CN101849026A - Steel for weld construction having excellent high-temperature strength and low-temperature toughness and process for producing the steel - Google Patents
Steel for weld construction having excellent high-temperature strength and low-temperature toughness and process for producing the steel Download PDFInfo
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- CN101849026A CN101849026A CN200980000058A CN200980000058A CN101849026A CN 101849026 A CN101849026 A CN 101849026A CN 200980000058 A CN200980000058 A CN 200980000058A CN 200980000058 A CN200980000058 A CN 200980000058A CN 101849026 A CN101849026 A CN 101849026A
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- 229910000831 Steel Inorganic materials 0.000 title claims abstract description 110
- 239000010959 steel Substances 0.000 title claims abstract description 110
- 238000000034 method Methods 0.000 title claims description 17
- 238000010276 construction Methods 0.000 title abstract description 5
- 230000008569 process Effects 0.000 title description 2
- 238000001816 cooling Methods 0.000 claims abstract description 22
- 239000000203 mixture Substances 0.000 claims abstract description 17
- 238000005098 hot rolling Methods 0.000 claims abstract description 13
- 239000012535 impurity Substances 0.000 claims abstract description 12
- XEEYBQQBJWHFJM-UHFFFAOYSA-N Iron Chemical compound [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims abstract description 10
- 229910052742 iron Inorganic materials 0.000 claims abstract description 5
- 238000003466 welding Methods 0.000 claims description 22
- 238000004519 manufacturing process Methods 0.000 claims description 17
- 229910052758 niobium Inorganic materials 0.000 abstract description 9
- 229910052804 chromium Inorganic materials 0.000 abstract description 7
- 238000010438 heat treatment Methods 0.000 abstract description 7
- 238000005336 cracking Methods 0.000 abstract description 3
- 229910052799 carbon Inorganic materials 0.000 abstract description 2
- 229910052757 nitrogen Inorganic materials 0.000 abstract description 2
- 229910052748 manganese Inorganic materials 0.000 abstract 1
- 229910052750 molybdenum Inorganic materials 0.000 abstract 1
- 229910052698 phosphorus Inorganic materials 0.000 abstract 1
- 230000000694 effects Effects 0.000 description 20
- 230000000052 comparative effect Effects 0.000 description 13
- 230000006866 deterioration Effects 0.000 description 13
- 239000002184 metal Substances 0.000 description 11
- 229910052751 metal Inorganic materials 0.000 description 11
- 238000005096 rolling process Methods 0.000 description 10
- 230000009466 transformation Effects 0.000 description 9
- 230000009970 fire resistant effect Effects 0.000 description 6
- 208000037656 Respiratory Sounds Diseases 0.000 description 5
- 229910001566 austenite Inorganic materials 0.000 description 5
- 230000008859 change Effects 0.000 description 5
- 239000011248 coating agent Substances 0.000 description 5
- 238000000576 coating method Methods 0.000 description 5
- 239000000463 material Substances 0.000 description 5
- 239000002244 precipitate Substances 0.000 description 5
- 150000001875 compounds Chemical class 0.000 description 4
- 239000013078 crystal Substances 0.000 description 4
- 210000003746 feather Anatomy 0.000 description 4
- 238000001556 precipitation Methods 0.000 description 4
- ATJFFYVFTNAWJD-UHFFFAOYSA-N Tin Chemical compound [Sn] ATJFFYVFTNAWJD-UHFFFAOYSA-N 0.000 description 3
- 229910001563 bainite Inorganic materials 0.000 description 3
- 239000012467 final product Substances 0.000 description 3
- QGZKDVFQNNGYKY-UHFFFAOYSA-N Ammonia Chemical compound N QGZKDVFQNNGYKY-UHFFFAOYSA-N 0.000 description 2
- RWSOTUBLDIXVET-UHFFFAOYSA-N Dihydrogen sulfide Chemical compound S RWSOTUBLDIXVET-UHFFFAOYSA-N 0.000 description 2
- UFHFLCQGNIYNRP-UHFFFAOYSA-N Hydrogen Chemical compound [H][H] UFHFLCQGNIYNRP-UHFFFAOYSA-N 0.000 description 2
- 230000001133 acceleration Effects 0.000 description 2
- 229910001567 cementite Inorganic materials 0.000 description 2
- 230000003749 cleanliness Effects 0.000 description 2
- 230000007613 environmental effect Effects 0.000 description 2
- 229910052739 hydrogen Inorganic materials 0.000 description 2
- 239000001257 hydrogen Substances 0.000 description 2
- 229910000037 hydrogen sulfide Inorganic materials 0.000 description 2
- KSOKAHYVTMZFBJ-UHFFFAOYSA-N iron;methane Chemical compound C.[Fe].[Fe].[Fe] KSOKAHYVTMZFBJ-UHFFFAOYSA-N 0.000 description 2
- 239000011159 matrix material Substances 0.000 description 2
- 238000001953 recrystallisation Methods 0.000 description 2
- 230000009467 reduction Effects 0.000 description 2
- 238000005204 segregation Methods 0.000 description 2
- 238000009628 steelmaking Methods 0.000 description 2
- 229910000859 α-Fe Inorganic materials 0.000 description 2
- 208000034189 Sclerosis Diseases 0.000 description 1
- 229910000746 Structural steel Inorganic materials 0.000 description 1
- UCKMPCXJQFINFW-UHFFFAOYSA-N Sulphide Chemical compound [S-2] UCKMPCXJQFINFW-UHFFFAOYSA-N 0.000 description 1
- 238000005275 alloying Methods 0.000 description 1
- 239000010953 base metal Substances 0.000 description 1
- 230000015572 biosynthetic process Effects 0.000 description 1
- 229910052796 boron Inorganic materials 0.000 description 1
- 239000000470 constituent Substances 0.000 description 1
- 238000009749 continuous casting Methods 0.000 description 1
- 229910052802 copper Inorganic materials 0.000 description 1
- 230000007797 corrosion Effects 0.000 description 1
- 238000005260 corrosion Methods 0.000 description 1
- 238000005520 cutting process Methods 0.000 description 1
- 230000002939 deleterious effect Effects 0.000 description 1
- 238000005516 engineering process Methods 0.000 description 1
- 238000002474 experimental method Methods 0.000 description 1
- 230000009975 flexible effect Effects 0.000 description 1
- 239000007789 gas Substances 0.000 description 1
- 238000005469 granulation Methods 0.000 description 1
- 230000003179 granulation Effects 0.000 description 1
- 229910052749 magnesium Inorganic materials 0.000 description 1
- 229910052759 nickel Inorganic materials 0.000 description 1
- 230000008520 organization Effects 0.000 description 1
- 238000010791 quenching Methods 0.000 description 1
- 229920006395 saturated elastomer Polymers 0.000 description 1
- 238000003860 storage Methods 0.000 description 1
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- 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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
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- 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
- 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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
- C21D8/0226—Hot rolling
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- 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
- C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
- C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
- C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
- C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
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- 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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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- 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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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/22—Ferrous alloys, e.g. steel alloys containing chromium with molybdenum or tungsten
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/24—Ferrous alloys, e.g. steel alloys containing chromium with vanadium
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/26—Ferrous alloys, e.g. steel alloys containing chromium with niobium or tantalum
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/28—Ferrous alloys, e.g. steel alloys containing chromium with titanium or zirconium
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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/38—Ferrous alloys, e.g. steel alloys containing chromium with more than 1.5% by weight of manganese
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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
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/46—Ferrous alloys, e.g. steel alloys containing chromium with nickel with vanadium
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
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- C21D2211/00—Microstructure comprising significant phases
- C21D2211/004—Dispersions; Precipitations
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- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
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Abstract
Disclosed is a steel for weld construction that has excellent high-temperature strength and low-temperature toughness and can be produced at low cost. The steel for weld construction is produced by heating a steel product comprising C: 0.003 to 0.05%, Si: not more than 0.60%, Mn: 0.6 to 2.0%, P: not more than 0.020%, S: not more than 0.010%, Cr: 0.20 to 1.5%, Nb: 0.005 to 0.05%, Al: not more than 0.060%, N: 0.001 to 0.006%, and Mo as an impurity limited to not more than 0.03% with the balance consisting of iron and unavoidable impurities, the steel product having a weld cracking susceptibility composition (PCM) value, defined by PCM = C + Si/30 + Mn/20 + Cu/20 + Ni/60 + Cr/20 + Mo/15 + V/10 + 5B, of not more than 0.22%, to 1000 to 1300 DEG C, terminating the hot rolling at a temperature of 800 DEG C or above, and then cooling the steel product.
Description
Technical field
The present invention is that the building structure refractory steel that the yield strength during with high temperature such as fire is maintained purpose is the invention of major objective, but be not limited to construction applications, use etc. the steel for welded structures of extensive use applicable to marine structure, boats and ships, bridge, various storage tank jar.In addition, the master is the so-called rank that is commonly referred to as 40 feather weight, 50 feather weight steel of yield strength 235～475MPa, tensile strength 400～640MPa as the strength level of the steel plate of object.
Background technology
Guaranteeing that high-temperature yield strength is the so-called fire-resistant steel of the construction applications of purpose, open with the spy and to disclose a lot of technical schemes headed by flat 2-77523 communique etc., its major part contains Mo.Really Mo is guaranteeing on the high-temperature yield strength of steel it is utmost point effective elements, but also is the element of high price simultaneously.
, standardized general structural steel in Japanese Industrial Standards (JIS) etc. reduce from about 350 ℃ of intensity, so its permissible temperature is about 350 ℃.Promptly; in the occasion that above-mentioned steel is used for the buildings of mansion, office, inhabitation, sky parking etc.; security during in order to ensure fire; the sufficient fireproof coating of obligated enforcement; in each relevant decree of the building of Japan, stipulated when fire, to avoid the steel temperature to reach more than 350 ℃.This is because above-mentioned steel become about 2/3 of normal temperature 350 ℃ of left and right sides yield strengths, less than the cause of necessary strength.Therefore, general steel are used for the occasion of fabrication, must implement fireproof coating, avoiding when the fire, the temperature of steel reaches 350 ℃.
In order to omit or to alleviate this fireproof coating, (following when not showing especially, so-called high temperature is meant 600 ℃ to the high-temperature yield strength when having improved the high temperature tension test under 600 ℃ of grades, and so-called hot strength is meant high-temperature yield strength.) fire-resistant steel begin to be used.
Usually, in fire-resistant steel, be that purpose is added Mo to keep hot strength., the market condition of Mo changes greatly, though also depend on addition, the situation that is in a ratio of high price with the fireproof coating cost is more.Therefore, the wait in expectation exploitation and the practicability of fire-resistant steel of the cheapness of not adding Mo.
The objective of the invention is, obtain a kind of Mo that does not add high price, hot strength excellence and as the also excellent steel for welded structures of the low-temperature flexibility of one of fundamental property of steel.For this reason, by composition of steel is limited to specified range, thereby and limits manufacture method and provide a kind of industrial stable and can supply with the hot strength excellence with low cost, suppress welding crack sensibility, guaranteed the method for the fire-resistant steel of low-temperature flexibility.
According to the present invention,, therefore can help the security of various broad-spectrum welded steel structure things to improve even can be in a large number and the steel for welded structures that suffers the pyritous environment also to have sufficient yield strength when supplying with fire at an easy rate etc.
Inventive point of the present invention is, in order stably to guarantee the hot strength under 600 ℃, by compound interpolation relatively the C amount of trace and the Mo that Cr and Nb replace high price, the precipitation strength that utilizes phase-change organization to strengthen and bring by the precipitate (carbonitride) of Cr, Nb.
Promptly find, improve the hardening capacity of steel by the Cr that under the situation of no Mo, adds, contains appropriate amount, the transformation temperature reduction, the hard tissue that contains cementite becomes bainite (bainitic).
Find thus, in normal temperature strength and hot strength raising, matrix be under low temperature relatively phase transformation fine bainite structure, therefore when high temperature, independent or compound carbonitride utmost point in its matrix of Cr that is caused by the compound interpolation of Cr and Nb and Nb is separated out imperceptibly, can guarantee, keep hot strength with high level, thereby finish the present application.
As mentioned above, do not contain the fire-resistant steel of Mo, itself utmost point is epoch-making, and simultaneously owing to do not contain the high Mo of hardening capacity, therefore as the fundamental property (intensity, toughness) of steel for welded structures much less, weldability, gas cutting be instead raising also.
The present application is also stipulated to form P with the content and the welding crack sensibility of each element headed by C, Si, the Mn by not only stipulating Cr, Nb
CM, and limit and to create conditions, thereby not only under the situation of the Mo that does not use high price, have both excellent hot strength and low-temperature flexibility, and guaranteed various use propertieies as steel for welded structures.Its main idea is as follows.
(1) manufacture method of the steel for welded structures of a kind of hot strength and low-temperature flexibility excellence, it is characterized in that, following steel are heated to 1000～1300 ℃ temperature, finish hot rolling system in the temperature more than 800 ℃, cool off then, its composition of described steel is counted with quality %
C：0.003～0.05％、
Below the Si:0.60%,
Mn：0.6～2.0％、
Below the P:0.020%,
Below the S:0.010%,
Cr：0.20～1.5％、
Nb：0.005～0.05％、
Below the Al:0.060%,
N：0.001～0.006％，
And will be limited in as the Mo of impurity below 0.03%, rest part is made of iron and unavoidable impurities, by P
CMThe welding crack sensibility of=C+Si/30+Mn/20+Cu/20+Ni/60+Cr/20+Mo/15+V/10+5B definition is formed P
CMValue is below 0.22%.
(2) according to the manufacture method of the steel for welded structures of (1) described hot strength and low-temperature flexibility excellence, it is characterized in that, finish above-mentioned hot rolling system after, quicken cooling since the temperature more than 750 ℃, stop to quicken cooling in the temperature below 550 ℃.
(3) manufacture method of the steel for welded structures of basis (1) or (2) described hot strength and low-temperature flexibility excellence is characterized in that % also contains in quality
V：0.01～0.10％、
Ti：0.005～0.025％
Among any one or two kinds of.
(4) manufacture method of the steel for welded structures of each described hot strength of basis (1)～(3) and low-temperature flexibility excellence is characterized in that % also contains in quality
Ni：0.05～0.50％、
Cu：0.05～0.50％、
B：0.0002～0.003％、
Mg：0.0002～0.005％
Among any one or two kinds of more than.
(5) manufacture method of the steel for welded structures of each described hot strength of basis (1)～(4) and low-temperature flexibility excellence is characterized in that % also contains in quality
Ca：0.0005～0.004％、
REM：0.0005～0.008％
Among any.
(6) steel for welded structures of a kind of hot strength and low-temperature flexibility excellence, it is characterized in that, be following steel to be heated to 1000～1300 ℃ temperature, finishes hot rolling system in the temperature more than 800 ℃, cool off then and obtain, its composition of described steel is counted with quality %
C：0.003～0.05％、
Below the Si:0.60%,
Mn：0.6～2.0％、
Below the P:0.020%,
Below the S:0.010%,
Cr：0.20～1.5％、
Nb：0.005～0.05％、
Below the Al:0.060%,
N：0.001～0.006％，
And will be limited in as the Mo of impurity below 0.03%, rest part is made of iron and unavoidable impurities, by P
CMThe welding crack sensibility of=C+Si/30+Mn/20+Cu/20+Ni/60+Cr/20+Mo/15+V/10+5B definition is formed P
CMValue is below 0.22%.
Embodiment
Interpolation scope for each alloying element of stipulating among the present invention describes.
C：0.003～0.05％
As high-strength steel, C is defined in extremely low level.The composition of it and other is together closely related with manufacture method.Among composition of steel, C is the element that brings maximum influence to the characteristic of steel.Lower limit 0.003% is that the heat affected zone of guaranteeing intensity, avoiding welding etc. softens to necessary above minimum value.
When C content was too much, hardening capacity was increased to more than necessity, caused detrimentally affect can for the balance, weldability etc. of the strength and toughness of steel.In addition, as described later,, have under lower temperature, to stop to quicken the refrigerative situation, at this moment,, the upper limit is defined as 0.05% in order to suppress near the extreme sclerosis the steel surface back side, the material change of thickness of slab direction according to thickness of slab, the intensity of target.
From operation change, consider that with the balance of other compositions reduce for fear of intensity, lower limit is preferably 0.005%, and then more preferably 0.01%.In addition, for fear of the change of over-drastic quench hardening, material, the upper limit is preferably 0.04%, and more preferably 0.03%.
Below the Si:0.60%
Si is the element that contains in steel for deoxidation, if add morely, and then weldability, HAZ toughness deterioration, so the upper limit is defined as 0.60%.The deoxidation of steel also can adopt Ti, Al to carry out, therefore according to determining that with the balance of these elements content gets final product., consider from the viewpoint of HAZ toughness, hardening capacity etc., low more preferred more, can not add yet.Therefore, can be 0.40%, 0.20%, 0.10% also with ceiling restriction.In addition, in the occasion of steel-making factory manufacturing steel, even do not add Si and utilize Ti, Al to come also to contain the Si more than 0.01% under the situation of deoxidation usually.
Mn：0.6～2.0％
Mn is guaranteeing indispensable element on the intensity of normal temperature, the toughness, is being limited to 0.6% under it.Be preferably more than 0.8% or more than 1.0%., Mn measures when too much, and hardening capacity rises, and not only makes weldability, HAZ toughness deterioration, and encourages the center segregation of continuous casting steel billet, so the upper limit is defined as 2.0%.Be preferably below 1.8%, more preferably below 1.6% or below 1.4%.
Below the P:0.020%
P has the tendency of the intercrystalline failure minimizing that makes among the HAZ at its content after a little while, and is therefore few more preferred more.If content is many, then make the low-temperature flexibility deterioration of mother metal, welding zone, so the upper limit is defined as 0.020%.More preferably below 0.015%, below 0.010% or below 0.008%.Can certainly not add.
Below the S:0.010%
From the viewpoint of the low-temperature flexibility of mother metal, S is few more preferred more.If content is many, then make the low-temperature flexibility deterioration of mother metal, welding zone, so the upper limit is defined as 0.010%.More preferably below 0.008%, 0.006%, 0.004%.Can certainly not add.
Cr：0.20～1.5％
Cr is one of most important element in the present application.In order to ensure hot strength, must together add Cr with Nb.This is because because the hardening capacity of Cr improves effect, transformation temperature reduces, the hard tissue that contains cementite becomes bainite, intensity when therefore improving normal temperature and high temperature, and when high temperature is utilized the cause of the precipitation strength that the precipitate (carbonitride) by Cr brings.
In order to enjoy these effects, the content of Cr is minimum to be required to be 0.20%.Be preferably more than 0.35%, more preferably more than 0.50%, more than 0.8% or 1.0%.,, then cause the toughness of mother metal, welding zone and the deterioration of weldability, also lose economy, so the upper limit is defined as 1.5% if addition is too much.Be preferably below 1.3%.
Nb：0.005～0.05％
Nb and Cr one are both the most important element in the present application.Precipitation strength same with Cr, utilize the precipitate (carbonitride) by Nb to bring in order to ensure hot strength.
Therefore, be required to be more than 0.005% at least.Be preferably more than 0.010%., if addition is too much, then cause the toughness deterioration of welding zone, so the upper limit is defined as 0.05%.Be preferably below 0.045%, more preferably below 0.030%.In addition, the interpolation of Nb can make austenitic non-recrystallization temperature rise the effect of the controlled rolling when also helping to bring into play hot rolling system to greatest extent.
By the compound interpolation of above-mentioned Cr and Nb, can not guarantee hot strength even there is Mo yet.Therefore, in the present application, do not carry out the interpolation of having a mind to of Mo.In addition, as the Mo of impurity be limited under the situation of by mistake sneaking into below 0.03%.
Below the Al:0.060%
Al is generally deoxidation and the element that contains in steel.Deoxidation also can adopt Si or Ti to carry out, therefore according to determining that with the balance of these elements its content gets final product., if Al content increases, the then cleanliness factor variation of steel not only, and the toughness deterioration of weld metal, so the upper limit is defined as 0.060%.Be preferably below 0.040%.Its content is few more preferred more, also can not add.In addition, in the occasion of steel-making factory manufacturing steel, even usually do not utilize Al to carry out also containing the Al more than 0.001% under the situation of deoxidation.
N：0.001～0.006％
N is the element that contains in steel as unavoidable impurities, but combines the formation carbonitride with Nb, and intensity is increased, and in addition, forms TiN, improves the performance of steel as described above.Therefore, as N content, minimumly be required to be 0.001%.Be preferably more than 0.0015%.Yet the increase of N content is harmful to welding heat influence area toughness, weldability, in steel of the present invention, is limited to 0.006% on it.More preferably below 0.0045%.
Then the interpolation reason to V, the Ti that can contain as required describes.
V：0.01～0.10％
V has the effect roughly same with Nb, and the effect of the V in the present application is to replenish Nb's.But V compares with Nb, and effect is little, and hardening capacity is also impacted, and therefore bound is limited.Lower limit is minimum as the effect that can enjoy interpolation V effectively, is defined as 0.01%.Be preferably more than 0.025%.The upper limit is considered welding crack sensibility described later is formed P
CMInfluence, be defined as 0.10%.Be preferably below 0.08%, more preferably below 0.05%.
Ti：0.005～0.025％
Preferably add Ti in order to improve mother metal and welding heat influence area toughness.Reason be Ti Al content after a little while (for example below 0.003%) combine with O, form with Ti
2O
3Be the precipitate of principal constituent, become the ferritic nuclear of generation intragranular phase transformation, welding heat influence area toughness is improved.
In addition, Ti combines with N, as TiN fine separating out in steel, thickization of the γ crystal grain when suppressing heating is effective to the grain refined of rolling structure.And the fine TiN that exists in the steel makes welded heat affecting zone organize grain refined when welding, and toughness is improved.In order to obtain these effects, Ti is minimum to be required to be 0.005%., make low-temperature flexibility, weldability deterioration, so its upper limit is defined as 0.025% if many mistakes then form TiC.Be preferably below 0.020%.
Then the interpolation reason for Ni, Cu, B, Mg describes.
Also adding the main purpose of these elements in basic composition, is that characteristics such as intensity, toughness are improved.Therefore be its addition element of confined character naturally and understandably.
Ni：0.05～0.50％
Ni then can not cause detrimentally affect and the intensity of mother metal, toughness are improved if do not add not superfluously weldability, welding heat influence area toughness.In order to bring into play these effects, must add more than 0.05% at least.
On the other hand, high price is not only in superfluous interpolation, and is also not preferred on weldability.In addition, if add Ni morely, then in liquid ammonia, has the possibility of bringing out stress corrosion cracking (SCC).According to present inventors' experiment, the interpolation up to 1.0% can not make weldability, the SCC in liquid ammonia deterioration greatly, improves intensity, the flexible effect is big, but be that preferentially the upper limit is defined as 0.50% with the economy.Further pay the utmost attention to the occasion of economy, also may be limited to 0.35%.
Cu：0.05～0.50％
Cu shows and roughly same effect, the phenomenon of Ni that superfluous interpolation except the weldability deterioration, also produces Cu fracturing line when hot rolling system, cause making difficulty, so ceiling restriction is 0.50%.Lower limit should be 0.05% for the minimum of the effect that can obtain essence.Pay the utmost attention to the occasion of economy, also can be with ceiling restriction 0.30%.
B：0.0002～0.003％
B suppresses ferritic generation in the austenite grain boundary segregation, and hardening capacity is improved, and helps intensity to improve.In order to enjoy this effect, minimum being required to be more than 0.0002%.
, too much interpolation, not only hardening capacity raising effect is saturated, and the possibility of deleterious B precipitate on the toughness of being formed on is arranged, so the upper limit is defined as 0.003%.Be preferably below 0.002%.In addition, as jar with steel etc., worry under the situation of stress saprophage crackle, it is more (for example in order to prevent sulfide stress saprophage crackle (SCC) that the hardness that reduces mother metal and welded heat affecting zone becomes the situation of key point, must make Rockwell hardness is HRC≤22 (HV≤248)), in such a case, preferably do not add the B that hardening capacity is increased.In addition,, there is the problem of adding the material deterioration of the heat affected zone toughness that causes etc. by B,, more preferably B is limited in below 0.0003% or do not add therefore for fear of these problems though B has the effect of raising intensity as described above.
Mg：0.0002～0.005％
Mg suppresses austenite crystal growth, the effect with grain refined, the highly malleablized that can seek the welding zone in welded heat affecting zone.In order to enjoy such effect, Mg is required to be more than 0.0002%.On the other hand, then little if addition increases with respect to the effect quantitative change of addition, on cost, be not very wise move therefore, so the upper limit is defined as 0.005%.Be preferably below 0.0035%.
Then the interpolation reason to Ca or REM describes.
Ca：0.0005～0.004％
REM：0.0005～0.008％
The form of Ca and REM control MnS, the low-temperature flexibility of raising mother metal also makes the hydrogen under moistening hydrogen-sulfide environmental bring out the reduction of crackle (HIC, SSC, SOHIC) susceptibility in addition.In order to bring into play these effects, minimumly be required to be 0.0005%.
; too much interpolation instead the cleanliness factor of steel is worsened, makes the base metal tenacity deterioration and makes the hydrogen under moistening hydrogen-sulfide environmental bring out the raising of crackle (HIC, SSC, SOHIC) susceptibility; so the upper limit of addition, Ca, REM are defined as 0.004%, 0.008% respectively.Preferably be respectively below 0.003%, below 0.006%.In addition, Ca and REM have roughly equal effect, therefore add any and get final product in above-mentioned scope, also can add both.
Even limit each composition of steel,, also can not get excellent characteristic if composition system is whole inappropriate.In the present application,, form P by the welding crack sensibility of following formula definition according to the content (quality %) of each element
CMValue be limited to below 0.22%.
P
CM＝C+Si/30+Mn/20+Cu/20+Ni/60+Cr/20+Mo/15+V/10+5B
P
CMBe the index of expression weldability, low more weldability is good more.In JIS G 3106 " Rolled Steel For Welded Structure ", though, be defined as below 0.24% also according to strength level, thickness of slab and difference is the strictest.
To the various welding crack tests of steel grade widely, as the condition that also can prevent welding cold cracking under stricter contained condition, envrionment conditions conscientiously, is with P according to present inventors
CMBe defined as below 0.22%.In addition, though lower limit is not particularly limited,, naturally and understandably restricted by the limited range of each composition.
Then, describe creating conditions.
Heating temperature before hot rolling system is limited to 1000～1300 ℃ reason, is that the austenite crystal in order will to heat the time keeps less, seeks the miniaturization of rolling structure.1300 ℃ is that the austenite in when heating not have the ceiling temperature of thickization terrifically, if Heating temperature is above this value, and the thick mixed granulation of austenite crystal then, microstructure after phase transformation is thickization also, so the remarkable deterioration of the toughness of steel.
On the other hand,,, not only be difficult to guarantee rolling end temp described later, and from the viewpoint of the solutionizing of the Nb that is used to make austenitic non-recrystallization temperature rise, present precipitation strength, lower limit is defined as 1000 ℃ then according to thickness of slab if Heating temperature is low excessively.Most preferred Heating temperature scope is 1050～1250 ℃.
To cool off after the end hot rolling system more than 800 ℃ at the steel that heat under the above-mentioned condition.Cooling way does not limit especially.Can be positioned in the atmosphere and cool off, but, can improve the characteristic of steel more by quicken to be cooled to the temperature below 550 ℃ from the temperature more than 750 ℃.
Rolling end temp is if be lower than 800 ℃, and then in the fewer the present application steel of C content, ferrite transformation is separated out, and might process (rolling) ferrite, and is not preferred aspect guaranteeing in low-temperature flexibility.Therefore, rolling end temp is limited to more than 800 ℃.Be preferably more than 820 ℃.
After finishing hot rolling system more than 800 ℃, the so-called 40 feather weight steel that strength ratio is lower (for example SM400 of JIS standard, SN400 steel) cool off the intensity that also can satisfy regulation even be positioned in the atmosphere.
; if 50 feather weight steel (for example SM490 of JIS standard, SN490 steel) or in 40 kilograms of steel thickness of slab thicken, then under the cooling attitude in being positioned over atmosphere, also be difficult to the stable intensity of guaranteeing; therefore preferably after finishing hot rolling system more than 800 ℃, from the acceleration of the temperature more than 750 ℃ cooling.Acceleration cooling after rolling is in order to improve the characteristic of steel more, not damage the feature of the excellence of the present application.
Quickening cooling, is to be used for will organizing miniaturization, the cooling that intensity and toughness are improved simultaneously by the cooling rate of accelerating the phase change zone after all.Therefore, if begin preceding or do not begin before phase transformation finishes at least, then nonsensical in fact in phase transformation.Therefore, quickening cooling beginning temperature limit fixes on more than 750 ℃.This quickens cooling, enjoying on its effect, must be cooled to the temperature below 550 ℃.When for the temperature above 550 ℃, the phase transformation when quickening cooling is not fully carried out, and the miniaturization of tissue is insufficient.Therefore preferably quicken refrigerative to begin temperature be more than 760 ℃, preferably quickening the scope that refrigerative stops temperature is below 520 and more than 300 ℃.
In addition, speed of cooling when quickening cooling, also depend on composition of steel, the intensity of being sought, low-temperature flexibility level, but preferred: the thickness of slab direction from the surface 1/4 position for thickness of slab, be more than 3 ℃/second from the average cooling rate that quickens cooling beginning temperature to 550 ℃.
In addition,, add the following temper of Ac1 temperature, also can not damage the feature of the excellence of the present application even for cooled rolling stock.Preferred without hesitation for homogeneity in the plate of eliminating refrigerative ununiformity, raising material.
Embodiment
(thickness 19～100mm) has been investigated its material to adopt converter-continuous casting-slab operation to make the steel plate of various composition of steel.
Table 1 illustrates the composition of steel of comparative steel and the present application steel, and table 2 illustrates creating conditions of steel plate and various characteristics.
Steel plate (steel of the present invention) according to the present application is made all has good characteristic.Relative therewith, the steel plate of not making (comparative steel) as can be known according to the present application, certain specific character is relatively poor.
Comparative steel 11 is because therefore C content height compares the low-temperature flexibility inequality of mother metal, simulated HAZ with the present application steel.
Comparative steel 12 is not added Nb, and in addition, the Cr content of comparative steel 13 is low, so hot strength is all low.
Comparative steel 14 is because C content is low, so hot strength is low.
Comparative steel 15 is because Cr content height, so the toughness inequality of mother metal, simulated HAZ.
Comparative steel 16 is because the Nb amount is high, so the HAZ poor toughness.
The composition of comparative steel 17-1～17-3 is identical with the present application steel 5., the rolling end temp of comparative steel 17-1 is low, as a result of, quicken cooling beginning temperature and can not guarantee and step-down, so normal temperature strength, hot strength is all low.Comparative steel 17-2 is because to quicken cooling beginning temperature low, so normal temperature strength, hot strength are all low.Comparative steel 17-3 stops the temperature height owing to quicken cooling, so normal temperature strength, hot strength are all low.
Comparative steel 18, though each element, manufacture method in the present application scope, normal temperature and pyritous intensity, toughness etc. satisfy the desired characteristic as the 490MPa level, P
CMTherefore height has produced crackle on weldability (tiltedly y type welding crack test).
Utilize possibility on the industry
According to the present invention, can be in a large number and the steel for welded structures of elevated temperature strength and excellent in low temperature toughness is provided at an easy rate. Its result as building structure usefulness, can alleviate or omit fireproof coating. In addition, in the purposes beyond building, also possess the key property of intensity, toughness etc., but also possess elevated temperature strength, therefore as the welded structure steel that might suffer high temperature, the security that can more improve works.
Among the present invention the expression number range " more than " and " following " include given figure.
Claims (6)
1. the manufacture method of the steel for welded structures of hot strength and low-temperature flexibility excellence, it is characterized in that, following steel are heated to 1000～1300 ℃ temperature, finish hot rolling system in the temperature more than 800 ℃, cool off then, its composition of described steel is counted with quality %
C：0.003～0.05％、
Below the Si:0.60%,
Mn：0.6～2.0％、
Below the P:0.020%,
Below the S:0.010%,
Cr：0.20～1.5％、
Nb：0.005～0.05％、
Below the Al:0.060%,
N:0.001～0.006%, and will be limited in as the Mo of impurity below 0.03%, rest part is made of iron and unavoidable impurities, by P
CMThe welding crack sensibility of=C+Si/30+Mn/20+Cu/20+Ni/60+Cr/20+Mo/15+V/10+5B definition is formed P
CMValue is below 0.22%.
2. the manufacture method of the steel for welded structures of hot strength according to claim 1 and low-temperature flexibility excellence is characterized in that, finish described hot rolling system after, quicken cooling since the temperature more than 750 ℃, stop to quicken cooling in the temperature below 550 ℃.
3. the manufacture method of the steel for welded structures of hot strength according to claim 1 and 2 and low-temperature flexibility excellence is characterized in that % also contains in quality
V：0.01～0.10％、
Any one or two kinds of among Ti:0.005～0.025%.
4. according to the manufacture method of the steel for welded structures of each the described hot strength of claim 1～3 and low-temperature flexibility excellence, it is characterized in that % also contains in quality
Ni：0.05～0.50％、
Cu：0.05～0.50％、
B：0.0002～0.003％、
More than any one or two kinds of among Mg:0.0002～0.005%.
5. according to the manufacture method of the steel for welded structures of each the described hot strength of claim 1～4 and low-temperature flexibility excellence, it is characterized in that % also contains in quality
Ca：0.0005～0.004％、
Among REM:0.0005～0.008% any.
6. the steel for welded structures of hot strength and low-temperature flexibility excellence, it is characterized in that, be following steel to be heated to 1000～1300 ℃ temperature, finishes hot rolling system in the temperature more than 800 ℃, cool off then and obtain, its composition of described steel is counted with quality %
C：0.003～0.05％、
Below the Si:0.60%,
Mn：0.6～2.0％、
Below the P:0.020%,
Below the S:0.010%,
Cr：0.20～1.5％、
Nb：0.005～0.05％、
Below the Al:0.060%,
N:0.001～0.006%, and will be limited in as the Mo of impurity below 0.03%, rest part is made of iron and unavoidable impurities, by P
CMThe welding crack sensibility of=C+Si/30+Mn/20+Cu/20+Ni/60+Cr/20+Mo/15+V/10+5B definition is formed P
CMValue is below 0.22%.
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| PCT/JP2009/050906 WO2010082361A1 (en) | 2009-01-15 | 2009-01-15 | Steel for weld construction having excellent high-temperature strength and low-temperature toughness and process for producing the steel |
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| CN101849026A true CN101849026A (en) | 2010-09-29 |
| CN101849026B CN101849026B (en) | 2012-07-04 |
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| US (1) | US20110262298A1 (en) |
| EP (1) | EP2380997B1 (en) |
| JP (1) | JP4834149B2 (en) |
| KR (1) | KR101189263B1 (en) |
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| CN102373387A (en) * | 2011-11-02 | 2012-03-14 | 武汉钢铁(集团)公司 | Steel plate for large-strain cold-bent tube and manufacturing method thereof |
| CN103114186A (en) * | 2013-03-15 | 2013-05-22 | 济钢集团有限公司 | Control cooling method of easy-welding high-performance steel plate |
| CN108368581A (en) * | 2016-01-18 | 2018-08-03 | 株式会社神户制钢所 | Forging quality steel and large-scale steel forgings |
| CN114763593A (en) * | 2021-01-12 | 2022-07-19 | 宝山钢铁股份有限公司 | Marine engineering steel with high humidity and heat atmosphere corrosion resistance and manufacturing method thereof |
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| JP5073396B2 (en) * | 2007-07-20 | 2012-11-14 | 新日本製鐵株式会社 | Manufacturing method of welded structural steel with excellent high temperature strength and low temperature toughness |
| CN102400049B (en) * | 2010-09-07 | 2014-03-12 | 鞍钢股份有限公司 | 490-grade fireproof steel plate for building structure and manufacturing method thereof |
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| EP3666911B1 (en) | 2018-12-11 | 2021-08-18 | SSAB Technology AB | High-strength steel product and method of manufacturing the same |
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| JPH06293915A (en) * | 1993-04-07 | 1994-10-21 | Nippon Steel Corp | Production of low alloy steel plate for line pipe excellent in co2 corrosion resistance and sour resistance |
| JPH08209241A (en) * | 1995-02-02 | 1996-08-13 | Nippon Steel Corp | Production of steel plate for line pipe excellent in carbon dioxide corrosion resistance and low temperature toughness |
| JPH08295929A (en) * | 1995-04-26 | 1996-11-12 | Nippon Steel Corp | Production of sour resistant steel sheet for line pipe excellent in co2 corrosion resistance and low temperature toughness |
| JP3873540B2 (en) * | 1999-09-07 | 2007-01-24 | Ｊｆｅスチール株式会社 | Manufacturing method of high productivity and high strength rolled H-section steel |
| CN1169991C (en) * | 2001-10-19 | 2004-10-06 | 住友金属工业株式会社 | Thin steel plate with good machining performance and formed precision and its mfg. method |
| EP1777315B1 (en) * | 2004-07-21 | 2012-03-14 | Nippon Steel Corporation | Steel for welded structure excellent in low temperature toughness of heat affected zone of welded part, and method for production thereof |
| JP4555694B2 (en) * | 2005-01-18 | 2010-10-06 | 新日本製鐵株式会社 | Bake-hardening hot-rolled steel sheet excellent in workability and method for producing the same |
| JP4709632B2 (en) * | 2005-10-28 | 2011-06-22 | 新日本製鐵株式会社 | Manufacturing method of high strength steel for welded structure with excellent high temperature strength and low temperature toughness |
| JP4571915B2 (en) * | 2006-02-08 | 2010-10-27 | 新日本製鐵株式会社 | Refractory thick steel plate and manufacturing method thereof |
| JP5098207B2 (en) * | 2006-04-11 | 2012-12-12 | 新日鐵住金株式会社 | Manufacturing method of high strength steel for welded structure with excellent high temperature strength and low temperature toughness |
| JP5098317B2 (en) * | 2006-12-08 | 2012-12-12 | 新日鐵住金株式会社 | Manufacturing method of welded structural steel with excellent high temperature strength and low temperature toughness |
| JP5073396B2 (en) * | 2007-07-20 | 2012-11-14 | 新日本製鐵株式会社 | Manufacturing method of welded structural steel with excellent high temperature strength and low temperature toughness |
-
2009
- 2009-01-15 KR KR1020097012504A patent/KR101189263B1/en active IP Right Grant
- 2009-01-15 EP EP09707108.8A patent/EP2380997B1/en active Active
- 2009-01-15 CN CN2009800000583A patent/CN101849026B/en not_active Expired - Fee Related
- 2009-01-15 JP JP2009509204A patent/JP4834149B2/en not_active Expired - Fee Related
- 2009-01-15 BR BRPI0901011A patent/BRPI0901011B1/en not_active IP Right Cessation
- 2009-01-15 WO PCT/JP2009/050906 patent/WO2010082361A1/en active Application Filing
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Cited By (7)
| Publication number | Priority date | Publication date | Assignee | Title |
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| CN102373387A (en) * | 2011-11-02 | 2012-03-14 | 武汉钢铁(集团)公司 | Steel plate for large-strain cold-bent tube and manufacturing method thereof |
| CN102373387B (en) * | 2011-11-02 | 2013-05-22 | 武汉钢铁(集团)公司 | Steel plate for large-strain cold-bent tube and manufacturing method thereof |
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| CN103114186B (en) * | 2013-03-15 | 2015-04-08 | 济钢集团有限公司 | Control cooling method of easy-welding high-performance steel plate |
| CN108368581A (en) * | 2016-01-18 | 2018-08-03 | 株式会社神户制钢所 | Forging quality steel and large-scale steel forgings |
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Also Published As
| Publication number | Publication date |
|---|---|
| WO2010082361A1 (en) | 2010-07-22 |
| BRPI0901011B1 (en) | 2019-09-10 |
| JPWO2010082361A1 (en) | 2012-06-28 |
| CN101849026B (en) | 2012-07-04 |
| BRPI0901011A2 (en) | 2015-11-24 |
| KR20100105821A (en) | 2010-09-30 |
| EP2380997A4 (en) | 2016-12-28 |
| EP2380997B1 (en) | 2020-01-08 |
| EP2380997A1 (en) | 2011-10-26 |
| KR101189263B1 (en) | 2012-10-09 |
| US20110262298A1 (en) | 2011-10-27 |
| JP4834149B2 (en) | 2011-12-14 |
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