CN101343712A - Heavy steel plate for high-heat energy input soldering with excellent shortness fissure spread stop character - Google Patents
Heavy steel plate for high-heat energy input soldering with excellent shortness fissure spread stop character Download PDFInfo
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- CN101343712A CN101343712A CNA2008101274249A CN200810127424A CN101343712A CN 101343712 A CN101343712 A CN 101343712A CN A2008101274249 A CNA2008101274249 A CN A2008101274249A CN 200810127424 A CN200810127424 A CN 200810127424A CN 101343712 A CN101343712 A CN 101343712A
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
-
- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
-
- C—CHEMISTRY; METALLURGY
- C21—METALLURGY OF IRON
- C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/002—Bainite
Abstract
A steel plate is provided which still exhibits excellent HAZ toughness and remarkable brittle cracking propagation cessation characteristic even under high thermal input welding. The inventive thick steel plate is formed by properly regulating chemical ingredients and meets the thick steel plates of the following formulae (1) and (2), and includes an organization having an organization with more than 95 area % of bainite fraction, and dislocation density of the bainite (rho<1/2>) is 1.0X10<6> to 5.0X10<7> (m<-1>). [Ti]/[N] is not less than 1.5 but not more than 4.0 ... (1), X value is not less than 40 but not more than 160 ... (2), X value = 500[C]+32[Si]+8[Mn]-9[Nb]+14[Cu]+17[Ni]-5[Cr]- 25[Mo]-34[V], in the formula, [] represents contents of each element (mass%).
Description
Technical field
The present invention relates to for example Plate Steel that welded structure was suitable for of boats and ships and marine structure etc., relate in particular to the tenacity excellent of the heat affected zone (Heat Affected Zone:HAZ) after high heat energy input is welded, and the also excellent Plate Steel of brittlement crevasse crack propagation halt characteristic.
Background technology
In recent years, for example the maximization of container-ship etc. is pushed into, and uses thickness of slab to be the Plate Steel more than the 50mm.In order to weld such Plate Steel expeditiously, just requiring to import heat is above so high heat energy input welding of 40kJ/mm or superelevation heat energy input welding (following by " high heat energy input welding " representative).
Yet if carry out high heat energy input welding, HAZ is heated to pyritous austenite region Xu Leng afterwards, therefore has this thickization of tissue, the problem that the remarkable deterioration of HAZ toughness is such.Thus, the welding heat input of having in the past limit.
In order to reach good HAZ toughness with so high heat energy input welding, for example patent documentation 1 proposes, and reduces the C content in the Plate Steel, and limits the content of the P that unavoidably sneaks into, and the content with Nb and B is controlled at suitable scope in addition.Patent documentation 2 is to make the TiN that is present in the welding steel contain Nb among the inclusion energetically in addition, to suppress thick ferritic generation.Yet in these technology, when TiN deficiency or TiN are abundant, this thickization of TiN, insufficient from nail hole effects such as CaO oxide compounds, so there is further room for improvement in HAZ toughness.In addition, the brittlement crevasse crack propagation halt characteristic of mother metal steel plate described later is not paid attention to.
Patent documentation 3 proposes, and makes steel plate contain N more in large quantities, and suitably controls the content balance of Ti and B.Yet in this technology, the amount of separating out of TiN and BN is also insufficient, and fine inadequately, and in addition owing to do not add Nb and hardenability is low, so ferrite becomes thick, so there is further room for improvement in HAZ toughness.In addition, the brittlement crevasse crack propagation halt characteristic of mother metal steel plate described later is not paid attention to.
On the other hand, in the large structure of boats and ships, marine structure, low temperature storage container, pipeline steel pipe, building civil structure thing etc., follow the accident of brittle rupture to make a big impact for economy and environment, it is required the security of height.Therefore, in the employed steel of these works, require low-temperature flexibility more.Particularly nearest, even, destroy such viewpoint, also require brittlement crevasse crack propagation halt characteristic or inhibition (arrest) excellent under the low temperature from preventing to reach because of unexpected accident etc. makes when on the works be full of cracks taking place.
In recent years, the technology of organizing the ultra micro refinement of the skin section of steel also is suggested, its make brittlement crevasse crack propagation halt characteristic improve on effectively.As this technology, for example open in patent documentation 4, when brittlement crevasse crack propagation, effective to the raising of brittlement crevasse crack propagation halt characteristic at the shear lip (shear lip) (viscous deformation zone) that the steel skin section takes place.Yet, in this technology, need to implement to be considered to be in not allow manageable technology under the actual production scale, promptly, make it re-heat again after once only cooling off the steel skin section, and in re-heat, processed, obtain thus brittlement crevasse crack propagation halt characteristic is effectively organized.In addition, though ferrite utilization processing recrystallize can make it miniaturization, but processing recrystallize ferrite is grown up easily, and therefore structural stability shortcoming also has change owing to delicate thermal process to cause organizing inhomogeneous incident problem with material.
In addition, in patent documentation 5, propose to have a kind of method, its homogeneous with the Hardness Distribution of thickness of slab direction turns to purpose, use contains the steel of V, the slab of heating directly cooled off and give temperature head and that ferrite is begun after generating is rolling, in rolling way or near the temperature field of rolling back transformation temperature once again make it re-heat.This technology makes the precipitation-hardening of V only act on the thickness of slab central part, can make the Hardness Distribution homogenization of thickness of slab direction, thereby realizes the raising of brittlement crevasse crack propagation halt characteristic.Yet, suitably separate out in order to make the V compound, need carry out more complicated technology, and with the solution of above-mentioned this " tissue stabilization " on also direct correlation may not be arranged.
As above-mentioned, up to now, though also propose to have the various brittlement crevasse crack propagation halt characteristic good technical that are used to make, but all be difficult to the stable desirable tissue of reaching under the scale of industry, even practical situation are under the scale of industry, still expectation can be stablized the establishment of the technology that realizes brittlement crevasse crack propagation halt characteristic.In addition, in these technology, the HAZ toughness when making high heat energy input welding improves does not carry out any consideration.
[patent documentation 1] spy opens the 2003-166033 communique
[patent documentation 2] spy opens the 2004-218010 communique
[patent documentation 3] spy opens the 2005-200716 communique
[patent documentation 4] spy opens flat 4-141517 communique
[patent documentation 5] spy opens flat 8-253812 communique
Summary of the invention
The present invention is under this situation and do, and its purpose is, still demonstrates good HAZ toughness even provide a kind of when high heat energy input welding, and the also excellent Plate Steel of brittlement crevasse crack propagation halt characteristic.
The so-called Plate Steel of the present invention that can reach above-mentioned purpose, has following some main idea: contain the C:0.030～0.15% (meaning of quality % respectively, down together), Si:1.0% following (not containing 0%), Mn:0.8～2.0%, P:0.03% following (not containing 0%), S:0.01% following (not containing 0%), Al:0.01～0.10%, Ti:0.015～0.03%, B:0.0010～0.0035%, N:0.0050～0.01%, Ca:0.005% following (not containing 0%), O:0.01% following (not containing 0%), and be the Plate Steel that satisfies following (1) formula and (2) formula, and the tissue of this Plate Steel is that bainite branch rate is the above tissues of 95 area %, and the dislocation desity (ρ of bainite
1/2) be 1.0 * 10
6～5.0 * 10
7(m
-1).
1.5≤[Ti]/[N]≤4.0…(1)
40≤X value≤160 ... (2)
X value=500[C]+32[Si]+8[Mn]-9[Nb]+14[Cu]+17[Ni]-5[Cr]-25[Mo]-34[V]
(in the formula, [] represents the content (quality %) of each element.)
In Plate Steel of the present invention, from good low-temperature flexibility and HAZ flexible viewpoint, preferred satisfied as inferior important document: (a) temperature range in δ territory is below 40 ℃; (b) at degree of depth t/4 position (t=thickness of slab), Ti is that the median size of carbonitride is below the 43nm.Also have, so-called " Ti is a carbonitride ", its aim is also to comprise any one of the carbide, nitride and the carbonitride that contain Ti.
Plate Steel of the present invention contains aforesaid C, Si, Mn, P, S, Al, Ti, B, N, Ca, O with specified amount respectively, and satisfy aforementioned (1) formula and (2) formula, surplus is made of Fe and unavoidable impurities basically, but as required, contain again as inferior element also useful: (a) Nb:0.035% following (not containing 0%); (b) Cu:2.0% following (not containing 0%), Ni:2.0% following (not containing 0%) and below the Cr:2.0% among (not containing 0%) more than a kind; (c) Mo:1.0% following (not containing 0%); (d) V:0.1% following (not containing 0%); (e) select among the group who constitutes by Mg, Sr, Ba more than a kind: add up to and (do not contain 0%) below 0.01%; (f) rare earth element: (do not contain 0%) below 0.01%; (g) select among the group who constitutes by Zr, Ta and Hf more than a kind: add up to and (do not contain 0%) below 0.05%; (h) Co:2.5% following (not containing 0%) and/or W:2.5% following (not containing 0%), according to the composition that is contained, the characteristic of steel plate is further improved.
According to the present invention, be accommodated in the suitable scope by amount and tissue each composition, and satisfy above-mentioned (1) formula and (2) formula, so adjusting chemical ingredients forms, and the dislocation desity of control bainite, even can realize thus under high heat energy input welding, still can demonstrating excellent HAZ toughness, and the also excellent Plate Steel of brittlement crevasse crack propagation halt characteristic.
Description of drawings
Fig. 1 is that HAZ toughness (vE is extracted in expression
-40) the mensuration sketch chart of the position of test film.
Embodiment
Present inventors are the carbonitride miniaturization by making Ti, attempt still reaching good HAZ toughness under high heat energy input welding.If the speed of cooling during molten steel solidification is certain, the dispersion state that then existing Ti is a carbonitride only is considered to the interpolation balance decision by Ti, N.What but present inventors studied with keen determination found that, by dwindling the temperature range in the δ territory of representing in the state graph of steel, even identical Ti, N addition, also can make Ti is the fine dispersion of carbonitride.
The X value of stipulating the relation of above-mentioned (2) formula is the function about the temperature range in δ territory.Present inventors attempt improving HAZ toughness and the relation of having found above-mentioned (2) formula, at first its fact are described.Last meaning described " δ territory ", the meaning is the zone of containing δ iron in the state graph of steel.Should " zone of containing δ iron ", except the zone of only containing δ iron, comprise that also 2 regions etc. of δ+γ contain the zone of δ iron and other states.And so-called " temperature range in δ territory " is meant the temperature range that contains δ iron (ceiling temperature in δ territory and lower limit temperature poor).Here in the steel of specific composition, for example under the situation of the temperature range of the temperature range of having only δ iron and δ+γ iron, the temperature range that adds up to the δ territory of their temperature ranges.The temperature range in this δ territory can be by forming to the chemical ingredients of comprehensive calculation of thermodynamics software (Thermo-calc can be bought by the CRC synthetic study) input steel plate and calculating.
In this δ iron because the velocity of diffusion of Ti is fast, so if the temperature range in δ territory is wide, then time of existing of δ iron long, think that thick Ti is that carbonitride is formed easily.Therefore to study by adjusting chemical ingredients and form to dwindle the temperature range in δ territory, so that Ti is the carbonitride miniaturization.For this reason, by the calculating of Thermo-calc, be that benchmark only changes a kind of chemical ingredients amount with the special component, investigate of the influence of each chemical ingredients thus to the temperature range in δ territory.According to this research, having determined has correlationship with the temperature range in δ territory, the X value of the function representative of being made up of chemical ingredients.
X value=500[C]+32[Si]+8[Mn]-9[Nb]+14[Cu]+17[Ni]-5[Cr]-25[Mo]-34[V]
(in the formula, [] represents the content (quality %) of each element.)
Coefficient in the above-mentioned formula of X value is corresponding to be, the variable quantity of the temperature range in the δ territory when making each chemical composition change by the steel of special component.Specifically, " 500 " of the coefficient of [C] for example, the meaning is that the C amount was increased 0.01% o'clock, reduces 5 ℃ approximately according to the temperature range in the calculating δ territory of Thermo-calc.And the temperature range in X value and δ territory is in the relation of inverse ratio (if the X value increases, then the temperature range in δ territory reduces) substantially.
Also have, among the element of the above-mentioned X value of regulation, except that the basal component (C, Si, Mn) of Plate Steel of the present invention, also comprise the element (Nb, Cu, Ni, Cr, Mo, V etc.) that contains as required, when not containing these elements, calculating X value does not just have these projects, and when containing these elements, is got final product by following formula calculating X value.
Based on such consideration, make and to have the steel plate of various X values and find that by making the increase of X value, can make Ti is the median size miniaturization of carbonitride, can improve HAZ toughness when investigating.
And by the X value is increased, low-temperature flexibility that can also steel plate also improves.It is that causing Ti is the median size minimizing of carbonitride because the X value is increased that this phenomenon is estimated to be.
As great being characterised in that of above-mentioned Plate Steel of the present invention, its chemical ingredients is formed the point that satisfies following formula (2).
40≤X value≤160 ... (2)
X value=500[C]+32[Si]+8[Mn]-9[Nb]+14[Cu]+17[Ni]-5[Cr]-25[Mo]-34[V]
(in the formula, [] represents the content (quality %) of each element.)
But, if the present invention does not infer the reason (minimizing of the median size of the carbonitride that the minimizing of the temperature range in δ territory brings to above-mentioned this, the HAZ toughness that the minimizing of median size brings and the raising of low-temperature flexibility etc.) limited, scope then of the present invention is limited by the scope that requires.Promptly satisfy Zhuan Li Yao the constitutive requirements stipulated in the scope of Ao Plate Steel within the scope of the present invention.
If each chemical ingredients amount is in proper range, then the X value is big more, and Ti is median size and the HAZ toughness and the base metal tenacity raising more of carbonitride.This X value following is limited to 40 (be preferably 45, more preferably 50).The upper limit of X value is determined by the appropriate amount of each chemical ingredients, is 160 (being preferably below 100, more preferably below 75).From the viewpoint that hard phase MA organizes the generation of (martensite-austenitic mixed structure) to suppress, the preferred upper limit of X value is below 75.
In Plate Steel of the present invention, be to adjust chemical ingredients more than 40 like this to form by making the X value, be that carbonitride is fine thereby make Ti.But the balance as if Ti content and N content is upset, then the toughness of steel plate, particularly HAZ toughness deterioration.The ratio of Ti content [Ti] and N content [N] ([Ti]/[N]) surpasses at 4.0 o'clock specifically, and it is thick that Ti is that carbonitride becomes, and HAZ toughness reduces.Otherwise, if be lower than 1.5, then because the influence of superfluous N, low-temperature flexibility and the reduction of HAZ toughness.Thereby in Plate Steel of the present invention, its another feature is except that above-mentioned (2) formula of regulation X value, also will satisfy following (1) formula, to realize the balance of Ti content [Ti] and N content [N].The preferred lower limit of being somebody's turn to do [Ti]/[N] is 2.0, and preferred upper limit is 3.5.
From the flexible viewpoint, the Ti in the preferred Plate Steel of the present invention is that carbonitride is fine.Thereby the Ti in the Plate Steel of the present invention is that carbonitride is preferably below the 43nm, more preferably below the 40nm, more preferably below the 35nm.
Ti among the present invention is that the value of the median size of carbonitride is the value of being measured by following mode.At first, with transmission electron microscope (TEM), observing multiplying power more than 60,000 times, field of view 2.0 μ m * 2.0 μ m more than, observing under the above condition in 5 places, place, the position (t=thickness of slab) of the dark t/4 of part of the thermal process of steel plate is represented in the observation conduct.Measure the area of each carbonitride in this visual field then, calculate the diameter of equivalent circle of each carbonitride by this area.The value of the diameter of equivalent circle of this each carbonitride being carried out arithmetical mean (addition is average) and obtaining is the median size of carbonitride for the Ti among the present invention.
Whether also have, differentiating is that Ti is a carbonitride, assigns to really according to the one-tenth of the main body that constitutes each carbonitride particle.That is, so-called " Ti is a carbonitride ", refer to will remove carbon elimination and nitrogen the total quality of remaining element as 100% o'clock, the ratio of Ti is more than the 50 quality %.The amount of element can be utilized energy dispersion type X ray detector (EDX) decision.But, because too fine carbonitride can not measure, so " Ti is a carbonitride " in this is limited to more than 5.
In Plate Steel, as above-mentioned except toughness is good, in the large structure of boats and ships, marine structure, low temperature storage container, pipeline steel pipe, building, bridge etc., follow the accident of brittle rupture to make a big impact for economy and environment, this just requires the security of height to it.Present inventors have also carried out research repeatedly from this viewpoint of raising that becomes this brittlement crevasse crack propagation halt characteristic in the lump.It found that, for brittlement crevasse crack propagation halt characteristic is improved, if be controlled to be tissue, and make the scope of the dislocation desity of bainite, then can improve brittlement crevasse crack propagation halt characteristic in regulation based on bainite (bainite branch rate is more than the 95 area %).
In Plate Steel of the present invention, by dislocation desity (ρ with bainite
1/2) be controlled at 1.0 * 10
6～5.0 * 10
7(m
-1) scope in, can realize excellent brittlement crevasse crack propagation halt characteristic.Metallic substance has been notified under the stress of desirable strength at break than anticipation and has been destroyed.This phenomenon is also known to be caused owing to having various defectives in metallic substance inside.As the kind of such defective, inclusion, precipitate, heterogeneous particles, dislocation etc. are arranged, by the control of these organizational factors, the improvement of base metal tenacity is carried out.
Present inventors think that these defect factors also can be exerted one's influence to brittlement crevasse crack propagation halt characteristic, thereby distinguish, and are special in being conceived to the organizational controls of dislocation desity, and brittlement crevasse crack propagation halt characteristic is enhanced.Cause brittlement crevasse crack propagation halt characteristic good by dislocation desity being controlled at suitable scope, can't brightly fully release about this mechanism, but can be estimated as, probably if dislocation desity uprises, then because the stress concentration of the be full of cracks leading section that the merging of dislocation etc. cause, can cause parent's surface of fracture to be formed easily, so the propagation of brittlement crevasse crack is difficult to stop.
In order to bring into play above-mentioned effect, need be with the dislocation desity (ρ of bainite
1/2) be controlled at 1.0 * 10
6～5.0 * 10
7(m
-1) scope.Dislocation desity (the ρ of bainite
1/2) be lower than 1.0 * 10
6(m
-1) time, can not guarantee strength of parent, opposite if dislocation desity (ρ
1/2) surpass 5.0 * 10
7(m
-1), brittlement crevasse crack propagation halt characteristic deterioration on the contrary then.The preferred lower limit of this dislocation desity is 5.0 * 10
6(m
-1), more preferably 1.0 * 10
7(m
-1), more preferably 1.5 * 10
7(m
-1) [or 2.0 * 10
7(m
-1) more than], be limited to 4.0 * 10 on preferred
7(m
-1) [more preferably 3.0 * 10
7(m
-1)].
The mensuration of above-mentioned dislocation desity adopts the X-ray diffraction method as general method to get final product.For example, just can try to achieve dislocation desity by the half price width of cloth of (200) face based on " CAMP-ISIJ VoL.17 (2004) P396～399 " described method.In the present invention, extract the test film on 25mm limit, at the face of the rolling surface level at thickness of slab direction electrolytic polishing and 1/4 position and as the mensuration face.
In the present invention, need become tissue based on bainite.Pass through predetermined bits dislocation density in the above described manner in addition, good brittlement crevasse crack propagation halt characteristic will obtain performance.But in order to bring into play such effect, not necessarily leaveing no choice but 100 area % all is bainite structure, gets final product more than counting 95 area % with bainite branch rate.As the tissue beyond the bainite, can enumerate Ma Shi basis, ferrite or perlite etc.Also have, in the present invention, bainite branch rate is followed following method and is measured.
(bainite divides the measuring method of rate)
Will be from the t/4 (t: after thickness of slab) test film on the 2cm limit of position extraction carries out mirror ultrafinish of each steel plate, carry out etching with nital (2% nitric acid-ethanolic soln), utilize observation by light microscope tissue (multiplying power: 100 times), n=10 (inferior) also takes pictures, by image analysis apparatus (MediaCybernetics system: imega-Pro Plus) calculate bainite and divide rate.At this moment, the lath-shaped beyond the ferrite is organized and all is considered as bainite.
Plate Steel of the present invention, because its chemical ingredients is formed the relation that satisfies above-mentioned (1) formula and (2) formula, and the dislocation desity of control bainite, HAZ toughness and brittlement crevasse crack propagation halt characteristic are all excellent.But, even satisfy these important documents, if the content of each chemical ingredients (each element) then still can not be reached above-mentioned effect not in suitable scope.Therefore Plate Steel of the present invention, above-mentioned except satisfying (1) formula and (2) formula, and the dislocation of regulation bainite satisfies beyond the density, its feature is that also the amount of each chemical ingredients is in the proper range as described below.Below, describe respectively for chemical ingredients.
[C：0.030～0.15％]
C is the needed element of intensity that is used to guarantee steel plate, the effective element that still is used for making the temperature range in δ territory of the state graph of steel to dwindle in addition.C content is lower than at 0.030% o'clock, and these effects can't be brought into play.On the other hand, if C content surpasses 0.15%, then the 2nd phase MA of hard tissue becomes too much, and base metal tenacity and HAZ toughness reduce.Therefore C content is decided to be 0.030～0.15%.The preferred lower limit of C content is 0.040% (more preferably more than 0.050%), and preferred upper limit is 0.10% (more preferably below 0.070%).
[Si:1.0% following (not containing 0%)]
Si is the intensity effective elements that is used to guarantee steel plate, therefore preferably makes it to contain (more preferably more than 0.20%) more than 0.10%.But if contain Si superfluously, then the MA tissue is a large amount of generates, and base metal tenacity and HAZ toughness reduce, so its upper limit need be 1.0%.The preferred upper limit of Si amount is 0.8%, more preferably 0.50%, more preferably 0.40%.
[Mn：0.8～2.0％]
Mn improves hardenability, to guaranteeing the intensity effective elements of steel plate.Mn content is lower than at 0.8% o'clock, and the effect that intensity is guaranteed can't be given full play to.On the other hand, if Mn content surpasses 2.0%, then base metal tenacity and HAZ toughness reduce.Therefore Mn content is decided to be 0.8～2.0%.The preferred lower limit of Mn is 1.00%, more preferably 1.20%, more preferably 1.50%.On the other hand, preferably having gone up of Mn amount is 1.80%, more preferably 1.60%.
[following (the not containing 0%) % of P:0.03%]
As the P of impurity element because can cause detrimentally affect, so its amount is preferably few as much as possible to base metal tenacity and HAZ toughness.Therefore the P amount is below 0.03%, to be preferably below 0.01%.But industrial that P amount in the steel is in is 0% very difficult.
[S:0.01% following (not containing 0%)]
S forms MnS and element that ductility is reduced, and particularly detrimentally affect is huge in high-tensile steel, so its amount is preferably few as much as possible.Therefore the S amount is below 0.01%, to be preferably below 0.005%.But industrial that S amount in the steel is in is 0% very difficult.
[Al：0.01～0.10％]
Al has deoxidation and by making the microstructure miniaturization make the element of the effect that base metal tenacity improves.In order to bring into play such effect fully Al is contained more than 0.01%.But, if contain Al superfluously, then base metal tenacity and HAZ toughness reduce on the contrary, so are limited to 0.10% on it.The preferred lower limit of Al content is 0.020%.On the other hand, its preferred upper limit is 0.060%, more preferably below 0.040%.
[Ti：0.015～0.03％]
Ti and N form fine nitride, and thickization (so-called anchoring effect) of the austenite crystal of the HAZ when suppressing welding is the effective elements that is used to make the raising of HAZ toughness.In order to bring into play such effect fully, containing Ti is more than 0.015%.But, if Ti content surplus, be defined as 0.03% on the then HAZ toughness deterioration on the contrary, so Ti content.Ti content is preferably more than 0.017%, below 0.020%.
[B：0.0010～0.0035％]
When B welded in high heat energy input, near HAZ, particularly fusion portion, making with BN was the intracrystalline ferrite generation of nuclear, and has the fixed action of solid solution N, is to the important element of the tough property improvement of HAZ.In the present invention,, B is contained more than 0.0010% in order to bring into play this effect fully, more than the content in the common Plate Steel.But if B content surplus, then thick bainite structure forms when high heat energy input welding, so HAZ toughness deterioration on the contrary.Therefore B content on be defined as 0.0035%.The preferred lower limit of B content is 0.0015% (more preferably more than 0.0020%), on be limited to 0.0030% (more preferably below 0.0025%).
[N：0.0050～0.01％]
N combines with Ti and forms fine carbonitride, suppresses thickization of austenite crystal when high heat energy input is welded, and is the element with the effect that makes the raising of HAZ toughness.If N content is very few, then above-mentioned effect can't be given full play to, so is defined as 0.0050% under it.On the other hand, if N content surplus then causes detrimentally affect to base metal tenacity and HAZ toughness, so is defined as 0.01% on it.The preferred lower limit of N content is 0.0055%, more preferably more than 0.0060%.In addition, the preferred upper limit of N content is 0.0090%, more preferably below 0.0080%.
[Ca:0.005% following (not containing 0%)]
Ca is the element with the effect that makes the raising of HAZ toughness, and in detail, Ca makes the MnS balling, by such inclusion being carried out morphology Control anisotropy is reduced, and improves HAZ toughness thus.On the other hand, form CaS, CaO, suppress thickization of the austenite crystal of HAZ, HAZ toughness is improved.Contain Ca in the steel plate and be preferably more than 0.0005% in order to bring into play such effect fully, preferably to make.Yet,, therefore will be defined as 0.005% on it if the content surplus of Ca makes base metal tenacity and HAZ toughness deterioration on the contrary.The preferred upper limit of Ca amount is 0.0030%, more preferably 0.0025%.
[O:0.01% following (not containing 0%)]
Reactions such as O and Al, Ca, Mg and at high temperature form stable oxide are the elements that effectively plays a role on thickization of the old austenite crystal that prevents HAZ.This effect increases along with increasing of its content, but if become superfluous, then purity reduces, and HAZ toughness reduces on the contrary, therefore will be defined as 0.01% on it.
Plate Steel of the present invention except that mentioned component, is made of Fe and unavoidable impurities basically.But the Plate Steel that contains other elements is not got rid of in invention, in scope of the present invention, in the scope of not damaging effect of the present invention, comprises the Plate Steel that contains other composition elements yet.
For example in Plate Steel of the present invention, except that mentioned component, also contain as inferior element also effective as required: (a) Nb:0.035% following (not containing 0%); (b) Cu:2.0% following (not containing 0%), Ni:2.0% following (not containing 0%) and below the Cr:2.0% among (not containing 0%) more than a kind; (c) Mo:1.0% following (not containing 0%); (d) V:0.1% following (not containing 0%); (e) select among the group who constitutes by Mg, Sr, Ba more than a kind: add up to and (do not contain 0%) below 0.01%; (f) rare earth element: (do not contain 0%) below 0.01%; (g) select among the group who constitutes by Zr, Ta and Hf more than a kind: add up to and (do not contain 0%) below 0.05%; (h) Co:2.5% following (not containing 0%) and/or W:2.5% following (not containing 0%), according to the kind of the composition that is contained, the characteristic of steel plate is further improved.
[Nb:0.035% following (not containing 0%)]
Nb improves the hardenability of blank, is the intensity effective elements that is used to improve steel plate, contains as required.Yet if Nb content surplus, base metal tenacity and HAZ toughness reduce, and therefore will be defined as 0.035% on it.In order to bring into play this effect, preferred Nb contains more than 0.005%, more preferably contains more than 0.010%.In addition, be limited to 0.025% on Nb content is preferred, more preferably below 0.020%.
[Cu:2.0% following (not containing 0%), Ni:2.0% following (not containing 0%) and below the Cr:2.0% among (not containing 0%) more than a kind]
Cu, Ni and Cr improve hardenability and the element that helps intensity to improve, can add as required.Wherein, Cu is considered to the temperature range in the territory of the same δ made from C and dwindles, and has that to make Ti be the effect of carbonitride miniaturization.Ni is used to make the temperature range in δ territory to dwindle effective elements in addition.In order to give full play to such effect, recommend it to contain and all be preferably more than 0.20%, more preferably more than 0.40%.If their amount surplus, then base metal tenacity and HAZ toughness have the tendency of reduction, so its upper limit all is decided to be 2.0%.Be preferably below 1.0%.
[Mo:1.0% following (not containing 0%)]
The intensity that Mo makes except improving hardenability still is used to prevent the temper brittleness effective elements improving, and can add as required.In order to bring into play such effect fully, recommend Mo content to be preferably more than 0.05%, more preferably more than 0.10%.If but Mo content surplus, then therefore base metal tenacity and HAZ toughness deterioration will be defined as 1.0% on it.Mo content is more preferably below 0.50%.
[V:0.1% following (not containing 0%)]
V is by a spot of interpolation, has the element of the effect that improves hardenability and temper softening impedance, can add as required.In order to bring into play such effect fully, recommend the V amount to be preferably more than 0.01%, more preferably more than 0.02%.But if the V amount is superfluous, then therefore base metal tenacity and HAZ toughness deterioration, will be defined as 0.1% on it.The V amount is preferably below 0.05%.
[select among the group who constitutes by Mg, Sr, Ba more than a kind: add up to and (do not contain 0%) below 0.01%]
Mg, Sr and Ba generate fine oxide compound in Plate Steel, suppress austenitic thickization of HAZ, thereby are effective elements on raising HAZ toughness.In order to give full play to such effect, preferably contain they more than a kind (total) more than 0.0003%.Yet, if their content surplus makes base metal tenacity and HAZ toughness deterioration on the contrary, so is limited to 0.01% on it.Be limited to 0.0040% on preferred, more preferably 0.0020%.
[rare earth element: (do not contain 0%) below 0.01%]
Rare earth element (REM) exists as oxide compound or sulfide, has under the promoter action of the austenite crystal miniaturization of HAZ and ferrite transformation, improves the effect of HAZ flexible, can apply flexibly effectively as required.Yet,, make HAZ toughness deterioration on the contrary, so its upper limit is preferably 0.01% if contain REM superfluously.REM more preferably on be limited to 0.003%.Also have, the REM that uses among the present invention comprises any of lanthanide rare dvielement, contains getting final product more than a kind of they.
[select among the group who constitutes by Zr, Ta and Hf more than a kind: add up to and (do not contain 0%) below 0.05%]
The same with the Ti carbonitride that forms with Hf of Zr, Ta, therefore thickization of the austenite crystal of the HAZ when suppressing welding be that the HAZ flexible is improved effective elements.This bring into play such effect fully, preferably contain adding up to more than a kind more than 0.001% of above-mentioned element, but if their content surplus, then base metal tenacity and HAZ toughness reduce on the contrary, when therefore containing these elements, its total is preferably below 0.05%, more preferably below 0.03%.
[Co:2.5% following (not containing 0%) and/or W:2.5% following (not containing 0%)]
Co and W improve hardenability, are the elements with effect of the intensity that improves steel plate.In order to give full play to this effect, preferably contain wherein a kind or both sides, be respectively more than 0.2%.But if their amount surplus, base metal tenacity and HAZ toughness deterioration, therefore the upper limit of amount with them all is decided to be 2.5%.
When making Plate Steel of the present invention, will be as the above-mentioned steel that satisfies the important document of chemical ingredients composition, [Ti]/[N] and X value, carry out melting with common smelting process, after cooling off this molten steel and becoming slab, the scope that for example is heated to 950～1300 ℃ is carried out hot rolling afterwards, making by the accumulation draft in the temperature range of T value ± 50 of following formula (3) regulation ℃ is more than 40%, and making accumulation draft under 750～800 ℃ then is 10～30% to finish rollingly, and its postcooling gets final product.
T value=750+4000[Nb]+326000[B]+250[Mo]+400[V] ... (3)
Also having the T value by following formula (3) regulation is the index that the bainite dislocation desity is adjusted.In addition among the element of the above-mentioned T value of regulation, in Plate Steel of the present invention, comprise the composition (B, Mo, V) that is contained as required, but when not containing these elements, then calculating the T value there are not these projects yet, and when containing these elements, calculate the T value by following formula (3) and get final product.
Why making the accumulation draft in the temperature range of T value ± 50 ℃ of following formula (3) defined is more than 40%, is from guaranteeing this viewpoint of dislocation desity, if draft at this moment is lower than 40%, then becoming low-dislocation-density.Making accumulation draft under 750～800 ℃ in addition is 10～30% also to be from guaranteeing close this viewpoint of dislocation, if draft at this moment is lower than 10%, then become low-dislocation-density, if surpass 30%, then becoming high dislocation density.
Plate Steel of the present invention is controlled the X value and is made the temperature range in δ territory narrow and small, therefore forms slab by under common condition, cooling off molten steel (for example being cooled to 1100 ℃ from 1500 ℃), can form the median size of abundant little Ti carbonitride thus with 0.1～2.0 ℃/second speed of cooling.But, in order to form finer carbonitride, preferably change the cooling water inflow and the method for cooling of casting machine, so that the speed of cooling when solidifying improves.
The present invention relates to Plate Steel, so-called Plate Steel is defined as JIS in this field, generally refers to more than the thickness of slab 3.0mm.But the thickness of slab of Plate Steel of the present invention is preferably more than the 20mm, more preferably more than the 40mm, more preferably more than the 60mm.Mention reason and be because, even so high heat energy input welding or superelevation heat energy input welding still demonstrates good HAZ toughness because the input heat is 40kJ/mm, therefore, even thickness of slab is very thick, by increasing the input heat, still can weld expeditiously.
[embodiment]
Below, enumerate embodiment and be described more specifically the present invention, but the present invention is not limited by the examples below certainly, before can meeting, can certainly be changed enforcement in the scope of aim described later, these all are included in the technical scope of the present invention.
Steel with the composition shown in following table 1～4, carry out melting with common smelting process, be cooled to 1100 ℃ and after becoming slab from 1500 ℃, be heated to 1100 ℃ and carry out hot rolling with 0.1～0.2 ℃/second speed of cooling, and according to circumstances carry out tempering, make the high-tensile steel of thickness of slab 60mm.At this moment, control is by the accumulation draft in the temperature range of T value ± 50 of aforementioned (3) formula regulation ℃, and the accumulation draft under 750～800 ℃.In following table 1～4, record and narrate [Ti]/[N], X value that the chemical ingredients of with good grounds steel plate form to be calculated in the lump, the value (record and narrate in the table is " δ territory ") and the T value of the temperature range in the δ territory of calculating by Thermo-calc.
Steel plate for manufacturing as above-mentioned, by following main points, with following method mensuration Ti is the median size of carbonitride, tensile strength, base metal tenacity, HAZ toughness and the brittlement crevasse crack propagation halt characteristic of steel plate, and measures area occupation ratio, the dislocation desity of bainite according to aforesaid method.These results and manufacture method (the accumulation draft in the temperature range of T value ± 50 ℃, the accumulation draft under 750～800 ℃) are presented in following table 5～8 together.
(Ti is the median size of carbonitride)
With transmission electron microscope (TEM),, observe the position (t=thickness of slab) of dark t/4 observing 60,000 times of multiplying powers, field of view 2.0 μ m * 2.0 μ m, observing under the condition more than 5 places, place.Measure the area of each carbonitride in this visual field then, calculate the diameter of equivalent circle of each carbonitride by this area.The diameter of equivalent circle of this each carbonitride is carried out arithmetical mean (addition is average), and to calculate the Ti of each steel plate be the median size of carbonitride.
(tensile strength of steel plate)
In the position (t=thickness of slab) of dark t/4, make the length direction of test film become the plate width direction (C direction) of steel plate, so extract the JIS4 test film, carry out tension test, measure tensile strength thus.
(base metal tenacity)
Position (t=thickness of slab) at dark t/4, make the length direction of test film become the rolling direction (L direction) of steel plate, so extract the V otch standard test sheet of JIS Z 2242 defineds, carry out at each temperature pendulum impact test (impact the sword radius: 2mm), the absorption energy (vE under measuring-40 ℃
-40).
(HAZ toughness)
40kJ/mm welds (electro-gas welding electrogas arc welding) with input heat energy, extract JIS4 test film (incision site is apart from the 0.5mmHAZ of fusion portion side) from position shown in Figure 1, carry out pendulum impact test under-40 ℃, measuring absorption can (vE
-40).What in the present invention, tensile strength 200J was above is qualified.
(evaluation of brittlement crevasse crack propagation halt characteristic)
Brittlement crevasse crack propagation halt characteristic is tested according to the method for the steel grade identification test direction defined of Japanese welding association.That is, it is by carrying out the test (ESSO test) of the otch processing of the 29mm degree of depth on the square test film of 50mm, trying to achieve brittlement crevasse crack propagation performance (Kca value) thus and show 600N/mm
1.5Temperature T K (℃).In the present invention, TK≤-40 ℃ are qualified.
[table 5]
[table 6]
[table 7]
[table 8]
Can carry out following investigation by these results.At first, the important document of the present invention's regulation is satisfied in test No.1～46, and any as can be known characteristic (tensile strength of steel plate, base metal tenacity, HAZ toughness and brittlement crevasse crack propagation halt characteristic) is all good.
With respect to this, a certain important document of test No.47～75 shortcoming the present invention regulations, certain deterioration in characteristics.
Claims (11)
1. the high heat energy input of an excellent brittlement crevasse crack propagation halt characteristic is welded and is used Plate Steel, it is characterized in that, contain C:0.030～0.15% in quality %, Si:1.0% is following but do not contain 0%, Mn:0.8～2.0%, P:0.03% is following but do not contain 0%, S:0.01% is following but do not contain 0%, Al:0.01～0.10%, Ti:0.015～0.03%, B:0.0010～0.0035%, N:0.0050～0.01%, Ca:0.005% is following but do not contain 0%, O:0.01% is following but do not contain 0%, and, satisfy following (1) formula and (2) formula, and, the tissue of this Plate Steel is that bainite branch rate is the above tissues of 95 area %, and, the dislocation desity ρ of bainite
1/2Be 1.0 * 10
6～5.0 * 10
7(m
- 1),
1.5≤[Ti]/[N]≤4.0…(1)
40≤X value≤160 ... (2)
X value=500[C]+32[Si]+8[Mn]-9[Nb]+14[Cu]+17[Ni]-5[Cr]
-25[Mo]-34[V]
In the formula, [] represents the mass percentage content of each element.
2. Plate Steel is used in high heat energy input welding according to claim 1, it is characterized in that the temperature range in δ territory is below 40 ℃.
3. Plate Steel is used in high heat energy input welding according to claim 1 and 2, it is characterized in that, and be in the position of t/4 in the degree of depth, Ti is that the median size of carbonitride is below the 43nm, wherein, the t=thickness of slab.
4. Plate Steel is used in high heat energy input welding according to claim 1 and 2, it is characterized in that, also contains below the Nb:0.035% in quality % but does not contain 0%.
5. high heat energy input welding Plate Steel according to claim 1 and 2, it is characterized in that, also contain below Cu:2.0% in quality % but do not contain 0%, below the Ni:2.0% but do not contain 0% and below the Cr:2.0% but do not contain select 0% more than a kind.
6. Plate Steel is used in high heat energy input welding according to claim 1 and 2, it is characterized in that, also contains below the Mo:1.0% in quality % but does not contain 0%.
7. Plate Steel is used in high heat energy input welding according to claim 1 and 2, it is characterized in that, also contains below the V:0.1% in quality % but does not contain 0%.
8. Plate Steel is used in high heat energy input welding according to claim 1 and 2, it is characterized in that, in quality % also contain add up to below 0.01% but do not contain 0% from Mg, Sr, Ba, select more than a kind.
9. Plate Steel is used in high heat energy input welding according to claim 1 and 2, it is characterized in that, also contains rare earth element in quality %: below 0.01% but do not contain 0%.
10. Plate Steel is used in high heat energy input welding according to claim 1 and 2, it is characterized in that, in quality % also contain add up to below 0.05% but do not contain 0% from Zr, Ta and Hf, select more than a kind.
11. Plate Steel is used in high heat energy input welding according to claim 1 and 2, it is characterized in that, also contain below Co:2.5% in quality % but do not contain 0%, below the W:2.5% but do not contain select 0% more than a kind.
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| JP2007183291A JP5110989B2 (en) | 2007-07-12 | 2007-07-12 | Large steel plate for high heat input welding with excellent brittle crack propagation stopping characteristics |
| JP2007-183291 | 2007-07-12 |
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| JP (1) | JP5110989B2 (en) |
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Also Published As
| Publication number | Publication date |
|---|---|
| JP5110989B2 (en) | 2012-12-26 |
| CN101343712B (en) | 2011-10-12 |
| KR100967498B1 (en) | 2010-07-07 |
| JP2009019244A (en) | 2009-01-29 |
| KR20090006728A (en) | 2009-01-15 |
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