CN101633993A - Steel with excellent toughness at welding heat influence part - Google Patents
Steel with excellent toughness at welding heat influence part Download PDFInfo
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- CN101633993A CN101633993A CN200910152111A CN200910152111A CN101633993A CN 101633993 A CN101633993 A CN 101633993A CN 200910152111 A CN200910152111 A CN 200910152111A CN 200910152111 A CN200910152111 A CN 200910152111A CN 101633993 A CN101633993 A CN 101633993A
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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
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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
- C22C38/04—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
Abstract
The invention provides an HAZ steel with excellent toughness which properly adjusts the chemical composition to disperse proper compound oxide in the steel organism, and makes the TiN which is disappeared due to the heat in welding not disperse so as to cause HAZ toughness to be excellent. The steel has 0.02-0.10% of C, less than 0.5% (not including 0%) of Si, 1.0-2.0% of Mn, less than 0.03% (not including 0%) of P, less than 0.02 (not including 0%) of S, less than 0.05% (not including 0%) of Al, 0.005-0.10% of Ti, 0.001-0.007% of REM, 0.001-0.050% of Zr, 0.002-0.010% of N, 0.001-0.010% of Ca and 0.0010-0.015% of O; and the value A prescribed in the relation is in a range of 500-6000.
Description
Technical field
The present invention relates to when employed steel such as welded bridge, high-rise and boats and ships, the toughness that is subjected to the position (hereinafter referred to as " welding heat affected zone " or " HAZ ") of heat affecting has been carried out the steel that improve.
Background technology
Be used in the desired characteristic of steel of bridge, high-rise and boats and ships etc., increasingly stringent requires to have good especially toughness in recent years.These steel are general many with welded joint, are subjected to heat affecting and the easy deterioration of toughness but the special problem that exists is HAZ when welding.This toughness deterioration embodies significantly more when the heat input in when welding is big more, and its reason is considered to be, if the heat input during welding is big more, the speed of cooling of HAZ is slow more, and hardenability reduces and generates thick island martensite body.Therefore in order to improve HAZ toughness, the heat input when doing one's utmost to suppress to weld gets final product.And on the other hand, improving on the welding operation efficient, the large-line energy welding process of for example electro-gas welding and solder flux-copper lining welding process etc. is adopted in expectation.
Therefore, even proposed when adopting the large-line energy welding process, also can suppress the steel of HAZ flexible deterioration.For example in patent documentation 1, proposition has a kind of by hanging down Cization, low Siization and hanging down the area occupation ratio that Nization reduces the island martensite body, makes the good steel of toughness of HAZ.Also open in this technology in addition, suppress thickization of austenite crystal (γ crystal grain) by the nitride that forms Ti and Zr, and nitride particles is also being brought into play the effect that makes HAZ organize miniaturization as authorizing the effect of waving from the ferrite transformation of γ intracrystalline.Also open in this external this technology, the fine oxide and the thioester thing that contain Ca, REM (rare earth element), Mg are dispersed in the steel, and the miniaturization of γ crystal grain is achieved thus, and can guarantee intensity, and the toughness of HAZ is improved.
Yet, when studying, present inventors find, if welding metal reaches high temperature more than 1400 ℃, then among the HAZ, particularly near the position (hereinafter referred to as " fusion portion ") of welding metal because the thermal conductance that is subjected to during welding causes above-mentioned TiN solid solution disappears, thereby can not suppress the toughness deterioration.
On the other hand, disclose a kind of technology in patent documentation 2, it is the sulfide (or complex sulfide) that contains the oxide compound of Ca and Mg and contain Ca, Cu, Mg etc. by formation, thereby the toughness that realizes HAZ improves.In addition, from can make good this viewpoint of toughness of HAZ by formation composite oxides steel, also propose relevant for forming, thereby improve the flexible technology (for example patent documentation 3～5) of HAZ by the composite oxides that make the oxide compound that contains REM and/or CaO and ZrO.
If the technology that research is proposed up to now, what then can judge is that it is exceedingly useful to the toughness of improving HAZ that composite oxides are dispersed in the steel.Particularly think composite oxides are dispersed in the steel, also can solid solution not disappear, the toughness of HAZ is improved even when welding, be subjected to heat affecting.Yet when carrying out the large-line energy welding, the realization that expectation can further improve the flexible steel of HAZ also is true.
[patent documentation 1] spy opens the 2002-194490 communique
[patent documentation 2] spy opens the 2004-169048 communique
[patent documentation 3] spy opens the 2007-100213 communique
[patent documentation 4] spy opens the 2007-247004 communique
Summary of the invention
The present invention is just under this situation and do, its purpose is, the extremely excellent steel of toughness of a kind of HAZ (welding heat affected zone) are provided, it is formed by suitably adjusting chemical ingredients, make the suitable composite oxides of dispersion in the steel tissue, and the TiN that the heat that is subjected in the time of can be because of welding by making not disappears disperses, thereby makes the toughness of HAZ (welding heat affected zone) extremely excellent.
The so-called steel of the present invention that can solve above-mentioned problem have following some main idea: contain the C:0.02～0.10% (meaning of " quality % " respectively.Down with), Si:0.5% following (not containing 0%), Mn:1.0～2.0%, P:0.03% following (not containing 0%), S:0.02% following (not containing 0%), Al:0.05% following (not containing 0%), Ti:0.005～0.10%, REM:0.001～0.007%, Zr:0.001～0.050%, N:0.002～0.010%, Ca:0.001～0.010% and O:0.0010～0.015%, and be in 500～6000 scope by the A value of following formula (1) regulation.
A value=[Ca] * [N] * 10
8(1)
Wherein, [Ca] and [N] represents the content (quality %) of Ca and N respectively.
In the steel of the present invention, as other elements preferably also contain among the following element more than a kind: Ni:1.50% following (not containing 0%), Cu:1.50% following (not containing 0%), Cr:1.5% following (not containing 0%), Mo:1.5% following (not containing 0%), Nb:0.25% following (not containing 0%), V:0.10% following (not containing 0%) and below the B:0.005% (not containing 0%), contain the intensity that as above element can improve mother metal.Also have, the surplus of described steel also can be iron and unavoidable impurities.
According to the present invention, the balance of the content by both keeping Ca and N, suitably adjusting chemical composition of steel again forms, thereby make the suitable composite oxides of dispersion in the steel tissue, even and by making because of the welding TiN that also can not disappear that the time is heated disperses, can realize the extremely excellent steel of toughness of HAZ (welding heat affected zone), this steel are when welding, be not limited to little～middle heat input welding,, also can prevent the toughness deterioration of welding heat affected zone (HAZ) even large-line energy welds.
Embodiment
Present inventors' research repeatedly with further being embodied as target of flexible steel that has improved welding heat affected zone.It found that, if be adjusted into following chemical constitution, promptly as dispersive composite oxides in the steel tissue, form for the composite oxides that contain REM, Zr and Ti, even and the TiN that also can not disappear such that is heated when welding is disperseed, then the toughness of welding heat affected zone further improves, thus the present invention fully.
Contain the composite oxides (below be designated as " Ti/REM/Zr composite oxides ") of REM, Zr and Ti,, more effectively bringing into play pinning effect, thereby suppress thickization of γ crystal grain γ crystal grain compared with the composite oxides that propose up to now.And steel of the present invention, in the effect of performance from these composite oxides, also make disperse in the steel nitride particles (TiN) as from the γ intracrystalline ferrite transformation nuclear play a role effectively (that is, improving the intracrystalline phase-change energy), make HAZ toughness excellent more thus.
, about TiN, under known composition at common steel is adjusted, if reach the high temperature of 1400 ℃ of levels, then solid solution disappearance (patent documentation 1) in steel.So TiN only makes above-mentioned such composite oxides disperse when solid solution disappears in steel, improves at the HAZ flexible to have limitation on the effect, can not bring into play the HAZ toughness of hope.This tendency is remarkable when hanging down N.
Therefore, even present inventors just reach the high temperature of 1400 ℃ of levels, the situation that also can solid solution in steel disappear is studied.Consequently,,, also can keep the coexisting state of above-mentioned composite oxides and TiN, can guarantee high-caliber HAZ toughness even then under the high temperature of large-line energy welding if contain the appropriate amount Ca of corresponding N content.That is, the A value that makes following formula (1) defined is 500～6000 scope, contains N content and C content so evenly, even then under the high temperature of large-line energy welding, the coexisting state of above-mentioned composite oxides and TiN also can be kept.
A value=[Ca] * [N] * 10
8(1)
Wherein, [Ca] and [N] represents the content (quality %) of Ca and N respectively.
The A value of following formula (1) defined is 500 when above, even under the high temperature of large-line energy welding, TiN also is difficult to disappear, and the effect that improves the intracrystalline phase-change energy obtains performance, can keep HAZ toughness and improve effect.But superfluous if above-mentioned A value becomes above 6000, then the thick inclusion of TiN, CaO, CaS etc. generates, and HAZ toughness is deterioration on the contrary.The preferred lower limit of above-mentioned A value is 2000.
By the A value of following formula (1) defined is controlled within the limits prescribed,,, think it to be because compared with the stronger CaS generation of the conformability of MnS and TiN about its reason even TiN also is difficult to disappear under the high temperature of large-line energy welding.
Steel of the present invention contain aforementioned such Ti/REM/Zr composite oxides, but such oxide compound will form by the suitable content of adjusting Ti, REM and Zr.And even this composite oxides the time are subjected to heat affecting and the high temperature that reaches 1400 ℃ of levels also can not disappear in solid solution in welding, therefore the HAZ when welding can prevent thickization of austenite crystal, as toughness deterioration that consequently can enough hand HAZ.
In steel of the present invention, above-mentioned such composite oxides form, can pass through with for example EPMA (Electron Probe X-ray Micro Analyzer, electronic probe X ray micro-zone analysis instrument) observes the cross section of steel, the inclusion that is confirmed in the field of view is carried out quantitative analysis and confirms.
Next, describe with regard to chemical composition of steel composition of the present invention.Steel of the present invention, for above-mentioned such Ti/REM/Zr composite oxides and TiN are disperseed, need suitably to adjust the element (Ti, REM, Zr, N) that constitutes them, and, also need suitably to adjust the content of Ca, and stipulate the reasons are as follows of scope of the basal component (C, Si, Mn, P, S, Al, O) of its content and steel.
[C：0.02～0.10％]
C is used to guarantee the intensity of steel (mother metal) and the element that can not be short of, and in order to bring into play this effect, need make it to contain more than 0.02%.Yet if C content surpasses 0.10%, HAZ generates the island martensite body in a large number when welding, and not only causes the toughness deterioration of HAZ, and weldability is also had disadvantageous effect.Therefore C content need be suppressed at below 0.10%.
[Si:0.5% following (not containing 0%)]
Si has desoxydatoin, and is the element that helps the intensity raising of steel (mother metal).In order to bring into play such effect effectively, preferably make it to contain more than 0.02%, more preferably contain more than 0.05%, further preferably contain more than 0.1%.But if Si content surpasses 0.5%, then therefore the weldability of steel (mother metal) and base metal tenacity deterioration need be suppressed at below 0.5%.Preferably be suppressed at below 0.45%, more preferably be suppressed at below 0.4%.Also have, when HAZ was required high tenacity, Si preferably was suppressed at below 0.3%.More preferably below 0.05%, further preferably below 0.01%.But, suppress Si content if so, though then the toughness of HAZ improves, intensity has the tendency of reduction.
[Mn：1.0～2.0％]
Mn is the element that helps the intensity raising of steel (mother metal), in order to bring into play this effect effectively, need make it to contain more than 1.0%.Preferably contain more than 1.3%.Yet if Mn content surplus makes the weldability deterioration of steel (mother metal), so need be suppressed at below 2.0%.Preferably below 1.7%.
[P:0.03% following (not containing 0%)]
P is the element of easy segregation, particularly the grain boundary segregation in steel and make the toughness deterioration.Therefore P need be suppressed at below 0.03%, preferably below 0.02%, more preferably below 0.015%.
[S:0.02% following (not containing 0%)]
S combines with Mn and generates sulfide (MnS), is the deleterious element that makes the deteriorated ductility of the toughness of mother metal and thickness of slab direction.S combines with La and Ce and generates LaS and CeS in addition, hinders the generation of oxide compound.Therefore S should be suppressed at below 0.02%, preferably below 0.015%, more preferably below 0.008%, particularly preferably in below 0.006%.
[Al:0.05% following (not containing 0%)]
Al is the strong element of deoxidation power, if add superfluously, and then can reduced oxide and be difficult to generate the oxide compound of expectation.Therefore, Al need be suppressed at below 0.05%, preferably below 0.03%, more preferably below 0.01%.
[Ti：0.005～0.10％]
Ti generates nitride and Ti/REM/Zr composite oxides such as TiN in steel, be the element that helps the toughness raising of HAZ.Bring into play such effect effectively for sending out, Ti need contain more than 0.005%, is preferably more than 0.007%, more preferably more than 0.01%.But if add superfluously, then make the toughness deterioration of steel (mother metal), therefore should be suppressed at below 0.10%.Preferably below 0.07%, more preferably below 0.06%.
[REM：0.001～0.007％]
REM (rare earth element) forms the Ti/REM/Zr composite oxides with Ti and Zr, is the element that helps the toughness raising of HAZ.In order to bring into play this effect effectively, REM is contained more than 0.001%, be preferably more than 0.002%.Yet if contain superfluously, the REM of solid solution condition increases, and therefore the toughness deterioration of mother metal should be suppressed at below 0.007%.Be preferably below 0.005%.Also have in the present invention, so-called REM is the meaning that contains lanthanon (15 kinds of elements from La to Ln) and Sc (scandium) and Y (yttrium), among these elements, preferably contains a kind of element selecting among La, Ce and the Y, more preferably contains La and/or Ce.
[Zr：0.001～0.050％]
Zr forms the Ti/REM/Zr composite oxides with Ti and REM, is the element that helps the toughness raising of HAZ.In order to bring into play this effect effectively, should make Zr content more than 0.001%, be preferably more than 0.002%.But if add superfluously, the carbide of then thick Zr generates, and therefore the toughness deterioration of mother metal should be suppressed at below 0.050%.Be preferably below 0.04%, more preferably below 0.03%.
[N：0.002～0.010％]
N is the element of separating out TiN, and TiN prevents thickization (pinning effect) of the austenite crystal that HAZ generates when welding, and promotes ferrite transformation (intracrystalline phase-change energy), therefore helps to make the toughness of HAZ to improve.In order to bring into play such effect effectively, N is contained more than 0.002%, be preferably more than 0.004%.The miniaturization of the many more austenite crystals of N obtains more promoting that the toughness that therefore acts on HAZ effectively improves.Yet if N content surpasses 0.010%, solid solution N measures increase, base metal tenacity deterioration.Therefore N need be suppressed at below 0.010%, is preferably below 0.008%.But the A value that N content certainly need above-mentioned according to making (1) formula defined is in the mode of the scope of regulation and adjusts.
[Ca：0.001～0.010％]
The disappearance of TiN when Ca suppresses the welding of high heat input is to make the toughness from TiN improve the element that effect obtains bringing into play effectively.By containing Ca, even under low N, can guarantee that also toughness improves needed TiN.In order to bring into play this effect effectively, Ca is contained more than 0.001%.More preferably more than 0.002%.But if add superfluously, then thick CaO and CaS generate, and therefore need be suppressed at below 0.010%.Be preferably below 0.009%, more preferably below 0.008%.But Ca content is the same with N content, and A value that certainly need above-mentioned according to making (1) formula defined is in the mode of the scope of regulation and adjusts.
[O：0.0010～0.015％]
O is the needed element of Ti/REM/Zr composite oxides that forms intracrystalline phase-change energy excellence.In order to bring into play this effect, O is contained more than 0.0010%.Yet, superfluous if O content becomes, generate thick oxide compound, HAZ toughness is deterioration on the contrary, therefore need be for below 0.015%.Also having the preferred lower limit of O content is 0.0020%.
The basal component of steel of the present invention as mentioned above, but the element more than a kind that contains as required among Ni:1.50% following (not containing 0%), Cu:1.50% following (not containing 0%), Cr:1.5% following (not containing 0%), Mo:1.5% following (not containing 0%), Nb:0.25% following (not containing 0%), V:0.10% following (not containing 0%) and the B:0.005% following (not containing 0%) is also effective, by containing these elements, can improve the intensity of steel.Stipulate the reasons are as follows of scope like this.
Ni is for the intensity that improves steel, and is the element that effectively plays a role for the toughness that improves steel, in order to bring into play such effect, preferably makes it to contain more than 0.05%.More preferably more than 0.1%, more preferably more than 0.2%.Though Ni is many more preferred more, because it is the element of high price, thus preferably be suppressed at below 1.50% from the viewpoint of economy, more preferably below 1.3%, more preferably below 1.1%.
Cu is the element that makes the steel solution strengthening, in order to bring into play this effect effectively, preferably makes it to contain more than 0.05%.More preferably more than 0.1%, more preferably more than 0.2%.Particularly, except solution strengthening, also bring into play the timeliness precipitation strength, can significantly improve intensity if make it to contain more than 0.6%.Yet, make it to surpass 1.50% if contain Cu superfluously, the toughness of steel (mother metal) is reduced, so Cu can be suppressed at below 1.50%.Be preferably below 1.3%, more preferably below 1.1%.
Improve intensity in order to add Cr, preferably make it to contain more than 0.01%.More preferably more than 0.02%, more preferably more than 0.03%.Yet if Cr content surplus, therefore the weldability deterioration preferably is suppressed at below 1.5%.More preferably below 1.3%, more preferably below 1.1%.
Improve intensity in order to add Mo, preferably make it to contain more than 0.01%.Recommend more preferably more than 0.02%, more preferably more than 0.03%.But, if Mo content surplus then makes weldability worsen, therefore preferably below 1.5%.More preferably below 1.3%, more preferably below 1.0%.
Improve intensity in order to add Nb, preferably make it to contain more than 0.005%.More preferably more than 0.01%, more preferably more than 0.03%.Yet if Nb content surplus, carbide (NbC) is separated out and is made the toughness deterioration of mother metal, therefore preferably is suppressed at below 0.25%.More preferably below 0.23%, more preferably below 0.2%.
Improve intensity in order to add V, preferably make it to contain more than 0.002%.More preferably more than 0.01%, more preferably more than 0.03%.Yet, if V content surplus weldability worsens, and the toughness deterioration of mother metal, so V is preferably below 0.10%.More preferably be suppressed at below 0.08%, further preferably be suppressed at below 0.06%.
B improves the intensity of steel, and combine with N in the steel in the heated HAZ refrigerative process when welding and separate out BN, makes from the ferrite transformation in the austenite crystal and obtains promotion.In order to bring into play this effect effectively, preferably make it to contain more than 0.0003%.More preferably more than 0.0005%, more preferably more than 0.0008%.Yet if B content surplus, the toughness deterioration of steel (mother metal) therefore is preferably below 0.005%.More preferably below 0.004%, more preferably below 0.003%.
Steel of the present invention contain above-mentioned element as necessary composition, and surplus also can be iron and unavoidable impurities (for example Mg, As and Se etc.).
When making steel of the present invention, will as above-mentioned, will adjust the molten steel that chemical ingredients is formed, follow that ordinary method casts continuously and after becoming slab, follow ordinary method again and carry out hot rolling and get final product.Also have, the form of the REM that adds to molten steel and Ca, Zr, Ti is not particularly limited, for example add pure La and pure Ce, pure Y etc. get final product as REM, perhaps add pure Ca, pure Zr, pure Ti, add Fe-Si-La alloy, Fe-Si-Ce alloy, Fe-Si-Ca alloy, Fe-Si-La-Ce alloy, Fe-Ca alloy, Ni-Ca alloy etc. in addition and get final product.In addition, also can add norium to molten steel.So-called norium is exactly the mixture of cerium family rare earth element, is exactly that to contain Ce be about 40～50% specifically, and containing La is about 20～40%.
Much less the steel of the present invention that so obtain for example can use as the material of the works of bridge and high-rise, boats and ships etc., little～middle heat input welding, even also can prevent the toughness deterioration of welding heat affected zone in the large-line energy welding.
[embodiment]
Below, illustrate in greater detail the present invention by embodiment, but following embodiment not limiting character of the present invention, the scope of aim described later also can suitably change enforcement before can meeting, and these all are included in the scope of technology of the present invention.
Embodiment 1
Modulate the various molten steel that show chemical ingredients in the following table 1,2.Also have, in following table 1, La adds with the form of Fe-La alloy, Ce adds with the form of Fe-Ce alloy, REM with contain about La:50% and Ce:25% about the form of norium add, Ca adds with the form of Ni-Ca alloy or Ca-Si alloy or Fe-Ca press-powder body, and Zr adds with the Zr monomer, and Ti adds with the form of Fe-Ti alloy.Also have, element is not added in "-" expression in following table 1 and the table 2.There is the meaning of "＜" to be before the numerical value in addition,, contains inevitably, therefore be detected in the scope that is lower than quantitative boundary though do not add this element.
[table 1]
[table 2]
With continuous casting machine above-mentioned molten steel is cast as slab, it is carried out hot rolling and obtains the steel plate of thickness 30～60mm.For each steel plate, in order to estimate the toughness that welding the time is subjected to the HAZ of heat affecting, simulation large-line energy welding and carry out the welding shown in following and reproduce test.Test is reproduced in welding, and it is that the test film that will downcut from above-mentioned steel plate heats, and makes its integral body reach 1400 ℃, cools off after this temperature keeps 60 seconds.Be 300 seconds cooling time that makes 800 ℃ to 500 ℃, so adjusts speed of cooling.It is that heat input is the large-line energy welding of 50kJ/mm that the test hypothesis is reproduced in this welding.
The impact of cooled sample is to carry out the pendulum impact test of V otch, and the absorption under measuring-40 ℃ can (vE
-40) and estimate.VE
-40For being qualified (HAZ toughness is good) more than the 100J.Measurement result is presented in the following table 3 with the A value.
[table 3]
| ??No. | A value ([Ca] * ({ N} * 10 1) | ??vE -40??(J) |
| ??1 | ??4200 | ??181 |
| ??2 | ??6000 | ??179 |
| ??3 | ??600 | ??131 |
| ??4 | ??2000 | ??157 |
| ??5 | ??800 | ??124 |
| ??6 | ??3500 | ??154 |
| ??7 | ??3500 | ??126 |
| ??8 | ??2400 | ??158 |
| ??9 | ??3200 | ??130 |
| ??10 | ??3000 | ??152 |
| ??11 | ??4000 | ??122 |
| ??12 | ??2800 | ??148 |
| ??13 | ??2800 | ??124 |
| ??14 | ??8400 | ??78 |
| ??15 | ??＜210 | ??87 |
| ??16 | ??4800 | ??77 |
| ??17 | ??300 | ??65 |
| ??18 | ??7200 | ??73 |
| ??19 | ??200 | ??23 |
| ??20 | ??1200 | ??35 |
| ??21 | ??1200 | ??56 |
| ??22 | ??14300 | ??27 |
| ??23 | ??3000 | ??54 |
| ??24 | ??2800 | ??61 |
| ??25 | ??3500 | ??57 |
| ??26 | ??3200 | ??48 |
| ??27 | ??2400 | ??51 |
| ??28 | ??3000 | ??45 |
| ??29 | ??2400 | ??17 |
| ??30 | ??3600 | ??25 |
By these results as can be known, the example of the important document of the present invention regulation is satisfied in No.1～13rd, can access the good steel of toughness of welding heat affected zone.With respect to this, No.14～30th, the example of a certain important document of disengaging the present invention regulation, the toughness inequality of welding heat affected zone.
Claims (3)
1. the steel of the tenacity excellent of a welding heat affected zone, it is characterized in that, contain C:0.02～0.10% in quality %, Si:0.5% is following but do not contain 0%, Mn:1.0～2.0%, P:0.03% is following but do not contain 0%, S:0.02% is following but do not contain 0%, Al:0.05% is following but do not contain 0%, Ti:0.005～0.10%, REM:0.001～0.007%, Zr:0.001～0.050%, N:0.002～0.010%, Ca:0.001～0.010% and O:0.0010～0.015%, and, A value by following formula (1) regulation is in 500～6000 scope
A value=[Ca] * [N] * 10
8(1)
Wherein, [Ca] and [N] represents the mass percentage content of Ca and N respectively.
2. steel according to claim 1, it is characterized in that, in described steel, also contain below Ni:1.50% in quality % as other elements but do not contain 0%, below the Cu:1.50% but do not contain 0%, below the Cr:1.5% but do not contain 0%, below the Mo:1.5% but do not contain 0%, below the Nb:0.25% but do not contain 0%, below the V:0.10% but do not contain 0% and below the B:0.005% but do not contain more than one the element of selecting 0%.
3. steel according to claim 1 and 2 is characterized in that, surplus is iron and unavoidable impurities.
Applications Claiming Priority (2)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2008189909A JP5283998B2 (en) | 2008-07-23 | 2008-07-23 | Steel with excellent toughness in weld heat affected zone |
| JP2008189909 | 2008-07-23 |
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| Publication Number | Publication Date |
|---|---|
| CN101633993A true CN101633993A (en) | 2010-01-27 |
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| CN200910152111A Pending CN101633993A (en) | 2008-07-23 | 2009-07-14 | Steel with excellent toughness at welding heat influence part |
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| Country | Link |
|---|---|
| JP (1) | JP5283998B2 (en) |
| KR (1) | KR20100010903A (en) |
| CN (1) | CN101633993A (en) |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102605277A (en) * | 2011-01-18 | 2012-07-25 | 株式会社神户制钢所 | Steel material for structural member having excellent corrosion resistance |
| CN103361549A (en) * | 2012-03-30 | 2013-10-23 | 株式会社神户制钢所 | Steel plate with excellent hydrogen induced cracking resistance, and manufacturing method of the same |
| CN112176147A (en) * | 2020-10-13 | 2021-01-05 | 五矿营口中板有限责任公司 | Manufacturing method of normalized thick steel plate suitable for large-wire welding |
Family Cites Families (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH03207812A (en) * | 1990-01-05 | 1991-09-11 | Nippon Steel Corp | Manufacture of steel excellent in toughness of base metal and toughness of joint |
| JP3287125B2 (en) * | 1994-08-24 | 2002-05-27 | 住友金属工業株式会社 | High tensile steel |
| JPH08333651A (en) * | 1995-06-06 | 1996-12-17 | Nippon Steel Corp | Steel material excellent in heat-affected zone hardening resistance |
| JP4825057B2 (en) * | 2005-09-12 | 2011-11-30 | 株式会社神戸製鋼所 | Steel with excellent toughness of weld heat affected zone and its manufacturing method |
| JP4515430B2 (en) * | 2006-09-29 | 2010-07-28 | 株式会社神戸製鋼所 | Steel with excellent toughness and base metal toughness of weld heat affected zone and its manufacturing method |
-
2008
- 2008-07-23 JP JP2008189909A patent/JP5283998B2/en not_active Expired - Fee Related
-
2009
- 2009-06-19 KR KR1020090054695A patent/KR20100010903A/en not_active Application Discontinuation
- 2009-07-14 CN CN200910152111A patent/CN101633993A/en active Pending
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN102605277A (en) * | 2011-01-18 | 2012-07-25 | 株式会社神户制钢所 | Steel material for structural member having excellent corrosion resistance |
| CN102605277B (en) * | 2011-01-18 | 2015-10-14 | 株式会社神户制钢所 | The Steel material for structural member of excellent corrosion resistance |
| CN103361549A (en) * | 2012-03-30 | 2013-10-23 | 株式会社神户制钢所 | Steel plate with excellent hydrogen induced cracking resistance, and manufacturing method of the same |
| CN112176147A (en) * | 2020-10-13 | 2021-01-05 | 五矿营口中板有限责任公司 | Manufacturing method of normalized thick steel plate suitable for large-wire welding |
| CN112176147B (en) * | 2020-10-13 | 2021-06-08 | 五矿营口中板有限责任公司 | Manufacturing method of normalized thick steel plate suitable for large-wire welding |
Also Published As
| Publication number | Publication date |
|---|---|
| JP5283998B2 (en) | 2013-09-04 |
| JP2010024523A (en) | 2010-02-04 |
| KR20100010903A (en) | 2010-02-02 |
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Application publication date: 20100127 |