CN100535165C - Large volume heat inputing in the welding tie-in tenacity excellent thick steel plate - Google Patents
Large volume heat inputing in the welding tie-in tenacity excellent thick steel plate Download PDFInfo
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- CN100535165C CN100535165C CNB200510114178XA CN200510114178A CN100535165C CN 100535165 C CN100535165 C CN 100535165C CN B200510114178X A CNB200510114178X A CN B200510114178XA CN 200510114178 A CN200510114178 A CN 200510114178A CN 100535165 C CN100535165 C CN 100535165C
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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- 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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- C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
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- C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
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Abstract
To provide a high strength thick steel plate in a class of 590 to 780 MPa which has excellent welded joint toughness (HAZ toughness) even when subjected to high heat input welding. Specified components of a thick steel plate, in particular, the total content of C, Mn, Cu and Ni are controlled by a specified parameter, the average number of fine Ti-containing oxides with a mean particle diameter of 0.05 to 1 [mu]m is controlled to >=10,000 pieces/cm<SP>2</SP>, and also the average number of coarse Ti-containing oxides with a mean particle diameter of >=2 [mu]m is controlled to <=2,000 pieces/cm<SP>2</SP>. Thus, even in a high strength thick steel plate in a class of 590 to 780 MPa, the toughness of the whole region of the HAZ in high heat input welding including, in particular, the weld heat affected zone in the vicinity of 3 to 5 mm from a melting line whose toughness is apt to decrease is remarkably improved.
Description
Technical field
The present invention relates to a kind of Plate Steel of big heat input welding joint tenacity excellent, relate to a kind of carry out also can bringing into play when big heat input is welded excellent welding joint flexible, the high-strength steel plate of 590～780MPa level.
Background technology
Always,, made following trial, in mother metal, disperseed, from intracrystalline ferrite has been generated during the cooling of HAZ portion tissue is carried out refinement, thereby guarantee HAZ toughness by making the oxide compound that contains Ti in order to ensure the HAZ toughness of Plate Steel.
For example in patent documentation 1, put down in writing; by making the Ti oxide compound of 0.1～3.0 μ m; or any one or two kinds of of complex body of Ti oxide compound and Ti nitride separate out; thereby the γ → α phase transformation during to the cooling in the coarse zone of HAZ portion is controlled; the intracrystalline ferrite is generated, thereby improve HAZ toughness.
In patent documentation 2 and patent documentation 3, showed, suppress by generation 1 time thick deoxidation resultant of generating in the molten steel (the deoxidation resultant of strong deoxidant element such as Al, Ca, REM), and 2 deoxidation resultants that the deoxidation owing to weak deoxidant element (Ti, Si, Nb, V, Ta) is generated carry out the dispersion of homogeneous, thereby guarantee the toughness of welding heat affected zone (HAZ portion).
In patent documentation 4, put down in writing, by make the Ti ratio of components more than 5%, the Al ratio of components is below 95%, particle dia is the Ti of 0.01～1.0 μ m and the composite oxides of Al, in steel, disperse equably, thereby the HAZ toughness of the steel when improving welding.
But, in these technology, in recent years, when becoming the welding of big heat input general, that the heat input constantly increases, be difficult to besides can guarantee the HAZ toughness that it is excellent.
To this, in patent documentation 5,6, put down in writing, in big heat input welding joint, in order to improve HAZ toughness, growth (thickization) to the austenite crystal under the high temperature that is heated to the HAZ field more than 1400 ℃ suppresses, in order to promote the refinement of reheat austenite crystal, utilized as the composition that generates oxide particle in the steel, contain Ca and be more than 3%, Al is the oxide compound more than 1%.
[patent documentation 1] special fair 7-824 communique (scope of claim)
[patent documentation 2] special fair 3-67467 communique (scope of claim)
[patent documentation 3] special fair 3-59134 communique (scope of claim)
[patent documentation 4] spy opens flat 9-3599 communique (scope of claim)
[patent documentation 5] spy opens 2003-313628 communique (scope of claim, 0031 section)
[patent documentation 6] spy opens 2003-313628 communique (scope of claim, 0030 section)
Summary of the invention
But above-mentioned patent documentation 5,6 is an object with the Plate Steel of 50～60 kg class (being lower than 590MPa).Therefore, the situation of the Plate Steel of the high-intensity 590～780MPa level more than this, in the oxide process of patent documentation 5,6, the flexible situation in the whole zone of HAZ when big heat input can take place to guarantee.According to present inventors' understanding, in above-mentioned patent documentation 5,6, particularly can not guarantee apart near the toughness of the welding heat affected zone solidus curve 3～5mm.
This is inferred to be is because following reason, in near distance solidus curve 3～5mm the welding heat affected zone, in the finer field of γ particle diameter ratio (about particle diameter 10 μ m), when big heat is imported, hardenability descends, easy thickization of bainite structure is because the karyogenesis frequency height of the bainite of crystal boundary generation type, so the intracrystalline bainite can not be shaped etc.
The present invention in light of this situation, its purpose is, a kind of high-strength steel plate of 590～780MPa level that welding joint toughness (HAZ toughness) is excellent when carrying out big heat input welding is provided.
In order to reach this purpose, the Plate Steel of big heat input welding joint tenacity excellent of the present invention is characterised in that, in quality %, each contains C:0.01～0.07%, Si:1.0% following (not comprising 0%), Mn:1.0～3.0%, Al: be lower than for 0.010% (not comprising 0%), Ti:0.005～0.050%, O:0.0010～0.0100%, contain Cu:0.1～1.5% in addition, more than in Ni:0.1～2.5% any, and, 20C (%)+1.5Mn (%)+Cu (%)+Ni (%) is 4.5～7.0%, remainder is essentially iron and unavoidable impurities, and median size is that the mean number of the oxide compound that contains Ti of 0.05～1 μ m is 10000/cm when observing with 1000 times of multiplying powers
2More than, and median size is that the mean number of the above oxide compound that contains Ti of 2 μ m is 2000/cm when observing with 200 times of multiplying powers
2Below.
Also have, in the present invention, the oxide compound of the above-mentioned Ti of containing is that as described later, the determinator of use EPMA device or FE-SEM/EDX device etc. when carrying out the compositional analysis of the inclusion in the steel, contains the oxide compound of Ti more than 10 quality %.Therefore, in the inclusion in steel, Ti content is lower than the oxide compound of 10 quality %, is not called the oxide compound of the Ti of containing of the present invention.Also have, above-mentioned " median size " is the equivalent round shaped grain footpath of containing the oxide compound of Ti.
As mentioned above, the situation of the Plate Steel of high-intensity 590～780MPa level, the oxide compound of the Ca of patent documentation 4,5 and Al system as mentioned above, can take place can not guarantee the whole regional flexible situation of HAZ when big heat is imported.
To this, among the present invention, in the oxide compound that in steel, exists, contain Ti,, fine oxide compound is generated in a large number except suppressing the quantity of thick oxide compound.It is many that the generation number of so fine oxide compound becomes, and generates the intracrystalline bainite easily in HAZ portion during cooling after the then big heat input welding.Its result, even the situation of the Plate Steel of high-intensity 590～780MPa level comprises that particularly toughness descends easily, apart near the welding heat affected zone above-mentioned solid phase line 3～5mm, the toughness in the whole zone of HAZ in the time of also can significantly improving big heat welding.
In addition, among the present invention, in order to ensure be not only solidus curve near, but the good toughness in the whole zone of HAZ is controlled the total of the content of C, the Mn of the element (improving the element of hardenability) that makes stabilization of austenite, Cu, Ni.
Therefore, Plate Steel of the present invention is suitable for the welded structure of boats and ships that intensity is 590～780MPa level, marine structure, bridge, building structure etc. etc. most, when using as this welded structure, even carry out the welding of big heat input, also can bring into play excellent welding joint toughness.
Embodiment
(oxide compound that contains Ti)
At first, the meaning of the oxide compound that contains Ti in the Plate Steel tissue of the present invention is carried out following explanation.Among the present invention, as mentioned above, in containing the oxide compound of Ti,, fine oxide compound is generated in a large number except suppressing the quantity of thick oxide compound.Specifically, median size is the mean number of the trickle oxide compound that contains Ti of 0.05～1 μ m, is 10000/cm when observing with 1000 times of multiplying powers
2More than, its on the other hand, median size is the mean number of the above oxide compound that contains Ti of 2 μ m, is 2000/cm when observing with 200 times of multiplying powers
2Below.
In the present invention, the above-mentioned oxide compound that contains Ti as mentioned above, is that to contain Ti be the above oxide compounds of 10 quality %.Be lower than 10 quality % at Ti content, in the poor oxide compound of Ti, the effect that does not have the HAZ formation intracrystalline bainite trickle oxide compound that contains Ti, when big heat input is welded, with thick contain the Ti oxide compound, become the ferrite product nucleus, suppress the effect of the generation of useful bainite.
As above-mentioned prior art, be not that the intracrystalline ferrite of the HAZ when big heat input is welded generates, in the present invention, the HAZ intracrystalline ferrite when big heat input is welded generates.Therefore, among the present invention, in steel, in advance, the above-mentioned fine oxide compound that contains Ti is existed in a large number.
As the present invention, HAZ intracrystalline ferrite when making big heat input welding generates, suppress the generation of the nuclear of near thickization of hardenability HAZ, during big heat input welding the finer solidus curve of the γ particle diameter ratio bainite structure due to low and crystal boundary generation type bainite.Therefore, even the situation of the Plate Steel of high-intensity 590～780MPa level, also can descend easily to particularly comprising toughness, apart near the welding heat affected zone above-mentioned solid phase line 3～5mm, the toughness in the whole zone of HAZ during big heat input welding is improved significantly.
Simultaneously, in order to ensure the quantity that exists of the oxide compound that contains Ti that this is fine, and do not hinder the formation of the bainite of intracrystalline, among the present invention, in advance, suppress the above-mentioned thick oxide compound that contains Ti.More particularly, the thick oxide compound that contains Ti that 2 μ m are above because ferritic generation can be stronger, thus as high temperature during big heat input welding under form the ferrite product nucleus easily, thereby suppress the generation of useful bainite.Also have, the thick like this oxide compound that contains Ti becomes the destructive starting point of fine bainite structure easily, also can hinder the thinning effect of bainite.
In order positively to bring into play above-mentioned action effect, obtain excellent welding joint toughness, among the present invention, median size is the trickle oxide compound that contains Ti of 0.05～1 μ m, with median size be more than the 2 μ m the oxide compound that contains Ti have quantity, be controlled in the mean number scope of above-mentioned the best.Therefore, the quantity of the oxide compound that contains Ti of any is outside the mean number scope of above-mentioned the best the time, under the situation of the Plate Steel of high-intensity 590～780MPa level, all can not improve particularly comprise toughness descend easily, apart near the welding heat affected zone above-mentioned solid phase line 3～5mm, the toughness in the whole zone of HAZ during big heat input welding.
The above-mentioned fine Ti oxide compound that contains, because the many more generations that promote the intracrystalline bainite more of number, so be preferably 20000/cm
2More than, 40000/cm more preferably
2More than exist for good.From the viewpoint of above-mentioned action effect, the fine number that contains the Ti oxide compound does not have the upper limit, but in common slab manufacturing process, think the fine number that contains the Ti oxide compound that can separate out on be limited to 1 * 10
8Individual/cm
2About.
In the above-mentioned fine oxide compound that contains Ti, can contain alloying element Si, Ca beyond the Ti, Mg etc.Wherein, particularly Mn is suitable for as the element that contains jointly with Ti.Ti+Mn is preferably and accounts for more than 60% of full alloying element (more preferably more than 70%) that constitutes oxide compound is good.
In addition, the above-mentioned thick oxide compound that contains Ti suppresses ferritic generation etc., above-mentioned inhibition effect in order to reach, and number is few more good more, preferably at 1000/cm
2Below, further preferably at 500/cm
2Below.
So, except suppressing the thick number that contains the Ti oxide compound, fine Ti inclusion is generated in a large number, be easy to generate the intracrystalline bainite in HAZ portion during cooling after the welding, can significantly improve HAZ toughness.Also have, steel plate of the present invention, as mentioned above, in HAZ portion the intracrystalline bainite is preferentially generated during cooling after the welding, when this cools off, how much generate crystal boundary bainite and ferrite sometimes, in the scope of the tough property improvement of not overslaugh HAZ, allow these bainites and ferritic generation.
(mensuration that contains the Ti oxide compound)
In observation, can use electric field radiation type scanning electronic microscope (FE-SEM) or scanning electronic microscope (SEM) or EPMA (electron probe microanalyzer) device etc. to the oxide compound that contains Ti with the afore mentioned rules multiplying power.Also have, in FE-SEM, for clearer and more definite differentiation steel parent phase with respectively contain the oxide compound of Ti, also can carry out EDX (Kevex system, Sigma energy dispersion type X-ray detector: energy dispersive X-rayspect rometer) analyze (FE-SEM/EDX) in addition.
Wherein, in 200 times of observations of multiplying power, be suitable for observing by the EPMA device to the thick oxide compound that contains Ti more than the median size 2 μ m.Also have, in 1000 times of fine observations that contain the Ti oxide compound of multiplying power, be suitable for using electric field radiation type scanning electronic microscope (FE-SEM) median size 0.05～1 μ m.So, among the present invention, in order to improve the precision and the reproducibility of the number of measuring the oxide compound that contains Ti, can be according to the size conversion multiplying power of the oxide compound that contains Ti.
For example, in the observation of the fine oxide compound that contains Ti, when using FE-SEM/EDX, at first, composition to the inclusion of median size 0.05～1 μ m that exists in the steel is analyzed, and obtains the ratio for the inclusion that contains the oxide compound that contain Ti of Ti more than 10 quality %.Then, at 0.1mm
2The field in, use 1000 times reflection electronic picture, to 0.01mm arbitrarily
2For example 10 visuals field take, use the image analysis software of the Image-ProPlus etc. of MEDIACYBERNETICS system, by these image analysis apparatus, the number of the inclusion of median size 0.05～1 μ m is measured.Then, the ratio of the total number in these 10 visuals field and the oxide compound of the above-mentioned Ti of containing multiplies each other, and enlarges 1000 times in addition again, obtains every 1cm
2The number of the oxide compound that contains Ti of median size 0.05～1 μ m.
(composition of Plate Steel)
Composition (unit: quality %), comprise the qualification reason of each element, carry out following explanation to Plate Steel of the present invention.Above-mentioned tissue (fine Ti is the number of inclusion and thick inclusion) to Plate Steel of the present invention is controlled, HAZ toughness when importing welding to improve big heat, and obtaining high-intensity mother metal characteristic is prerequisite, the composition of Plate Steel of the present invention, as scope shown in following, method in accordance with regulations is fabricated to effectively.
Promptly, described steel plate, each contains C:0.01～0.07%, Si:1.0% following (not comprising 0%), Mn:1.0～3.0%, Al: be lower than 0.010% (not comprising 0%), Ti:0.005～0.050%, O:0.0010～0.0100%, contain in addition more than in Cu:0.1～1.5%, Ni:0.1～2.5% any, and, 20C (%)+1.5Mn (%)+Cu (%)+Ni (%) is 4.5～7.0%, and remainder is essentially iron and unavoidable impurities.
Such Plate Steel form be because, in HAZ portion the intracrystalline bainite is generated during particularly for the cooling after welding, the mother metal composition is adjusted very important.Specifically, in above-mentioned composition, the C amount is higher relatively, and the intracrystalline bainite generates easily.
In big heat input welding, so, also be easy to generate the crystal boundary bainite even suppress ferritic generation in addition because the speed of cooling of HAZ portion slowly generates ferrite easily.So, be inferred as the C amount of relative raising HAZ portion, can suppress ferritic generation and also suppress the generation of crystal boundary bainite, thereby promote the generation of intracrystalline bainite.
Also have, in order to suppress the generation of above-mentioned crystal boundary bainite, it is very effective selectively to contain the alloying element strong just like the carbide generation energy of Nb, V.Nb and V carry out segregation around the Ti oxide compound, thereby stop the generation of Ti oxide compound nucleation bainite.
In addition, among the present invention, be not limited in solidus curve that the intracrystalline bainite generates near, good toughness in order to ensure the whole zone of HAZ, as mentioned above, by following parameter, the total amount of the content of the element (improving the element of hardenability) C, the Mn that make stabilization of austenite, Cu, Ni is controlled.By control,, also can improve hardenability, the bainite that the refinement intracrystalline generates even the speed of cooling of the HAZ portion of big heat input welding is slack-off to the total content of these elements.
Below, the reason that each amount of element is stipulated describes.
C：0.01～0.07％
C (carbon) guarantees the necessary element of strength of parent, needs 0.01% at least.Also have, improve the C amount, promote the generation of intracrystalline bainite.These effects are preferably and can obtain performance more than 0.02% more than 0.01%.On the other hand, C amount is excessive, then can worsen anti-solder cracks and HAZ toughness on the contrary, so be suppressed at below 0.07%, be preferably and be lower than 0.05%.Therefore, C content is 0.01～0.07, is preferably 0.02～be lower than 0.05% scope.
Si:1.0% following (not comprising 0%)
Si, solution strengthening helps to guarantee the intensity of mother metal.Be as the useful element of preparation reductor in addition.These effects, preferably contain can obtain more than 0.05% the performance.On the other hand, surpass 1.0%, tighter various places say that excessive containing then can be reduced base metal tenacity and HAZ toughness above 0.5%, thus Si on be limited to 1.0%, be preferably 0.5%.Also have, the scope of Si content is preferably 0.05～1.0%, and more preferably 0.05～0.5%.
Mn：1.0～3.0％
Mn has the effect of the hardenability of improving steel, and has and promote the generation of intracrystalline bainite to improve HAZ flexible effect.In order to bring into play such effect effectively, contain more than 1.0%, be preferably more than 1.2% very necessary.On the other hand, make its excessive containing, then can worsen HAZ toughness, thus on be limited to 3.0%, be preferably below 2.5%.Therefore, the scope of Mn content is 1.0～3.0%, is preferably 1.2～2.5% scope.
Al: be lower than for 0.010% (not comprising 0%)
Al is very necessary as powerful deoxidant element, preferably contains more than 0.001%, more preferably more than 0.002%.On the other hand, Al surpassed for 0.005% excessive containing strictly speaking more than 0.010%, then can increase the ratio of the Al in the oxide compound that contains Ti, reduced the effect that promotes that the intracrystalline bainite generates.Therefore, Al content is being lower than 0.010%, is preferably 0.001～0.010%, more preferably 0.002～0.005% scope.
Ti (total amount): 0.005～0.050%
Ti as mentioned above, forms the fine oxide compound that contains Ti (part is a nitride), promotes the generation of intracrystalline bainite, is to have the important element that improves HAZ toughness effect.In order to bring into play such effect, it is contained more than 0.005%, be preferably more than 0.008% to good.On the other hand, the Ti amount is excessive, and the oxide compound that then contains Ti becomes thick, and the oxide compound that perhaps contains Ti is too much, can worsen HAZ toughness and base metal tenacity on the contrary, so be suppressed at below 0.05%, is preferably below 0.030%.Therefore, full Ti content is preferably 0.008～0.030% scope in 0.005～0.050% scope.
More than any of Cu:0.1～1.5%, Ni:0.1～2.5%
Cu and Ni all help to improve hardenability, and mother metal is carried out highly malleablized, and refinement HAZ tissue, thereby improve base metal tenacity and HAZ toughness.In order to bring into play such effect, making it contain more than any of Cu or Ni is more than 0.1%, to be preferably more than 0.2%.On the other hand, make its excessive Cu of containing and Ni, then the sclerosis of HAZ becomes significantly, can reduce HAZ toughness on the contrary.Therefore, be limited to 1.5% on the Cu, be preferably 1.2%, be limited to 2.5% on the Ni, be preferably 2.2%.
Also have, contain Cu and surpass at 0.5% o'clock,, recommend preferably to contain the Ni over half of Cu content (quality %), further contain the above Ni of chemical equivalent from preventing the viewpoint of the thermal rupture rolling.
O：0.0010～0.0100％
O (oxygen) forms the oxide compound that contains Ti, as mentioned above, is the generation effective elements to the intracrystalline bainite that promotes HAZ.In order to bring into play such effect, it is contained be good more than 0.0010%, be preferably more than 0.0015%, more preferably more than 0.0020%.On the other hand, oxygen level is excessive, then easily generates the thick oxide compound that contains Ti, can worsen HAZ toughness on the contrary.Therefore oxygen level is necessary to be suppressed at below 0.0100%, is preferably below 0.0030%.
20C(％)+1.5Mn(％)+Cu(％)+Ni(％)＝4.5～7.0％
In addition, among the present invention, be not limited in solidus curve near, in order to ensure the good toughness in the whole zone of HAZ,, control with the total amount by above-mentioned parameter to C discussed above, Mn, Cu, Ni.By content to the element that makes stabilization of austenite (improving the element of hardenability) C, Mn, Cu, Ni, control by above-mentioned parameter, even the speed of cooling of the HAZ portion of big heat input welding is slack-off, also can improve hardenability, the bainite that the refinement intracrystalline generates.
Above-mentioned parameter is more than 4.5%, and can bring into play increases the hardenability effect, and the bainite structure that can the refinement intracrystalline generates can improve the toughness in the whole zone of HAZ.This parameter is lower than 4.5%, even for example C, Mn, each content of Cu, Ni can not be brought into play the effect of above-mentioned increase hardenability in the scope of defined, the bainite structure that can not the refinement intracrystalline generates can not improve the toughness in the whole zone of HAZ.
In addition, this parameter surpasses 7.0%, even for example C, Mn, each content of Cu, Ni are in the scope of defined, because formed MA (martensite) amount increases in the MA bainite structure, it is higher to reduce the whole regional flexible possibility of HAZ on the contrary.
Below, the element that optionally contains is described.
More than any one or two kinds of among Cr:0.1～2.0%, Mo:0.1～1.0%, Nb:0.10% following (not comprising 0%), the V:0.10% following (not comprising 0%).
Cr, Mo, Nb, V all can improve hardenability, strengthen strength of parent.Also have, Cr has the hardenability of raising refinement HAZ tissue, helps to improve HAZ flexible effect.Nb, V have the raising anti-temper softening, strengthen the effect of strength of parent.In order to bring into play these effects, make selectively that it contains that Cr:0.1% is above, Mo:0.1% above, Nb is preferably more than 0.01%, more than V any one or two kinds of in being preferably more than 0.01%.
In addition, excessive these elements that contains can reduce HAZ toughness respectively on the contrary.Cr causes martensitic increase that HAZ toughness is descended.Mo becomes the sclerosis of HAZ and significantly makes the decline of HAZ toughness.Nb, V suppress the formation of intracrystalline bainite, worsen HAZ toughness.Therefore, each on be limited to Cr:2.0%, Mo:1.0%, Nb:0.10%, V:0.10%.
B：0.0005～0.0050％
B solid solution in steel has the effect that improves hardenability.Also have in HAZ portion, can also bring into play the effect that the ferrite that suppresses crystal boundary generates the generation of the bainite that promotes intracrystalline.In order to bring into play such effect, it is contained more than 0.0005%.On the other hand, B content is too much, can reduce hardenability on the contrary, and suppresses the formation of intracrystalline bainite, and HAZ toughness is worsened.Therefore B content is 0.0005～0.0050%, is preferably 0.0005～0.0030%.
More than any one or two kinds of among Zr:0.05% following (not comprising 0%), Mg:0.0050% following (not comprising 0%), Ca:0.0050% following (not comprising 0%), the REM:0.0050% following (not comprising 0%).
Zr, Mg, Ca, REM have the HAZ of improvement flexible effect, but each excessive containing then can be worsened HAZ toughness on the contrary.
For example, Zr improves HAZ toughness by fixed nitrogen.Ca carries out balling with the inclusion of MnS sulfides etc., reduces the anisotropy of inclusion shape, thereby improves HAZ toughness.The inclusion of Mg, REM refinement MnS sulfides etc., thus HAZ toughness improved.But these Ca, Mg, REM make its each excessive containing, and contain thickization of Ti oxide compound owing to make, so can worsen HAZ toughness on the contrary.
Therefore, it is any one or two kinds of when above that it is contained, each is below the Zr:0.05%, is preferably 0.005～0.03%, Mg:0.0050% is following, be preferably below 0.0040%, Ca:0.0050% is following, be preferably below 0.0040%, and REM:0.0050% is following, be preferably below 0.0040%.
Then, impurity is carried out the following description.
N (nitrogen) is owing to worsening base metal tenacity and HAZ toughness, so be impurity in the present invention.But N and Ti form nitride and promote intracrystalline bainite ground to generate, and have the HAZ of improvement flexible effect, so allow to contain N to 0.0090%.
P (phosphorus) and S (sulphur) also are the elements that exists as impurity, have the bad influence of degradation under weldability and the base metal tenacity.Therefore P is suppressed at below 0.020% and (is preferably below 0.010%), and S is suppressed at and (is preferably below 0.005%) below 0.010% to good.
(manufacture method)
Plate Steel of the present invention, operation self can be made by usual method.But, in order to control the number of above-mentioned fine oxide compound that contains Ti and the thick oxide compound that contains Ti, comprise preferably and creating conditions, carry out following explanation.
In above-mentioned patent documentation 2 and patent documentation 3,, disclosed and before casting, controlled dissolved oxygen content etc., the methods such as speed of cooling when control is solidified as the size of controlled oxidation thing and the method for number.But, can not reduce the above thick oxide compound that contains Ti of 2 μ m that the present invention gazes at.Also have, only reduce the oxygen amount in the molten steel, can not guarantee the number of the fine oxide compound that contains Ti given to this invention.
The present invention carries out melting by the common smelting process of converter etc. equally, then obtain the former material steel (slab) of institute's dimensioning by the common casting of Continuous casting process etc., but in order to increase the number of the fine oxide compound that contains Ti, reduce thick inclusion and contain the oxide compound of Ti, in this smelt stage, the dissolved oxygen content of the steel before Ti added and Ti add the hold-time of back till cast and carry out strictness and be controlled to be good.
Specifically, in smelt stage, when adding Ti, at first control dissolved oxygen content in the molten steel in the scope of 20～100ppm.By the control of such dissolved oxygen content, the above-mentioned fine oxide compound that contains Ti is generated, can guarantee the fine oxide compound that contains Ti of amount given to this invention.
For the fine oxide compound that contains Ti of more generation, the dissolved oxygen content in the molten steel is good more than 20ppm, is preferably more than the 25ppm.On the other hand, the dissolved oxygen content that adds in the preceding molten steel of Ti is too much, then generates thick oxide compound that contains Ti and other oxide compound easily, for not good.Therefore, the dissolved oxygen content in the molten steel is suppressed at the interpolation that 100ppm carries out Ti afterwards.Be preferably the dissolved oxygen content in the molten steel is suppressed at the interpolation that 70ppm carries out Ti afterwards.In order in smelt stage the dissolved oxygen content in the molten steel to be controlled as mentioned above, can add Mn deoxidation, vacuum C (carbon) deoxidation, add the Si deoxidation by carrying out separately or through the following method of suitable combination.
Also have, after Ti adds, kept 10～50 minutes with stationary state.By the maintenance behind such interpolation Ti, can guarantee the fine oxide compound that contains Ti as the appropriate size of the product nucleus useful effect of intracrystalline bainite, the Ti oxide compound is floating upward, separation can also to make above thick the containing of 2 μ m that easily becomes the ferritic product nucleus of intracrystalline, thereby removes.In order positively to remove the above-mentioned thick Ti oxide compound that contains, carry out remaining goodly more than 10 minutes, be preferably more than 15 minutes, more preferably more than 20 minutes.
Also have, above-mentioned maintenance, the mode as common melting is carried out keeps between about 1550～1650 ℃.
On the other hand, this hold-time is long, and then fine inclusion aggegation, thickization can not be guaranteed the fine oxide compound that contains Ti of defined amount of the present invention, for not good.Therefore, the hold-time is below 50 minutes, is preferably below 40 minutes.
In actually operating, after adding with ultimate constituent content, Ti, Si, Mn and C carry out above-mentioned maintenance, be cast into good thereafter.
Carry out melting by such method, can guarantee that the present invention decides an amount of fine oxide compound that contains Ti, and can reduce the thick oxide compound that contains Ti.
Former material steel (slab) according to the manufacture method of common Plate Steel, after the heating, carries out hot rolling, stops along the growth of the set tissue of rolling direction, obtains the tissue through recrystallize when hot rolling is finished.Steel plate carries out water quenching after hot rolling is finished., carry out the tempering of steel plate, form the product of Plate Steel thereafter.
Below, for embodiment the present invention is carried out more specific description,, be not subjected to the restriction of following embodiment from of the present invention basic, it also is possible carrying out suitable change and implement in above-mentioned, the following scope that is suitable for purport of the present invention, these any all be included in the technical scope of the present invention.
[embodiment]
The steel of chemical constitution shown in table 1 (example) and the table 2 (comparative example), shown in table 3 (example) and table 4 (comparative example), hold-time to the stationary state behind dissolved oxygen content before the interpolation Ti of smelt stage and the interpolation Ti is carried out various conversion, and melting, casting obtain slab.After resulting slab is heated to 1100 ℃, is rolled, cools off, obtain the steel plate of thickness of slab 50mm.Also have,, carried out 500～650 ℃ temper for intensity and the toughness of adjusting mother metal.
Take test portion from resulting like this steel plate, measured the size of the oxide compound that contains Ti that exists in mother metal characteristic, HAZ toughness, the mother metal.These results represent in table 3 and table 4.
(mother metal characteristic)
Take No. 4 test films of JIS from each steel plate of above-mentioned manufacturing, carry out tension test, measured the tensile strength of steel plate, and carried out pendulum impact test, measured the toughness (vE of steel plate according to JISZ2242 according to JISZ2241
-20).
Here, tensile strength is more than the 590MPa and the pendulum impact value is the above material of 150J, is evaluated as the mother metal characteristic of the excellence with high-intensity high tenacity, in the material of the mother metal characteristic of guaranteeing such excellence, as described below, HAZ toughness is estimated.
(welding joint toughness)
The test film that cuts out from each steel plate of above-mentioned manufacturing (size: 12.5mm * 32mm * 55mm), the near (thermal cycling of the thermal process of+0.5mm) the HAZ solidus curve when being equivalent to the SAW welding of big heat input of 100kJ/mm.That is, be heated to 1400 ℃, after this temperature keeps 5 seconds, carry out from 800 ℃ to 500 ℃ till 730 seconds cooling heat circulation.Also has the thermal cycling of the thermal process of the HAZ in zone when having carried out being equivalent to above-mentioned big heat input welding, apart from about solidus curve 3～5mm.That is, be heated to 1200 ℃, after this temperature keeps 5 seconds, carry out from 800 ℃ to 500 ℃ till 730 seconds cooling heat circulation.From these each test films, take each pendulum impact test sheet, measure vE
0(1400 ℃ and 1200 ℃).Then, difference vE
0For being evaluated as the welding joint tenacity excellent more than the 150J.
(oxide compound that contains Ti)
Size to the oxide compound that contains Ti that exists in the mother metal is measured by the following method.
(position of taking test portion) locates
In 1/4 position of thickness of slab, the test portion of taking can be observed the section parallel with rolling direction.Use resulting test portion, as described below, having measured median size respectively is the above thick oxide compounds that contain Ti of 2 μ m, and median size is the number of the fine oxide compound that contains Ti of 0.05～1.0 μ m.
Median size is the mensuration of the above thick oxide compound number that contains Ti of 2 μ m
Use above-mentioned EPMA device, to 100mm
2(zone of 10mm * 10mm) is observed for 200 times with multiplying power, and measuring median size is the number of the above thick oxide compound that contains Ti of 2 μ m.Also have, the size that contains the oxide compound of Ti is, obtains the equivalent round shaped grain footpath of crystal grain, is averaged crystal grain diameter value (down with).
Median size is the mensuration of the fine oxide compound number that contains Ti of 0.05～1.0 μ m
Use above-mentioned FE-SEM/EDX device, the composition that 20 median sizes are the inclusion of 0.05～1 μ m is analyzed, obtain the ratio that contains the oxide compound that contain Ti of Ti more than 10 quality %.Then, at 0.1mm
2The zone in, use 1000 times reflection electronic picture, to 0.01mm arbitrarily
210 visuals field take, by image analysis apparatus, the number of the inclusion of median size 0.05～1 μ m is measured, the total number in these 10 visuals field and the ratio of the above-mentioned Ti of containing oxide compound multiply each other, and enlarge 1000 times in addition again, obtain every 1cm
2The number of the oxide compound that contains Ti of median size 0.05～1.0 μ m.These results represent in table 3 and table 4.
As table 1,3 clear and definite shown in, example 1～20 comprises and the parameter of 20C (%)+1.5Mn (%)+Cu (%)+Ni (%) satisfies composition of the present invention, and dissolved oxygen content and hold-time all form according to preferred melting method manufacturing.
Therefore, median size is the mean number of the oxide compound that contains Ti of 0.05～1 μ m, is 10000/cm when observing with 1000 times of multiplying powers
2More than, and median size is that the mean number of the above oxide compound that contains Ti of 2 μ m is 2000/cm when observing with 200 times of multiplying powers
2Below.This result can obtain the strength of parent of 590～780MPa level and the base metal tenacity more than the 210J.Also have, the thermal cycling characteristic is same, the vE of 1400 ℃ and 1200 ℃
0All can obtain the above toughness of 150J.
These results demonstrate, even under the situation of the Plate Steel of high-intensity 590～780MPa level, comprise that particularly toughness descends easily, apart near the welding heat affected zone above-mentioned solid phase line 3～5mm, the toughness in the whole zone of HAZ in the time of also can significantly improving big heat welding.
To this, clearly show any elementary composition all outside scope of the present invention of comparative example 21～29,32 from table 2,4.
Also have, comparative example 30～31, the parameter of 20C (%)+1.5Mn (%)+Cu (%)+Ni (%) is outside the scope of the invention.
In addition, comparative example 33～35, composition consist of within the invention scope, and dissolved oxygen content or hold-time make outside the condition of preferred melting method and form.
Its result, comparative example, strength of parent and base metal tenacity are compared low with example, and perhaps strength of parent is identical with example with base metal tenacity, but the thermal cycling characteristic, the vE of 1400 ℃ and 1200 ℃
0All significantly low.
These results demonstrate, these comparative examples outside the scope of the invention, under the situation of the Plate Steel of high-intensity 590～780MPa level, particularly comprise apart near the welding heat affected zone solidus curve 3～5mm the toughness in the whole zone of HAZ when not having to improve big heat welding.
For example, comparative example 21 is because the C amount is excessive, so although satisfy the regulation of the oxide compound that contains Ti, its thermal cycling characteristic (HAZ toughness) is significantly low.
Comparative example 22, because the Mn quantity not sufficient, so can not guarantee strength of parent, although satisfy the regulation of the oxide compound that contains Ti, thermal cycling characteristic (HAZ toughness) is poor.
Comparative example 23 is because the Mn amount is excessive, so although satisfy the regulation of the oxide compound that contains Ti, thermal cycling characteristic (HAZ toughness) is poor.
Comparative example 24, because the Al amount is excessive, the thick oxide compound that contains Ti is too much, so the thermal cycling characteristic is poor.
Comparative example 25 is because the Cu amount is excessive, so although satisfy the regulation of the oxide compound that contains Ti, thermal cycling characteristic (HAZ toughness) is poor.
Comparative example 26 is because the Ni amount is excessive, so although satisfy the regulation of the oxide compound that contains Ti, thermal cycling characteristic (HAZ toughness) is poor.
Comparative example 27, because the Ti amount is excessive, the fine oxide compound that contains Ti is very few, so thermal cycling characteristic (HAZ toughness) is poor.
Comparative example 28, the oxygen quantity not sufficient is because the dissolved oxygen content during melting also seldom, so the fine oxide compound that contains Ti is very few, so thermal cycling characteristic (HAZ toughness) is poor.
Comparative example 29, the oxygen amount is excessive, and the dissolved oxygen content during owing to melting is also excessive, and so the thick oxide compound that contains Ti is too much, the fine oxide compound that contains Ti tails off, and thermal cycling characteristic (HAZ toughness) is poor.
Comparative example 32 is because the boron amount is excessive, so although satisfy the regulation of the oxide compound that contains Ti, base metal tenacity and thermal cycling characteristic (HAZ toughness) are poor.
Comparative example 30, the parameter of 20C (%)+1.5Mn (%)+Cu (%)+Ni (%) is lower than 4.5%, outside the scope of the invention.Therefore, no matter whether C, Mn, Cu, Ni contain in each specified amount scope, 1200 ℃ thermal cycling characteristic is poor, does not have to improve the toughness of HAZ3～5mm part.This is because there is not to bring into play the effect of the above-mentioned increase hardenability of C, Mn, Cu, Ni, the bainite structure that can not the refinement intracrystalline generates.
Comparative example 31, above-mentioned parameter surpasses 7.0%, outside the scope of the invention.Therefore, no matter whether C, Mn, Cu, Ni contain in each specified amount scope, 1200 ℃ thermal cycling characteristic is poor, does not have to improve the toughness of HAZ3～5mm part.This is because because the amount of formed MA (martensite) increase in the MA bainite structure has reduced the toughness in the whole zone of HAZ on the contrary.
Comparative example 33, because the dissolved oxygen content before the interpolation Ti of smelt stage is too much, the thick oxide compound that contains Ti is separated out in a large number, has surpassed the number of regulation.Therefore, thermal cycling characteristic is at 1400 ℃ vE
0For about 102J, toughness is significantly low.
Comparative example 34, because the hold-time of the stationary state behind the interpolation Ti of smelt stage is too short, the thick oxide compound that contains Ti is separated out in a large number, has surpassed the number of regulation, the fine in addition oxide compound that contains Ti is less relatively.Therefore, thermal cycling characteristic is at 1400 ℃ vE
0For about 85J, toughness is significantly low.
Comparative example 35, because the hold-time of the stationary state behind the interpolation Ti of smelt stage is long, the thick oxide compound that contains Ti is separated out in a large number, has surpassed the number of regulation, the fine in addition oxide compound that contains Ti is less relatively.Therefore, thermal cycling characteristic is at 1400 ℃ vE
0For about 99J, toughness is significantly low.
Proved from above result, one-tenth of the present invention is grouped into, with the regulation of the oxide compound that contains Ti, under the situation of the Plate Steel of high-intensity 590～780MPa level, particularly comprise apart near the welding heat affected zone solidus curve 3～5mm, the critical meaning of the tough property improvement in the whole zone of HAZ during big heat welding.
[table 1]
[table 2]
[table 3]
[table 4]
[industrial utilize possibility]
As described above, according to the present invention, even can provide a kind of when carrying out big heat input welding, The steel plate of 590～780MPa level that welding point toughness (HAZ toughness) is excellent. Therefore, originally The steel plate of invention can be suitable for the high strength of boats and ships, marine structure, bridge, building structure etc. The use of welded structure.
Claims (4)
1. the Plate Steel of one kind big heat input welding joint tenacity excellent, it is characterized in that, in quality %, each contains C:0.01～0.07%, Si:1.0% is following and do not comprise 0%, Mn:1.0～3.0%, Al: be lower than 0.010% and do not comprise 0%, Ti:0.005～0.050%, O:0.0010～0.01 00%, contain Cu:0.1～1.5% in addition, more than in Ni:0.1～2.5% any, and, 20C%+1.5Mn%+Cu%+Ni% is 4.5～7.0%, remainder is essentially iron and unavoidable impurities
Median size is that the mean number that contains the Ti oxide compound of 0.05～1 μ m is 10000/cm when observing with 1000 times of multiplying powers
2More than, and median size is that the above mean number that contains the Ti oxide compound of 2 μ m is 2000/cm when observing with 200 times of multiplying powers
2Below;
Described Plate Steel be smelt stage with the molten steel before adding Ti in dissolved oxygen content be controlled in the scope of 20～100ppm and after adding Ti in the molten steel and kept 10～50 minutes with stationary state, make.
2. the Plate Steel of big heat input welding joint tenacity excellent according to claim 1, it is characterized in that, above-mentioned Plate Steel also contain Cr:0.1～2.0%, Mo:0.1～1.0%, Nb:0.10% following and do not comprise 0%, V:0.10% is following and do not comprise more than any one or two kinds of in 0%.
3. the Plate Steel of big heat input welding joint tenacity excellent according to claim 1 is characterized in that above-mentioned Plate Steel also contains B:0.0005～0.0050%.
4. the Plate Steel of big heat input welding joint tenacity excellent according to claim 1, it is characterized in that, above-mentioned Plate Steel also contain Zr:0.05% following and do not comprise 0%, Mg:0.0050% is following and do not comprise 0%, Ca:0.0050% is following and do not comprise 0%, REM:0.0050% is following and do not comprise more than any one or two kinds of in 0%.
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|---|---|---|---|
| JP2004312916 | 2004-10-27 | ||
| JP2004312916A JP4311740B2 (en) | 2004-10-27 | 2004-10-27 | Thick steel plate with high heat input welded joint toughness |
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| BRPI0607524B1 (en) * | 2006-12-20 | 2016-01-19 | Nippon Steel & Sumitomo Metal Corp | steel and method of its production |
| NO343351B1 (en) * | 2006-12-20 | 2019-02-04 | Nippon Steel Corp | Steel with excellent toughness in welding heat affected welding zone and method of manufacture thereof |
| JP4976906B2 (en) * | 2007-04-09 | 2012-07-18 | 株式会社神戸製鋼所 | Thick steel plate with excellent HAZ toughness, base material toughness, elongation, and strength-elongation balance |
| JP4891836B2 (en) * | 2007-05-09 | 2012-03-07 | 株式会社神戸製鋼所 | Steel plate with excellent toughness of weld heat affected zone in high heat input welding |
| JP5201665B2 (en) * | 2007-11-13 | 2013-06-05 | 株式会社神戸製鋼所 | High strength thick steel plate for welding with excellent toughness of heat affected zone during high heat input welding |
| KR100957940B1 (en) * | 2007-12-13 | 2010-05-13 | 주식회사 포스코 | High strength Steel Plate for High Heat Input Welding having Welded Joint with Superior Impact Toughness in Weld Heat Affected Zone |
| KR100957982B1 (en) * | 2007-12-24 | 2010-05-17 | 주식회사 포스코 | Steel for Welding Structure having Welded Joint with Superior CTOD Properties in Weld Heat Affected Zone |
| KR100910493B1 (en) * | 2007-12-26 | 2009-07-31 | 주식회사 포스코 | Flux Cored Arc Weld Metal Joint Having Superior CTOD in Low Temperature |
| CN101925685B (en) * | 2008-07-30 | 2013-01-02 | 新日本制铁株式会社 | High-strength thick steel products excellent in toughness and weldability, high-strength ultra-thick h shape steel and processes for manufacturing both |
| KR101151577B1 (en) * | 2008-12-22 | 2012-05-31 | 가부시키가이샤 고베 세이코쇼 | Steel plate |
| JP5493557B2 (en) * | 2009-07-31 | 2014-05-14 | Ｊｆｅスチール株式会社 | Steel material for large heat input welding |
| JP5630322B2 (en) * | 2011-02-24 | 2014-11-26 | Ｊｆｅスチール株式会社 | High-tensile steel plate with excellent toughness and manufacturing method thereof |
| US9403242B2 (en) | 2011-03-24 | 2016-08-02 | Nippon Steel & Sumitomo Metal Corporation | Steel for welding |
| JP5824434B2 (en) * | 2011-11-14 | 2015-11-25 | 株式会社神戸製鋼所 | Thick steel plate with excellent toughness in weld heat affected zone |
| EP2784168B1 (en) * | 2011-11-25 | 2016-11-23 | Nippon Steel & Sumitomo Metal Corporation | Steel material for welding |
| JP5811044B2 (en) * | 2012-06-13 | 2015-11-11 | 新日鐵住金株式会社 | Thick high-strength steel sheet excellent in weldability and weld heat-affected zone toughness and method for producing the same |
| CN104364405B (en) * | 2013-06-13 | 2016-12-07 | 新日铁住金株式会社 | Welding super high tensile steel plate |
| CN103741079A (en) * | 2014-01-09 | 2014-04-23 | 鞍钢股份有限公司 | Ultrahigh-strength steel plate for ocean engineering and production method thereof |
| JP7248896B2 (en) * | 2019-06-17 | 2023-03-30 | 日本製鉄株式会社 | High strength steel plate for high heat input welding |
| CN112501488B (en) * | 2020-10-22 | 2021-10-26 | 福建三宝钢铁有限公司 | Preparation process of H08A steel |
| CN112281065B (en) * | 2020-10-28 | 2022-03-29 | 龙岩学院 | 780 MPa-grade high-heat-input welding steel for improving toughness of heat affected zone and manufacturing method thereof |
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| JP4022019B2 (en) * | 1998-07-16 | 2007-12-12 | 新日本製鐵株式会社 | High-strength cold-rolled steel sheet with excellent formability after welding and difficult to soften weld heat-affected zone |
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| KR20060049390A (en) | 2006-05-18 |
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