CN101586220A - The high-tensile steel of the toughness of welding heat affected zone and endurance crack resistance excellence - Google Patents
The high-tensile steel of the toughness of welding heat affected zone and endurance crack resistance excellence Download PDFInfo
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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
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- C22C38/001—Ferrous alloys, e.g. steel alloys containing N
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- 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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- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—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
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Abstract
Steel plate of the present invention is suitably controlled the value of prescribed relationship formula (1)～(3) formula regulation, and, count with diameter of equivalent circle and to contain the every 1mm of Ti nitride below the 0.05 μ m
2Have 5.0 * 10
6More than individual, wherein, count containing Ti nitride number and accounting for more than 75% of 0.01～0.03 μ m, contain the every 1mm of Cr carbide with what diameter of equivalent circle was counted 0.05～0.3 μ m with respect to all containing Ti nitride number with diameter of equivalent circle
2Have 5.0 * 10
3More than individual.According to this formation, even carried out the input heat when being the large-line energy welding of 30～100kJ/mm, can guarantee also that HAZ toughness is good, and, can suppress the advance rate of crackle, guarantee good fatigue lifetime.
Description
Technical field
The present invention relates to be applicable to the high-tensile steel and the manufacture method thereof of the welded structure of bridge and high-rise, boats and ships etc., the advance rate that particularly relates to the tenacity excellent of heat affected zone after the large-line energy welding of 30～100kJ/mm (below, abbreviate " HAZ " as) and can suppress crackle is guaranteed the high-tensile steel of good fatigue lifetime.
Background technology
In recent years, along with the maximization of above-mentioned various welded structures, thickness of slab is that the welding of the above high-tensile steel of 50mm is inevitable.Therefore, in all areas,, be the state that points to the above large-line energy welding of 30kJ/mm from the viewpoint of the improvement of welding procedure efficient.
But, carrying out large-line energy when welding, HAZ is heated to Xu Leng behind the pyritous austenite region, and therefore, what have near HAZ portion (particularly the welding seam part of HAZ portion) organizes thickization, the problem of the easy deterioration of toughness of its part.The toughness (below, be called " HAZ toughness ") of guaranteeing this HAZ portion well becomes permanent problem.
The technology of the HAZ toughness deterioration when being used to prevent the large-line energy welding has various motions so far.As improving HAZ flexible technology, be well known that it is effective disperseing to contain the Ti nitride in steel.As this technology, for example, shown in No. the 3746707th, Japanese Patent, having proposed in intensity is in the super bainitic steel of 590MPa level, realizes the optimizing of alloying element, and, guarantee good HAZ toughness by the control that contains the Ti nitride.
On the other hand, even present inventors hold the steel that pyritous heat affecting HAZ toughness when having taken the lead in proposing being subjected to welding in 2005-200716 number can deterioration yet the spy.In this technology, heavy addition N in steel, and suitably control the interpolation balance of Ti and B even the amount of the TiN that not solid solution exists is increased, improves HAZ toughness.
But in the field of welding, further requiring to improve HAZ toughness is truth.Particularly, be in the super bainitic steel of 590MPa level in intensity, still there is the inadequate situation of HAZ toughness.In addition, need corresponding customer need, be not only the mean value of HAZ toughness (pendulum absorption energy), also need further to improve Schwellenwert and make near the tough sexual balance of weld seam good.
In addition, in above-mentioned welded structure, by stress application repeatedly be not minority, therefore, in order to ensure the security of structured material, it is of crucial importance in design that the high-tensile steel that uses as former material has good fatigue characteristic.The fatigue process of steel is divided into following two processes: the progress of the crackle that the generation of the crackle of stress concentration portion and elder generation take place.And in general great machinery parts, the macroscopic crackle is considered to use boundary, does not allow the design of crack progress basically.But, in welded structure, even fatigue cracking takes place also can not cause immediately destroying, this crackle was found by making regular check on etc. before arriving terminal stage, if the part place under repair that this crackle is entered, crackle is grown up arrive final destructive length, even then there is the crackle works can use fully yet.
In welded structure, exist in a large number as the toe of weld portion of stress concentration portion, it is technical near impossible to prevent that fully fatigue cracking from occurring in, and in addition, does not also allow economically.Promptly, for the fatigue lifetime that makes welded structure good, and prevent comparing of crackle, it is effective that the state that has existed from crackle prolongs the crack progress life-span significantly, for this reason, the design of advance rate that can delay the crackle of steel as much as possible is very important.
Technology as the speed that suppresses tired progress also has various motions so far, following technology has for example been proposed: form hard mutually and soft 2 phase constitutions mutually in No. the 2962134th, Japanese Patent, bending, stop, the branch of the crackle by soft phase/hard phase border suppress crack progress speed.
But, in this technology, needing to form the tissue that contains soft ferritic structure basically, existence can not be made the problem of high-tensile steel.
In addition, in No. the 3741078th, Japanese Patent, proposed constituting by bainite structure and/or martensitic stucture, the minimum minor face length of its streaky structure is below the 1.3 μ m and contains under the situation of bainite structure, with long-width ratio contained in the bainite structure is that the area ratio of the island martensite body more than 5 is controlled at and is lower than 5%, makes fatigue craze progression suppress (fatigue craze progression resistivity) good High Strength Steel thus.But, can not guarantee good HAZ toughness.
Summary of the invention
The present invention In view of the foregoing carries out, its purpose is the useful method that following high-tensile steel is provided and is used to make this steel plate, this steel plate is imported large-line energy when welding that heat is 30～100kJ/mm, be not only the mean value of HAZ toughness (pendulum absorption energy), and further improving Schwellenwert, near the tough sexual balance the weld seam is good, and, the advance rate that can suppress crackle is guaranteed good fatigue lifetime.
Can solve the steel plate of the present invention of above-mentioned problem, contain the C:0.02～0.05% (meaning of " quality % ", down with), the adding up to of following, the Cu of following, Mn:0.5～2.0% of Si:0.20%, Al:0.01～0.07%, Cr:0.6～1.5%, Ti:0.010～0.040%, B:0.0010～0.0050%, N:0.0040～0.0080%, Ca:0.0050% and Ni: 0.1～2.4%, surplus is iron and unavoidable impurities, and, the condition of satisfied all following (A)～(D).
[condition (A)]
The BP value that is limited by following formula (1) is in the scope of 90～190 (quality %).
BP value (quality %)=414[C]+78[Si]+31[Mn]+79[Cr]-14[Cu]-26[Ni]+218[Mo] ... (1)
Wherein, [C], [Si], [Mn], [Cr], [Cu], [Ni] and [Mo] represent the content (quality %) of C, Si, Mn, Cr, Cu, Ni and Mo respectively.
[condition (B)]
To contain the every 1mm of Ti nitride below the diameter of equivalent circle 0.05 μ m
2Have 5.0 * 10
6More than individual, wherein, containing Ti nitride number and account for more than 75% in diameter of equivalent circle 0.01～0.03 μ m with respect to all containing Ti nitride number.
[condition (C)]
Contain the every 1mm of Cr carbide in diameter of equivalent circle 0.05～0.3 μ m
2Have 5.0 * 10
3More than individual.
[condition (D)]
The DI that limits by following formula (2) or (3)
1Value or DI
2Value is more than 50.
[Mn＞1.2% o'clock]
DI
1＝1.16×([C]/10)
1/2×(0.75[Si]+1)×{5.1([Mn]-1.2)+5.0}×(0.35[Cu]+1)×(0.36[Ni]+1)×(2.16[Cr]+1)×(3[Mo]+1)×(1.75[V]+1)×(200[B]+1)…(2)
[Mn≤1.2% o'clock]
DI
2＝1.16×([C]/10)
1/2×(0.75[Si]+1)×3.33([Mn]+1)×(0.35[Cu]+1)×(0.36[Ni]+1)×(2.16[Cr]+1)×(3[Mo]+1)×(1.75[V]+1)×(200[B]+1)…(3)
Wherein, [C], [Si], [Mn], [Cu], [Ni], [Cr], [Mo], [V] and [B] represent the content (quality %) of C, Si, Mn, Cu, Ni, Cr, Mo, V and B respectively.
Also have, described " diameter of equivalent circle " is the size that is conceived to contain the Ti nitride and contains the Cr carbide, obtains the imaginary circular diameter that equates with its area, nitride and the carbide confirmed on infiltration type electron microscope (TEM) sightingpiston.In addition, contain the Ti nitride as the what is called of object among the present invention and be meant TiN, also comprise the nitride of a part (about atomic ratio measuring is below 50%) in addition by other nitride shaping element (for example, Nb, Zr, V etc.) displacement Ti.On the other hand, the present invention as the what is called of object contain the Cr carbide be meant with metathetical such as Fe, a part of Mn (Cr, Fe)
3C, (Cr, Fe)
7C
3, (Cr, Fe)
23C
6Deng.Wherein, and basic conduct in normal temperature (Cr, Fe)
3C exists.
In steel plate of the present invention, can also (a) contain below the Mo:0.4% as required, (b) Nb content being suppressed at also is useful below 0.005%, can further improve the characteristic of Plate Steel according to the kind of the element that contains or suppress.
According to steel plate of the present invention, can guarantee yielding stress more than 480MPa, and tensile strength is more than the 590MPa.In addition, high-tensile steel of the present invention is being applicable to that thickness of slab is more than the 50mm, and effect was remarkable when the input heat was the welding of 30～100kJ/mm.
According to the present invention, satisfy the relation of above-mentioned (1)～(3) formula, simultaneously the chemical ingredients of steel plate is formed and be defined in the suitable scope, and, suitably control contains Ti nitride and the dispersion state (size that contains the Cr carbide, number/density), thus: the fine Ti nitride that contains that solid solution does not disappear in steel when large-line energy welds is disperseed in steel, and, the fine Cr carbide that contains of the obstacle that becomes fatigue craze progression is disperseed in steel, and, the size of bainite piece can be guaranteed be suitable size, therefore, the high-tensile steel that can be achieved as follows: can guarantee tough sexual balance well, realize the tough property improvement of welding heat affected zone (HAZ) simultaneously, and, can suppress the advance rate of crackle and guarantee good fatigue lifetime.
0 description of drawings
Fig. 1 is the explanatory view that shows the shape of fatigue craze progression test film.
Fig. 2 shows BP value and HAZ toughness (vE
-20) the graphic representation of relation.
Fig. 3 is the graphic representation of relation that shows the fatigue craze progression speed of the number that contains the Cr carbide of 0.05～0.3 μ m and mother metal.
Embodiment
In intensity is in the super steel plate of 590MPa, forms bainite structure in HAZ, also a lot of to the not clear point of the influence of bainite structure form for alloying element.Present inventors study bainite structure form and alloy designs policy in order to hold the HAZ flexible influence of alloying element for the bainite steel plate.
Consequently, obtain following understanding: turn to below the 10 μ m if the bainite structure of HAZ (piece size) is fine, then can guarantee good HAZ.Then, think that the miniaturization of bainite piece is relevant with the motivating force of bainite structure, and think that the composition design of implementing motivating force is risen gets final product, and the influence of various alloys is studied.
When considering the forming process of bainitic transformation, think the temperature that its phase driving force can produce by the motivating force of bainitic transformation (below, be called " T
0Temperature ") and the temperature that produces of actual bainitic transformation (below, " B be called
sPoint ") the difference explanation.
Therefore, further to alloying element to each temperature (T
0Temperature, B
sPoint) influence is studied.For above-mentioned T
0Temperature can be calculated by calculation of thermodynamics, therefore, uses calculation of thermodynamics software (Thermo-calc can buy from the CRC synthetic study), the influence of each alloying element is studied, and the influence of each alloying element carry out fixed patternization.On the other hand, for B
sPoint in present stage, owing to can not calculate theoretically, therefore uses experimental value.That is, obtain the B of the different steel grade of alloying element by experiment
sPoint is according to the influence of each element of regression analysis fixed pattern.Obtain Liang Shi poor of gained, as (T
0Temperature-B
sPoint) formula thus, is obtained the BP value by following formula (1) regulation.And this BP value is in the scope of 90～190 (quality %) time, and HAZ becomes suitable bainite structure form, reaches good HAZ toughness.
BP value (quality %)=414[C]+78[Si]+31[Mn]+79[Cr]-14[Cu]-26[Ni]+218[Mo] ... (1)
Wherein, [C], [Si], [Mn], [Cr], [Cu], [Ni] and [Mo] represent the content (quality %) of C, Si, Mn, Cr, Cu, Ni and Mo respectively.
Also have, in the element of the above-mentioned BP value of regulation, outside the basal component (C, Si, Mn, Cr, Cu, Ni) of Plate Steel of the present invention, can also contain the element (for example Mo) that contains as required, when not containing this element, calculate BP value as this project not, when containing this element, get final product according to above-mentioned formula (1) calculating BP value.
In addition, though even present inventors make the molten residual Ti nitride (below, be representative with TiN) achieve success on increasing (described spy opens 2005-200716) that contains in high-temperature soldering, but, based on this technology,, carried out research repeatedly in order further to improve HAZ toughness.
When welding, show fine TiN fusion, and the movement (Ostwald's growth) of thick TiN grain growth.Present inventors are conceived to this movement, disperse in a large number in order to make fine TiN as much as possible, even so that the Ti distribution is also fine evenly after grain is grown up, be controlled to be in the every 1mm of TiN below the diameter of equivalent circle 0.05 μ m if find
2Be 5.0 * 10
6Individual above getting final product.
In addition, above-mentioned Ostwald grows up and can promote that the distribution of sizes (deviation) of TiN is big, tissue after the welding is inhomogeneous easily, be conceived to this, in order to suppress this phenomenon as much as possible, draw following understanding, if the ratio that makes TiN shared fine TiN in all gets final product disperseing equably more than a certain amount of.Specifically, account for more than 75% of all TiN numbers if distinguished the fine TiN number that makes in diameter of equivalent circle 0.01～0.03 μ m, then can prevent to weld the back tissue becomes inhomogeneous.
In steel plate of the present invention,, be that main body is disperseed with fine TiN by control described later.Therefore, even contain some thick TiN (for example, in diameter of equivalent circle than the big TiN of 0.05 μ m), this thick TiN substantially can be not influential to the steel plate characteristic yet, and therefore, " all TiN " also comprises this thick TiN.Also have, the fine TiN number of 0.01～0.03 μ m accounts for the ratio (below, be sometimes referred to as " occupation rate ") of all TiN numbers, is preferably more than 77%, more preferably more than 80%.
On the other hand, think in,, then can suppress the progress of crackle if improve the frequency of intracrystalline crackle conflict when crack progress based on bainite single phase structure mutually.Present inventors study the factor that the crackle that becomes intracrystalline is resisted, and its result has distinguished that the miniaturization of above-mentioned bainite piece size is effective to fatigue cracking, and the fine dispersion that contains the Cr carbide is effective.
The relation that satisfies above-mentioned formula (1) for the miniaturization of bainite structure (piece size) gets final product.On the other hand, when the influence that one-tenth is grouped into, manufacture method suppresses the dispersion state that contains the Cr carbide and fatigue craze progression is studied, distinguished and made on C content and the optimized basis of Cr content, stop the temperature optimizing by making cooling after rolling begin temperature, speed of cooling, cooling, the fine bottom bainite of the type of cutting off is generated, and, can make to contain the fine dispersion between bar, in the bar of Cr carbide, can realize that good fatigue craze progression suppresses.Specifically, contain the every 1mm of Cr carbide by making in diameter of equivalent circle 0.05～0.3 μ m
2Have 5.0 * 10
3Individual above (condition of above-mentioned (C)) can be brought into play good fatigue craze progression and suppress.
In thickness of slab is high-tensile steel more than the 50mm, be more than the 590MPa in order to ensure tensile strength, need make the DI that represents by described (2) formula or (3) formula
1Value or DI
2Value is more than 50.This DI
1Value or DI
2Value is the index of hardenability, and this value is lower than at 50 o'clock, can not guarantee that tensile strength is more than the 590MPa.In addition, the upper limit of this value determines separately according to the upper limit (aftermentioned) of each composition.Also have, described (2) formula and (3) formula are obtained according to ASTM A255.
Then, the one-tenth that steel plate of the present invention (mother metal) is described is grouped into.As mentioned above, steel plate of the present invention satisfies above-mentioned (1)～(3) formula even its chemical ingredients is formed, and does not suppress if the content of chemical ingredients separately (element) can not be realized excellent HAZ toughness and fatigue craze progression in suitable scope.Therefore, in the high-tensile steel of the present invention, good and satisfy the relation of above-mentioned (1)～(3) formula except containing the Ti nitride and containing the distribution situation of Cr carbide, the amount of chemical ingredients separately also need be in following suitable scope.The scope qualification of these compositions be the reasons are as follows described.
“C：0.02～0.05％”
C contains the Cr carbide in the intensity of guaranteeing steel plate and generation, makes fatigue craze progression suppress the good indispensable element of.Particularly, in order to bring into play the generation that contains the Cr carbide effectively, need contain more than 0.02% of solid solution limit of bcc (body centered structure).Be preferably more than 0.03%.When C content increases, when welding, cause HAZ toughness deterioration a large amount of generation of HAZ portion island martensite body (MA phase).In addition, it is big that the diffusion frequency of the C in the cooling becomes, and contains thickization of Cr carbide, shows the tendency of fatigue characteristic deterioration, and therefore, C content need be below 0.05%.Be preferably below 0.04%.
" Si:0.20% is following "
Si is guaranteeing element useful on the intensity of steel plate by solution strengthening, but excessive containing sometimes, and MA generates mutually in a large number in HAZ, or causes containing thickization of Ti nitride, the average toughness of HAZ (below, be designated as " HAZ toughness (ave) ") deterioration.From this viewpoint, Si content need preferably be suppressed at below 0.10% for below 0.20%.Also have, from guaranteeing HAZ flexible viewpoint, Si content can be 0%.
“Mn：0.5～2.0％”
Mn guarantees that in the hardenability that improves steel plate intensity, HAZ toughness (ave) go up useful element, in order to bring into play this effect effectively, need contain more than 0.5%.Be preferably more than 0.8%.But, surpassing for 2.0% excessive containing sometimes, the sclerosis of HAZ becomes significantly, HAZ toughness (ave) deterioration, therefore, Mn content is below 2.0%.Be preferably below 1.6%.
“Al：0.01～0.07％”
Al is useful as deoxidant element.In order to bring into play this effect, need contain more than 0.01%, be preferably more than 0.02%.But when Al content was excessive, MA generated HAZ toughness (ave) deterioration mutually in a large number in HAZ, therefore, need be suppressed at below 0.07%, is preferably below 0.04%.
“Cr：0.6～1.5％”
Cr with make described T
0Temperature descends to comparing the Bs point is descended, and is to make HAZ organize the element of performance useful effect in the miniaturization in the motivating force of guaranteeing bainitic transformation.In addition, also performance makes and contains the Cr carbide and make fatigue craze progression suppress good effect.In order to bring into play these effects, Cr need contain more than 0.6%, is preferably more than 0.7%.But when Cr content was excessive, HAZ toughness (ave) is deterioration on the contrary, therefore, need be suppressed at below 1.5%.Be preferably below 1.2%.
“Ti：0.010～0.040％”
Ti and N reaction forms the fine Ti nitride (for example TiN) that contains, and is in thickization of austenite grain (γ grain) that suppresses HAZ, makes useful element on the HAZ toughness stabilization.In order to bring into play this effect effectively, Ti need contain more than 0.010%, is preferably (more preferably more than 0.015%) more than 0.012%.But, when Ti content is excessive, contains thick its number of Ti nitride and reduce, therefore, HAZ flexible deviation increases.Thus, Ti content should be suppressed at below 0.040%.Be preferably (more preferably below 0.030%) below 0.035%.
“B：0.0010～0.0050％”
Molten residual TiN served as that nuclear is separated out the effect that makes HAZ toughness homogenizing as BN when B brought into play with high temperature.In order to bring into play this effect effectively, need contain more than 0.0010%.Be preferably more than 0.0012%.When but B content was excessive, the HAZ sclerosis was remarkable, HAZ toughness (ave) deterioration, therefore, need be below 0.0050%.Be preferably below 0.0040%.
“N：0.0040～0.0080％”
N contains useful element in the even miniaturization of old γ particle diameter that the fine dispersion of Ti nitride makes HAZ making.In order to bring into play this effect, N content need be for more than 0.0040%.Be preferably more than 0.0050%.But when N content was excessive, solid solution N amount increased HAZ toughness (ave) deterioration, and therefore, N need be suppressed at below 0.0080%, is preferably below 0.0070%.
" Ca:0.0050% is following "
Ca has makes the thick effect that the Ti nitride reduces (reducing with the thick nitride of oxide-based inclusion compound crystal) that contains, and is the element that helps the improvement of HAZ toughness (minimum value).This effect increases and increases along with Ca content, preferably contains more than 0.0010%.But when Ca content was excessive, therefore thickization of inclusion HAZ toughness deterioration, need be suppressed at below 0.0050%.Be preferably below 0.0030%.
" total of Cu and Ni: 0.1～2.4% "
Cu and Ni performance make the effect of the tough property improvement of mother metal, are to improving HAZ toughness (ave) effective elements.In order to bring into play this effect, preferably their totals contain more than 0.1%.More preferably more than 0.4%.But when the total content of these elements was excessive, HAZ sclerosis became significantly, and, make the motivating force of the bainitic transformation HAZ toughness deterioration on the contrary that descends.Thus, their total content need be suppressed at below 2.4%, is preferably below 2.2%, more preferably below 2.0%.
That stipulates among the present invention contains element as mentioned above, and surplus is iron and unavoidable impurities, as this unavoidable impurities, allows sneaking into of element (for example P, S, Sn, As, the Pb etc.) that bring into according to the situation of raw material, material, producing apparatus etc.In addition, can also contain or suppress following element energetically and also be effectively, further be improved according to the characteristic of the kind steel plate of the composition that contains or suppress.
" Mo:0.4% is following "
Mo makes described T
0Temperature rises but the Bs point is descended, and is to make HAZ organize the element of useful effect in the miniaturization in the motivating force of guaranteeing bainitic transformation.This effect is along with the increase of Mo content is brought into play effectively.But when Mo content was excessive, HAZ toughness (ave) is deterioration on the contrary, and therefore, preferred Mo is suppressed at below 0.4%.
" Nb:0.005% is following "
Nb has the effect of the motivating force of guaranteeing bainitic transformation, but Nb content has the possibility of thickization of bainite structure when excessive.Thus, preferably suppress Nb content as much as possible, be limited to 0.005% (more preferably below 0.003%) on it.
In the present invention, in order to control the fine dispersion that contains the Ti nitride as described above, recommendation is that mode more than the 20 quality % is adjusted to and is grouped into the X value by following formula (4) regulation, making rolling preceding heat-up time is in 4 hours, and, the speed of cooling that makes when casting to cool off more than 10 ℃/minute, forms steel billet 1500～1300 ℃ temperature range.In addition, for such controlled chilling speed, can exemplify and reduce steel billet thickness, or increase the means of cooling water inflow.These are created conditions describe.
X value (quality %)=500[C]+32[Si]+8[Mn]-9[Nb]+14[Cu]+17[Ni]-5[Cr]-25[M o] ... (4)
Wherein, [C], [Si], [Mn], [Nb], [Cu], [Ni], [Cr] and [Mo] represent the content (quality %) of C, Si, Mn, Nb, Cu, Ni, Cr and Mo respectively.
Also have, same with described (1) formula, be worth in the element at the above-mentioned X of regulation, except that the basal component (C, Si, Mn, Cr, Cu, Ni) of high-tensile steel of the present invention, can also contain the element (for example Nb, Mo etc.) that contains as required, but when not containing this element, calculate the X value as this project not, when containing this element, calculate the X value according to above-mentioned formula (4) and get final product.
Contains the Ti nitride and when the casting of steel ingot, separate out, but its precipitation state is subjected to the influence of alloying element, this be clear and definite (for example, special be willing to 2006-163852 number).The X value of stipulating above-mentioned (2) formula relation is the function about the temperature range in δ territory.The meaning of above-mentioned what is called " δ territory " is the zone of containing δ iron in the phasor of steel.Be somebody's turn to do " zone of containing δ iron " except the zone of δ iron, also comprise the two phase region of δ+γ etc., contain the zone of δ iron and other states.And so-called " temperature range in δ territory " is meant the temperature range that contains δ iron (ceiling temperature in δ territory and lower limit temperature poor).At this, in the steel of specific composition, the situation of the temperature range of the temperature range of δ iron and δ+γ iron for example, the temperature range that adds up to the δ territory of their temperature range.The temperature range in this δ territory is the chemical ingredients of steel plate to be formed be input to the described calculation of thermodynamics software (Thermo-calc can buy from the CRC synthetic study), calculates thus.
In this δ iron, because the velocity of diffusion of Ti is fast, so the temperature range in δ territory is when big, thinks that the time that δ iron exists is elongated, and the thick Ti nitride that contains forms easily.Therefore, contain the miniaturization of Ti nitride and study forming the temperature range of dwindling the δ territory by adjusting chemical ingredients, making.For this reason, by the calculating of Thermo-calc, be one that benchmark only changes the chemical ingredients amount with the special component, thus, investigate of the influence of each chemical ingredients to the temperature range in δ territory.By this research, the temperature range of obtaining with the δ territory has correlationship, the above-mentioned X value of the function representation of being made up of chemical ingredients.
Coefficient in the above-mentioned formula of X value with from the steel of special component, the variable quantity correspondence of the temperature range in the δ territory when making each chemical composition change.Specifically, for example the meaning of the coefficient of [C] [500] is, the C amount was increased 0.01% o'clock, and by the calculating of Thermo-calc, the temperature range in δ territory reduces about 5 ℃.And the temperature range in X value and δ territory has roughly inverse proportional relation (the X value increases, the relation that the temperature range in δ territory reduces).
In view of this consideration, when making steel plate and investigating, distinguished by making the increase of X value, can miniaturization have contained the average particle diameter of Ti nitride, can improve HAZ toughness with various X values.If each chemical ingredients amount is in suitable scope, then the X value is big more, just gets over the average particle diameter that the energy miniaturization contains the Ti nitride, can improve HAZ toughness and base metal tenacity.This X value following is limited to 20 (be preferably 25, more preferably 30).The upper limit of X value is below 128 according to the optimum quantity decision of each chemical ingredients.
On the other hand, heat-up time before rolling is when surpassing 4 hours, thickization that contains the Ti nitride carried out, 0.05 the following number of μ m reduces, in addition, speed of cooling during casting (1500～1300 ℃ temperature ranges) is even be lower than 10 ℃/minute, and thickization of TiN carried out, and the following number of 0.05 μ m reduces.
Also have, be preferably 950～1250 ℃ for the Heating temperature before rolling.When this temperature is lower than 950 ℃, can not fully form austenitic state.In addition, when Heating temperature surpasses 1250 ℃, thickization of austenite grain, the bainite piece size after the phase transformation has the tendency of thickization.
In the present invention, in order to control the fine dispersion that contains the Cr carbide as described above, preferably at Ar
3The above temperature of transformation temperature finishes rolling, from be cooled to the temperature range of 350 ℃～500 ℃ (not comprising 350 ℃) more than the said temperature with the average cooling rate more than 5 ℃/second.
Above-mentioned cooling begins temperature, is being lower than Ar
3During transformation temperature, form the mixed structure of ferrite and bainite, be difficult to guarantee the intensity of stipulating.When the average cooling rate from said temperature was lower than 5 ℃/second, the diffusion of C and Cr took place easily, and containing thickization of Cr carbide can not finely disperse.
Cooling stops temperature below 350 ℃ the time, and MA generates mutually, the toughness deterioration.In addition, MA phase (island martensite body) is owing to be the phase of excessive solid solution C, and therefore, C is obtained mutually by MA, can not fully guarantee to contain the Cr carbide.When cooling stopped temperature above 500 ℃, the diffusion of C and Cr became easily, contains thickization of Cr carbide, can not finely disperse.
In satisfying the high-tensile steel of the present invention of above-mentioned important document, the HAZ tenacity excellent, and, suppress the advance rate of crackle and guarantee good fatigue lifetime, in addition, also can guarantee yielding stress on the intensity: more than the 480MPa, tensile strength: more than the 590MPa.
Also have, the present invention relates to Plate Steel, be meant as the JIS definition at so-called Plate Steel in this field, general thickness is the above steel plate of 3.0mm.But, more than the preferred 50mm of Plate Steel of the present invention, more preferably more than the 60mm.That is, be that the above large-line energy welding of 30～100kJ/mm also shows good HAZ toughness even Plate Steel of the present invention is imported heat, therefore,,, also can efficiently weld by increasing the input heat even thickness of slab is thick.
The Plate Steel of the present invention that so obtains can use as the material of the works of for example bridge and high-rise, boats and ships etc., in little～middle input heat welding, can prevent the toughness deterioration of welding heat affected zone, in the large-line energy welding, also can prevent the toughness deterioration of welding heat affected zone.
Embodiment
Below, illustrating in greater detail the present invention by embodiment, following embodiment does not have and limits character of the present invention, suitably changes in the scope of aim before and after meeting and implements all to be fine, and this all is included in the technical scope of the present invention.
The steel of forming with the chemical ingredients shown in the following table 1 of converter melting (steel grade A～V), by various creating conditions (speed of cooling during casting, rolling before heat-up time, cooling beginning temperature (rolling end temp), speed of cooling (rolling postcooling speed), cooling stop temperature) make steel plate.Also have, in table 1, also show X value [=500[C]+32[Si simultaneously by described (4) formula regulation]+8[Mn]-9[Nb]+14[Cu]+17[Ni]-5[Cr]-25[Mo]] value and the Ar that stipulates by following (5) formula
3Transformation temperature.In addition, in the table 1 "-" expression not have the interpolation element.
Ar
3Transformation temperature (℃)=868-369 * [C]+24.6 * [Si]-68.1 * [Mn]-36.1 * [Ni]-20.7 * [Cu]-24.8 * [Cr] ... (5)
Wherein, [C], [Si], [Mn], [Ni], [Cu] and [Cr] represent the content (quality %) of C, Si, Mn, Ni, Cu and Cr respectively.
In following table 2, show creating conditions of this moment.Also have, " speed of cooling during casting " of table 2 is speed of cooling of the temperature range of 1500～1300 ℃ of controls.The thickness of slab that in following table 2, also shows resulting each steel plate.
Table 2
| Experiment N o. | Steel grade | Speed of cooling during casting (℃/minute) | Heat-up time (hr) before rolling | Thickness of slab (mm) | Cooling beginning temperature (℃) | Speed of cooling (℃/second) | The cooling stop temperature (℃) |
| 1 | A | 12 | 3.0 | 80 | 758 | 5 | 420 |
| 2 | B | 12 | 3.0 | 80 | 792 | 6 | 440 |
| 3 | C | 12 | 3.0 | 80 | 812 | 6 | 405 |
| 4 | D | 12 | 3.0 | 80 | 776 | 5 | 396 |
| 5 | E | 12 | 3.0 | 80 | 767 | 5 | 374 |
| 6 | F | 12 | 3.0 | 50 | 780 | 15 | 390 |
| 7 | G | 12 | 3.0 | 60 | 765 | 9 | 402 |
| 8 | H | 12 | 6.0 | 50 | 761 | 15 | 424 |
| 9 | I | 9 | 3.0 | 50 | 800 | 14 | 496 |
| 10 | J | 12 | 2.0 | 60 | 746 | 10 | 402 |
| 11 | K | 12 | 3.0 | 80 | 815 | 5 | 378 |
| 12 | L | 12 | 3.0 | 50 | 701 | 13 | 389 |
| 13 | M | 12 | 3.0 | 70 | 812 | 7 | 411 |
| 14 | N | 12 | 3.0 | 70 | 792 | 8 | 437 |
| 15 | O | 12 | 3.0 | 50 | 878 | 13 | 403 |
| 16 | P | 12 | 3.0 | 60 | 806 | 10 | 368 |
| 17 | Q | 12 | 3.0 | 80 | 807 | 6 | 389 |
| 18 | R | 12 | 3.0 | 70 | 804 | 9 | 359 |
| 19 | S | 12 | 3.0 | 50 | 807 | 12 | 431 |
| 20 | T | 10 | 3.0 | 75 | 746 | 7 | 426 |
| 21 | U | 12 | 3.0 | 80 | 751 | 5 | 374 |
| 22 | V | 12 | 3.0 | 50 | 776 | (0.3 putting cold) | - |
| 23 | V | 12 | 3.0 | 80 | 776 | 5 | 280 |
| 24 | V | 12 | 3.0 | 80 | 776 | 5 | 529 |
| 25 | V | 12 | 3.0 | 80 | 666 | 5 | 401 |
For as each test board of above-mentioned manufacturing in following main points measure the individual number density that contains the Ti nitride (in the number that contains the Ti nitride below the diameter of equivalent circle 0.05 μ m and in the occupation rate that contains the Ti nitride of diameter of equivalent circle 0.01～0.03 μ m), contain the individual number density (with the number that contains the Cr carbide of diameter of equivalent circle 0.05～0.3 μ m) of Cr carbide, the yielding stress YSS of steel plate (wherein, measures 0.2% yield-point (σ
0.2)), tensile strength TS, HAZ toughness (mean value (ave), Schwellenwert (min)), crack progress speed (fatigue craze progression speed trial).These results are displayed in Table 3 together.
" mensuration that contains the individual number density of Ti nitride "
T (thickness of slab)/4 part of each steel plate is observed with the condition of 60,000 times observation multiplying power, field of view 2 * 2 (μ m), 5 positions, observation place by infiltration type electron microscope (TEM) and (to observe boundary: 0.010 μ m).And, measure the area that respectively contains the Ti nitride in this visual field by image analysis, calculate the diameter of equivalent circle of each nitride according to this area.Whether also have, differentiating by EDX (energy dispersion type X-ray detector) is to contain the Ti nitride.
With diameter of equivalent circle is that the number that contains the Ti nitride below the 0.05 μ m is converted into every 1mm
2Obtain, and that calculates diameter of equivalent circle and be 0.01～0.03 μ m fine contains the Ti nitride with respect to all the contain the Ti nitride individual percentage (occupation rate: %) of (also comprise diameter of equivalent circle meter surpass 0.05 μ m contain the Ti nitride).
" mensuration that contains the individual number density of Cr carbide "
T (thickness of slab)/4 part of each steel plate is observed with the condition of 40,000 times observation multiplying power, field of view 2 * 2 (μ m), 5 positions, observation place by infiltration type electron microscope (TEM).And, measure the area that respectively contains the Cr carbide in this visual field by image analysis, calculate the diameter of equivalent circle of each carbide according to this area.Whether also have, differentiating by EDX (energy dispersion type X-ray detector) is to contain the Cr carbide.And, be that the number that contains the Cr carbide of 0.05～0.3 μ m is converted into every 1mm with diameter of equivalent circle
2Obtain.
" tension test "
Take No. 4 test films of JISZ2201 from t (thickness of slab)/4 part of each steel plate in the direction rectangular, carry out tension test, measure yielding stress YS (0.2% yield-point: σ with the main points of JISZ2241 with respect to rolling direction
0.2), tensile strength TS.And TS is more than the 590MPa, YS be 460MPa above be evaluated as qualified.
" evaluation of HAZ flexible "
Take No. 4 test films of JISZ2201 from t (thickness of slab)/4 part of each steel plate in the direction rectangular, implement one large-line energy welding of input heat: 80kJ/mm by electroslag welding with respect to rolling direction.And the HAZ portion for distance weld seam (molten thread) 0.5mm carries out-20 ℃ pendulum impact test, measures to absorb energy (vE
-20).At this moment, 5 test films are measured absorption energy (vE
-20), obtain mean value (ave) and minimum value (min).And, vE
-20Mean value (ave) for 150J above be evaluated as tenacity excellent, vE
-20Minimum value (min) improve for the above stabilization that is evaluated as of 100J.
" fatigue craze progression speed trial "
Take thickness from t (thickness of slab)/4 part of each steel plate: the compact type test film of 12.5mm (CT test film).Fig. 1 shows the shape of resulting CT test film this moment.In addition, for taking of the test film of HAZ portion, (13mm * 65mm * 65mm) is after the heating in 1400 ℃ * 50 seconds to take steel ingot from each steel plate, after being equivalent to import the thermal cycling test of heat: 80kJ/mm (800～500 ℃ with cooling in 700 seconds), be processed into above-mentioned CT test film.Using these CT test films, is benchmark with ASTME647, implements the fatigue craze progression test, thus, obtains fatigue craze progression speed.The test conditions of this moment, as follows.
Test method: make the electricity consumption oil pressure department style of dress ± 10 tons of protracted test machines, the mensuration of crack length is tried to achieve by computer-controlled flexibility (コ Application プ ラ イ ア Application ス) method.The meaning of so-called flexibility method is the ratio (δ/P) automatically measure crack length according to this flexibility of crackle shedding deformation δ and load p.
Testing circumstance: room temperature, atmosphere
Control method: loading control, control waveform: sine wave
Stress ratio: R=0.1
Trial speed: 600～1200cpm
The imagination crackle takes place and HAZ, mother metal progress from toe of weld, estimates by the value of the Δ K=30 (MPa √ m) in middle Δ K zone for mother metal, estimates by the value of the Δ K=10 (MPa √ m) in little Δ K zone for HAZ portion.Also have, the stabilized growth zone of setting up for by PARIS (the パ リ ス) rule of following (6) formula regulation is distinguished in the Δ K zone of these tests.
da/dn＝C(ΔK)
m…(6)
Wherein, a: be full of cracks length, n: the number of occurrence, C, m: the constant of the conditional decision of material, loading etc., Δ K: stress sampling factor scope.
Also have, the metewand of fatigue craze progression speed is 15～30 * 10 for mother metal owing to common steel
-5So advance rate about mm/cycle (during Δ K=30) is 12.0 * 10
-5Mm/cycle is following to be qualified, is 0.4～0.8 * 10 for HAZ portion owing to common steel
-5Mm/cycle (during Δ K=10)
Can carry out following investigation (also have, following No. represents table 2,3 experiment No.) from these results.The example (example of the present invention) of the important document of the present invention regulation, chemical ingredients composition, BP value, DI are satisfied in No.1～7th
1Or DI
2Value, X value and contain the Ti nitride and contain the fine dispersion of Cr carbide suitable, the good fatigue craze progression of toughness that can access welding heat affected zone suppresses also good steel plate.
With respect to this, No.8～25th, the example (comparative example) outside the important document of the present invention's regulation, any characteristic inequality.As described below in detail.
No.8,9 is used to make and contains the fine dispersive of Ti nitride and create conditions and depart from felicity condition, contains thickization of Ti nitride, and the number density fully and the occupation rate that contain the Ti nitride are not reached HAZ toughness (ave, min) deterioration.
C content in the No.10 steel plate and Si content have exceeded the scope of the present invention's regulation, contain the thickization generation of Cr carbide, and the crack progress of mother metal speeds up.
Si content in the No.11 steel plate exceeds the scope of the present invention regulation, and the form that contains the Ti nitride bad (fail to obtain fine contain Ti nitride) can not obtain good HAZ toughness.In addition, the crack progress speed of HAZ portion also accelerates.
Mn content in the No.12 steel plate exceeds the scope of the present invention's regulation, even it is good with the form that contains the Cr carbide to contain the Ti nitride, but HAZ toughness deterioration.
The scope (the BP value also departs from) of the discontented unabridged version invention of the Cr content in No.13 steel plate regulation, the fine dispersion that contains the Cr carbide is not reached, HAZ toughness deterioration, and the crack progress of mother metal and HAZ suppresses equal deterioration.In addition, because DI
1Or DI
2Value does not satisfy specialized range, and therefore, strength of parent descends.Cr content in the No.14 steel plate exceeds the scope (the BP value also departs from) of the present invention's regulation, HAZ toughness deterioration, and the crack progress of mother metal and HAZ suppresses equal deterioration.
All do not contain Cu and Ni in the No.15 steel plate, Mo content surpasses the scope (the BP value also departs from) of the present invention's regulation in addition, the form that contains the Ti nitride bad (fail to obtain fine contain Ti nitride), HAZ toughness deterioration, and the crack progress of mother metal and HAZ suppresses equal deterioration.In addition, because DI
1Or DI
2Value does not satisfy specialized range, and therefore, strength of parent descends.
Ti content in the No.16 steel plate exceeds the scope of the present invention regulation, the form that contains the Ti nitride bad (fail to obtain fine contain Ti nitride), HAZ toughness deterioration.
B in No.17～19 steel plates and N content outside the scope of the present invention regulation, HAZ toughness deterioration.In addition, Al in the No.20 steel plate and Cu content are excessive, and, the specialized range (the BP value also departs from) of the discontented unabridged version invention of Cr content, a fine sufficient occupation rate that contains the Ti nitride and a fine number density fully that contains the Cr carbide are not reached, and HAZ toughness and crack progress suppress equal deterioration.
Ni content in the No.21 steel plate is excessive, and, the specialized range (the BP value also departs from) of the discontented unabridged version invention of Cr content, nor contain Cu, a fine number density fully that contains the Cr carbide is not reached, and HAZ toughness and crack progress suppress equal deterioration.
No.22～25 are used to make and contain the fine dispersive of Cr carbide and create conditions outside suitable scope, contain thickization of Cr carbide, and a number density fully that contains the Cr carbide is not reached any deterioration at least that strength of parent and crack progress suppress.
Based on these results as can be known, in Fig. 2, show BP value and HAZ toughness ((vE
-20) relation, suitably adjust the BP value make HAZ toughness good on effectively.In addition, in Fig. 3, show the relation of the fatigue craze progression speed of the number that contains the Cr carbide of 0.05～0.3 μ m and mother metal, reach contain the Cr carbide fine and be dispersed in the inhibition of the crack progress of realizing mother metal useful.
Claims (5)
1, a kind of steel plate, it is characterized in that, in quality % contain C:0.02～0.05%, below the Si:0.20%, Mn:0.5～2.0%, Al:0.01～0.07%, Cr:0.6～1.5%, Ti:0.010～0.040%, B:0.0010～0.0050%, N:0.0040～0.0080%, below the Ca:0.0050%, Cu and Ni add up to: 0.1～2.4%, surplus is iron and unavoidable impurities, and, satisfy the condition of whole following (A)～(D)
[(A) condition]
By the BP value of following formula (1) regulation scope at 90～190 (quality %),
BP value (quality %)=414[C]+78[Si]+31[Mn]+79[Cr]-14[Cu]-26[Ni]+218[Mo] ... (1)
Wherein, [C], [Si], [Mn], [Cr], [Cu], [Ni] and [Mo] represent the mass percentage content of C, Si, Mn, Cr, Cu, Ni and Mo respectively,
[(B) condition]
Count with diameter of equivalent circle and to contain the every 1mm of Ti nitride below the 0.05 μ m
2Have 5.0 * 10
6More than individual, wherein, the number that contains the Ti nitride of counting 0.01～0.03 μ m with diameter of equivalent circle accounts for more than 75% with respect to the number that all contains T i nitride,
[(C) condition]
Contain the every 1mm of Cr carbide with what diameter of equivalent circle was counted 0.05～0.3 μ m
2Have 5.0 * 10
3More than individual,
[(D) condition]
DI by following formula (2) or (3) regulation
1Value or DI
2Value is more than 50,
[Mn＞1.2% o'clock]
DI
1＝1.16×([C]/10)
1/2×(0.75[Si]+1)×{5.1([Mn]-1.2)+5.0}×(0.35[Cu]+1)×(0.36[Ni]+1)×(2.16[Cr]+1)×(3[Mo]+1)×(1.75[V]+1)×(200[B]+1)…(2)
[Mn≤1.2% o'clock]
DI
2＝1.16×([C]/10)
1/2×(0.75[Si]+1)×3.33([Mn]+1)×(0.35[Cu]+1)×(0.36[Ni]+1)×(2.16[Cr]+1)×(3[Mo]+1)×(1.75[V]+1)×(200[B]+1)…(3)
Wherein, [C], [Si], [Mn], [Cu], [Ni], [Cr], [Mo], [V] and [B] represent the mass percentage content of C, Si, Mn, Cu, Ni, Cr, Mo, V and B respectively.
2, steel plate according to claim 1 is characterized in that, % also contains below the Mo:0.4% in quality.
3, steel plate according to claim 1 is characterized in that, in quality % Nb content is suppressed at below 0.005%.
4, steel plate according to claim 1 is characterized in that, yielding stress is more than the 480MPa, and tensile strength is more than the 590MPa.
5, steel plate according to claim 1 is characterized in that, thickness of slab is more than the 50mm.
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| JP6064896B2 (en) * | 2013-12-27 | 2017-01-25 | Ｊｆｅスチール株式会社 | Steel material with excellent fatigue crack propagation characteristics, method for producing the same, and method for determining steel materials with excellent fatigue crack propagation characteristics |
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