temperature is cooled between 400～250 ℃ and stop temperature from the leading portion refrigerative.
When the leading portion refrigerative stops temperature and is higher than the said temperature scope, almost there is not the increase of intensity, on the contrary, and when being lower than the said temperature scope, the toughness variation.In addition, the leading portion speed of cooling is lower than above-mentioned scope in limited time becomes polygonal ferrite and is the tissue of main body and can't obtain the raising of intensity down, on the contrary, surpasses going up in limited time of above-mentioned scope, and toughness reduces.And then, back segment refrigerative cooling stop temperature being higher than the said temperature scope in limited time, the rising of intensity becomes insufficient.In addition, the back segment speed of cooling is lower than the following of above-mentioned scope prescribes a time limit, and strength of parent is not enough, on the contrary, prescribes a time limit on above above-mentioned scope, and the toughness of mother metal reduces.In addition, compare with the speed of cooling of leading portion when too fast, generate the island martensite body, make the toughness variation of mother metal when the speed of cooling of back segment.
In addition, among the present invention,, can be implemented in the temper (tempering) of 450～650 ℃ temperature range to above-mentioned cooled steel in order to reduce remaining internal stress.When the temper temperature is lower than 450 ℃, residual stress (residual stress) to remove effect little, on the other hand, when the temper temperature uprises and when surpassing 650 ℃, various carbonitrides (carbonitride) are separated out and precipitation strength are taken place, and toughness reduces, so not preferred.
As described above, in the manufacture method of high-strength steel of the present invention, importantly, control two stage cooling conditionss after suitable rolling rate corresponding with the hot rolled rolling temperature and suitable controlled rolling finish, especially by making leading portion refrigerative speed of cooling greater than back segment refrigerative speed of cooling, mother metal becomes the tissue that acicular ferrite is a main body, can access intensity-good steel of tough sexual balance.
In addition, in the present invention, content by making the N in the chemical ingredients surpasses 0.0030%, make leading portion refrigerative speed of cooling for greater than 20 ℃/second and below 45 ℃/second, to make the leading portion refrigerative stop temperature be more than 450 ℃ and be lower than 500 ℃, can produce the yielding stress with mother metal at an easy rate is the also good high-strength steel of toughness (CTOD characteristic) of the heat affected zone after the above high strength of 550MPa and good-toughness and the welding.
Embodiment
With steel billet with table 1-1 and the table No.1 that becomes to be grouped into～31 shown in the 1-2 is former material, implements hot rolling and leading portion cooling and back segment and cool off under the condition shown in table 2-1 and the table 2-1, produces the Plate Steel of thickness 25～80mm.In addition, the temperature of putting down in writing among table 2-1 and the table 2-2 is by calculating the temperature at thickness of slab 1/4 place of trying to achieve by radiating thermometric steel plate skin temperature.Cut sample from the Plate Steel that obtains like this, supply in tension test and Charpy impact test.In the tension test, the mode that the y direction of sentencing test film from the thickness of slab 1/4 of Plate Steel is parallel to rolling direction cuts JIS4 tension test sheet, measures yielding stress (YS), tensile strength (TS).In addition, in the Charpy impact test, cut JIS4 shock test sheet along the rolling width direction, measure the absorption energy (vE-40 ℃) under-40 ℃ the temperature from the thickness of slab 1/4 of each Plate Steel.Subsequently, it is good the test film that satisfies YS 〉=460MPa, TS 〉=570MPa and vE-40 ℃ 〉=200J all conditions to be evaluated as the mother metal characteristic.
In addition, in principle, for from YS, TS and the vE-40 ℃ of test board that the Plate Steel that all satisfies said reference cuts as the mother metal characteristic, process monolateral double V-groove (single bevelgroove) (30 ° of groove angles (bevel angle)), importing heat is the co3 gas arc welding (CO of 25kJ/cm
2Arc welding), make welding joint, the CTOD test film from this welding joint straight line welded bonds (straight bond) portion at monolateral double V-groove of cutting imposes otch carries out the CTOD test under-10 ℃ temperature.In addition, the making of CTOD test film and test conditions carry out according to British specification BS7448.In addition, cutting with the incision site is the JIS4 shock test sheet of welded bonds portion, carries out Charpy impact test under-40 ℃ temperature, measures to absorb energy (vE-40 ℃).
Above-mentioned test-results is put down in writing simultaneously and is shown among table 2-1 and the table 2-2.By these results as can be known, the steel plate of example of the present invention, yielding stress (YS) and the above summer ratio of 200J with the above mother metal of 460MPa absorb energy (vE-40 ℃), the intensity of mother metal, toughness are all good, and vE-40 ℃ of co3 gas arc welding joint welded bonds portion also for more than the 200J, the CTOD value is more than the 0.10mm, and the toughness of welding heat affected zone is also good.Relative therewith, at the steel of scope of the present invention comparative example in addition, can only obtain the steel plate of above-mentioned any characteristic variation more than.
In addition, in the steel plate of example of the present invention, N surpasses steel plate No.11～17 of 0.0030 quality %, and by the pinning effect of TiN, the CTOD of weld part is good, is more than 0.45.
And then, in the steel plate of example of the present invention, leading portion refrigerative speed of cooling after N surpasses 0.0030 quality %, hot rolling surpass 20 ℃/second and below 45 ℃/second and the leading portion refrigerative to stop temperature be more than 450 ℃ and be lower than steel plate No.15 and the No.16 that makes under 500 ℃ the condition, the yielding stress that all has mother metal is the above high strength of 550MPa.
Utilize possibility on the industry
High-strength steel of the present invention is not only applicable to boats and ships or marine structures, pipeline steel pipe, pressurized vessel, but also is applicable to the steel structure that welding assembly forms in the fields such as building/building.
Claims (6)
1. high-strength steel, it has following one-tenth and is grouped into:
Contain that C:0.03～0.10 quality %, Si:0.30 quality % are following, Mn:1.60～2.30 quality %, P:0.015 quality % following, S:0.005 quality % is following, Al:0.005～0.06 quality %, Nb:0.004～0.05 quality %, Ti:0.005～0.02 quality %, N:0.001～0.005 quality %, Ca:0.0005～0.003 quality %
And the content of Ca, S and O satisfies following (1) formula, and surplus is made up of Fe and unavoidable impurities,
0＜(Ca-(0.18+130×Ca)×O)/1.25/S＜1 …(1)
Wherein, Ca, S and O represent the quality % content of each element.
2. high-strength steel according to claim 1, it also contains and is selected from that B:0.0003～0.0025 quality %, V:0.2 quality % are following, Cu:1 quality % is following, Ni:2 quality % is following, Cr:0.7 quality % is following and Mo:0.7 quality % one or more in following on the basis that mentioned component is formed.
3. the manufacture method of a high strength steel; With behind heating steel billet to 1050～1200 ℃; The rolling rate of accumulation in the temperature range more than 950 ℃ of being applied to is more than 30%, the rolling rate of accumulation in being lower than 950 ℃ temperature range is 30～70% hot rolling; Then; Carry out leading portion cooling and back segment cooling; The leading portion cooling stops temperature from the hot rolling end temp with 5～45 ℃ of/second coolings that are cooled between 600～450 ℃; Back segment cooling from described leading portion cooling stop temperature with more than 1 ℃/second and 5 ℃ of/second coolings that are cooled to below 450 ℃ of less than stop temperature
Wherein, described steel billet has following one-tenth and is grouped into:
Contain that C:0.03～0.10 quality %, Si:0.30 quality % are following, Mn:1.60～2.30 quality %, P:0.015 quality % following, S:0.005 quality % is following, Al:0.005～0.06 quality %, Nb:0.004～0.05 quality %, Ti:0.005～0.02 quality %, N:0.001～0.005 quality %, Ca:0.0005～0.003 quality %
And the content of Ca, S and O satisfies following (1) formula, and surplus is made up of Fe and unavoidable impurities,
0＜(Ca-(0.18+130×Ca)×O)/1.25/S＜1 …(1)
Wherein, Ca, S and O represent the quality % content of each element.
4. the manufacture method of high-strength steel according to claim 3, wherein, described high-strength steel also contains and is selected from that B:0.0003～0.0025 quality %, V:0.2 quality % are following, Cu:1 quality % is following, Ni:2 quality % is following, Cr:0.7 quality % is following and Mo:0.7 quality % one or more in following on the basis that mentioned component is formed.
5. according to the manufacture method of claim 3 or 4 described high-strength steels, wherein, the cooled steel of back segment is implemented 450～650 ℃ temper.
6. according to the manufacture method of each described high-strength steel in the claim 3～5, wherein, described leading portion cooling is cooled off with 5～20 ℃/second.
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Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0694569B2 (en) * | 1987-02-27 | 1994-11-24 | 新日本製鐵株式会社 | Manufacturing method of steel with excellent low temperature toughness in the heat affected zone |
| JP2002317242A (en) * | 2001-04-19 | 2002-10-31 | Nkk Corp | High tensile strength steel for welding structure used under low temperature having excellent weld heat affected zone toughness |
| JP2007231312A (en) * | 2006-02-28 | 2007-09-13 | Jfe Steel Kk | High-tensile-strength steel and manufacturing method therefor |
| JP2007277681A (en) * | 2006-04-11 | 2007-10-25 | Nippon Steel Corp | Method for manufacturing high-strength steel sheet with superior toughness in welding heat-affected zone |
Family Cites Families (12)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS601929B2 (en) * | 1980-10-30 | 1985-01-18 | 新日本製鐵株式会社 | Manufacturing method of strong steel |
| JPS5877529A (en) * | 1981-10-31 | 1983-05-10 | Nippon Steel Corp | Manufacture of high tensile thick steel |
| JPS60152626A (en) | 1984-01-20 | 1985-08-10 | Kawasaki Steel Corp | Method for stabilizing toughness of high tension steel for welded structure |
| JPS60184663A (en) | 1984-02-29 | 1985-09-20 | Kawasaki Steel Corp | High-tensile steel for low temperature service for welding with large heat input |
| JP3045856B2 (en) | 1991-11-13 | 2000-05-29 | 川崎製鉄株式会社 | Method for producing high toughness Cu-containing high tensile steel |
| JP3699657B2 (en) * | 2000-05-09 | 2005-09-28 | 新日本製鐵株式会社 | Thick steel plate with yield strength of 460 MPa or more with excellent CTOD characteristics of the heat affected zone |
| JP2002235114A (en) * | 2001-02-05 | 2002-08-23 | Kawasaki Steel Corp | Method for producing thick high tensile strength steel excellent in toughness of high heat input weld zone |
| JP3869747B2 (en) * | 2002-04-09 | 2007-01-17 | 新日本製鐵株式会社 | High-strength steel plate, high-strength steel pipe and manufacturing method excellent in deformation performance |
| EP1533392B1 (en) * | 2002-09-04 | 2017-08-02 | JFE Steel Corporation | Steel product for high heat input welding and method for production thereof |
| CN100513611C (en) * | 2005-03-31 | 2009-07-15 | 杰富意钢铁株式会社 | High-strength steel plate and process for production thereof, and high-strength steel pipe |
| JP4997805B2 (en) * | 2005-03-31 | 2012-08-08 | Ｊｆｅスチール株式会社 | High-strength thick steel plate, method for producing the same, and high-strength steel pipe |
| BRPI0615362B8 (en) * | 2005-08-22 | 2016-05-24 | Nippon Steel & Sumitomo Metal Corp | seamless steel pipe for process and line pipe for your production |
-
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- 2009-03-27 KR KR1020137005580A patent/KR20130035277A/en active Application Filing
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- 2009-03-27 WO PCT/JP2009/056906 patent/WO2009123292A1/en active Application Filing
- 2009-03-27 EP EP09726619.1A patent/EP2272994B1/en active Active
Patent Citations (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0694569B2 (en) * | 1987-02-27 | 1994-11-24 | 新日本製鐵株式会社 | Manufacturing method of steel with excellent low temperature toughness in the heat affected zone |
| JP2002317242A (en) * | 2001-04-19 | 2002-10-31 | Nkk Corp | High tensile strength steel for welding structure used under low temperature having excellent weld heat affected zone toughness |
| JP2007231312A (en) * | 2006-02-28 | 2007-09-13 | Jfe Steel Kk | High-tensile-strength steel and manufacturing method therefor |
| JP2007277681A (en) * | 2006-04-11 | 2007-10-25 | Nippon Steel Corp | Method for manufacturing high-strength steel sheet with superior toughness in welding heat-affected zone |
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Also Published As
| Publication number | Publication date |
|---|---|
| EP2272994A1 (en) | 2011-01-12 |
| KR20130035277A (en) | 2013-04-08 |
| EP2272994B1 (en) | 2014-11-12 |
| EP2272994A4 (en) | 2014-01-08 |
| KR20100116701A (en) | 2010-11-01 |
| KR20150094793A (en) | 2015-08-19 |
| WO2009123292A1 (en) | 2009-10-08 |
| JP2009263777A (en) | 2009-11-12 |
| CN105821313A (en) | 2016-08-03 |
| JP5439887B2 (en) | 2014-03-12 |
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Application publication date: 20110713 |