CN104937125A - Hot-rolled steel plate for high-strength line pipe - Google Patents
Hot-rolled steel plate for high-strength line pipe Download PDFInfo
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- CN104937125A CN104937125A CN201480005063.4A CN201480005063A CN104937125A CN 104937125 A CN104937125 A CN 104937125A CN 201480005063 A CN201480005063 A CN 201480005063A CN 104937125 A CN104937125 A CN 104937125A
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Abstract
Provided is a seam-welded pipe for a high-strength line pipe having superior HIC resistance. A hot-rolled steel plate for a high-strength line pipe is characterized by: having an elemental composition by mass% of 0.02-0.06% of C, 0.05-0.25% of Si, 0.60-1.10% of Mn, no greater than 0.008% of P, no greater than 0.0010% of S, 0.010-0.060% of Nb, 0.001-0.020% of Ti, no greater than 0.05% of Mo, 0.05-0.50% of Cr, 0.01-0.08% of Al, 0.0005-0.0050% of Ca, and no greater than 0.005% of O, and furthermore at least one selected from among no greater than 0.50% of Cu, no greater than 0.50% of Ni, and no greater than 0.10% of V, the remainder comprising Fe and unavoidable impurities; satisfying formula (1); the metal structure being bainitic ferrite; and the ratio of the hardness of a center segregated section and a non-segregated section being less than 1.20. Formula (1): SP<=1.90, where SP is determined from SP=Mn+Mo+11.3C+0.29(Cu+Ni)+0.60Cr+0.88V, the chemical symbols in the formula signifying the mass% of the respective elements.
Description
Technical field
The present invention relates to hot-rolled steel sheet and manufacture method thereof, described hot-rolled steel sheet has hydrogen-induced cracking resistance (hydrogen induced cracking resistance) (hereinafter referred to as hic resistance), and there is the intensity of API (American Petroleum Institute) standard x more than 52, the pipeline steel tube electricity consumption seam steel pipe starting material be suitable as the Energy resources of conveying crude oil or Sweet natural gas and so on use.
Background technology
In the past, from the viewpoint of transport efficiency, pipeline steel tube mainly uses and can manufacture major diameter and the UOE steel pipe of the steel pipe of heavy wall, recently, replace UOE steel pipe, popularize gradually with high strength electricity seam steel pipe (highstrength electric resistance welded steel pipe) that the hot-rolled steel sheet (hot rolled strip) of the high and more cheap roll-shape of productivity is material.Except cost aspect, electricity seam steel pipe also has the following advantages, that is, wall thickness deviation and circularity excellence compared with UOE steel pipe.On the other hand, the feature of the tubing method (pipe production method) of electricity seam steel pipe is, be cold rolling shaping (cold roll forming), the plastix strain (plastic strain) of giving when manufacturing steel pipe is especially large compared with UOE steel pipe.
In recent years crude oil and the increase of the construction of natural gas fields along with energy requirement and the progress of extraction technique, oil field and gas field be polar region, high depth gradually.For the pipeline steel tube used in such place, except desired strength, toughness and weldability, also require the so-called acid-resistant property (sour resistance) of hic resistance, resisting sulfide stress corrosion crack (sulfate stress corrosion cracking resistance) (SSC) and so on.For the pipeline steel tube of not load stress after laying, hic resistance is even more important.
HIC is that the hydrogen ion generated by corrosion reaction becomes hydrogen atom on steel surface and invades in steel, gather around the thick carbide of inclusion, the NbC etc. such as MnS or hard second phase (second hardphase) thus pressure in producing, finally make the phenomenon that steel crack.In addition, when giving plastix strain to steel, import a large amount of dislocations (dislocation) at above-mentioned inclusion, carbide and hard second phase periphery, thus hydrogen atom is more easily gathered, therefore encouraged HIC.
In order to solve the problem of above-mentioned HIC, propose various solve scheme all the time.
In patent documentation 1, disclose a kind of form the content of the element of inclusion by making to be combined with S, O (oxygen) and N respectively add up to less than 0.01%, or the maximum diameter of inclusion is controlled below 5 μm, by innoxious for the inclusion of the starting point becoming HIC, again the hardness of center segregation portion (center segregation part) is set to below Hv330, thus improves the method for resistance to HIC.
In patent documentation 2, disclose a kind of size by reducing to become the TiN of the starting point of HIC, thus reduce the method for HIC area occupation ratio (area ratio of HIC).Specifically, by adjusting the addition of Al and Ca, and CaO/Al is made
2o
3weight ratio be 1.2 ~ 1.5, thus by the Al-Ca system sulfide miniaturization in molten steel, and to make with this sulfide be caryogenic Al-Ti-Ca system complex inclusion is less than 30 μm.
In addition, the Nb concentration that Patent Document 3 discloses a kind of region by making the distance being arranged in 5% of thickness of slab from the central part in thickness of slab direction towards thickness of slab direction is less than 0.060%, and by Ti control of the concentration below 0.025%, thus not easily become the method for the carbonitride of Nb and Ti of HIC starting point.
Patent Document 4 discloses a kind of Mn by adding in minimizing steel measure and reduce center segregation, thus improve hic resistance, effectively use Cr and Mo that center segregation is more difficult, manufacture the method for the high-strength line-pipe steel pipe of hic resistance excellence thus.
Prior art document
Patent documentation
Patent documentation 1: Japanese Unexamined Patent Publication 2006-63351 publication
Patent documentation 2: Japanese Patent No. 4363403 publication (International Publication WO2005/075694 publication)
Patent documentation 3: Japanese Unexamined Patent Publication 2011-63840 publication
Patent documentation 4: Japanese Patent No. 2647302 publication (Japanese Unexamined Patent Publication 5-271766 publication)
Summary of the invention
But in the technology recorded in patent documentation 1, the hardness in center segregation portion is still very high, and the inclusion namely allowed to becoming starting point is innoxious, also has the problem that cannot ensure sufficient hic resistance to the electric slit-tube giving large plasticity time shaping.
In addition, in the technology recorded in patent documentation 2 and patent documentation 3, concrete countermeasure is not taked to the hardness in segregation portion of control center, there is the inclusion namely allowed to becoming starting point innoxious, for electric slit-tube, still producing the problem of large HIC yet.
And, in the technology recorded in patent documentation 4, by excessive interpolation Cr and Mo, thus encourage the generation of the hard second phase such as martensite, the hardness in center segregation portion increases, so for the electric slit-tube imparting large plasticity when shaping, there is the problem that must reduce the hardness in center segregation portion further.
The present invention carries out in view of above-mentioned problem, its object is to provide a kind of high-strength line-pipe steel of hic resistance excellence effective electricity seam steel pipe, be applicable to electric slit-tube pipeline steel tube, be subject to the crack length ratio (hereinafter referred to as CLR)=less than 15% of the HIC after the plastix strain of such as 10%.
Here hic resistance excellence refers to, in NACE solution (NACE TM-0284 solution A: 5%NaCl+0.5%CH
3oOH, 1 saturated H of normal atmosphere
2s, pH=3.0 ~ 4.0) in dipping 96hr after crack length ratio (CLR) be less than 15%.
The present invention invents based on following opinion, namely, in order to reduce the hardness in center segregation portion and obtain desired intensity, the opinion that the relation for the hardness in center segregation portion and steel composition, organizational composition and HIC achievement and manufacturing condition is carried out great many of experiments and obtained.
First, the relation of the HIC achievement of product and the hardness in center segregation portion is investigated.Its result, makes if known the Vickers' hardness in center segregation portion be below HV230, then can realize crack length ratio (CLR)≤15%.This itself, namely in order to improve the hardness in hic resistance and segregation portion of control center as recording in patent documentation 1, be all the time well-known.
But, carry out the data gathering of product further, the maximum hardness in center segregation portion is suppressed when below Hv230 even if result is known, also have the situation of CLR > 15%, consider this reason of investigation from the homogeneous viewpoint of material.The hardness ratio (Vickers' hardness in the Vickers' hardness/non-segregation portion in center segregation portion) in the portion of center segregation shown in Fig. 1 and non-segregation portion and the relation of crack length ratio (CLR).If can distinguish thus, hardness ratio be less than 1.20, CLR is less than 15%.
When thising is presumably because that the Hardness Distribution in thickness of slab direction is uneven, if be subject to large plastix strain, then strain concentrating between the high position of the hardness of center segregation and the not high position of hardness, there just becomes the trap point (trap site) of hydrogen atom.
Then, composition hardness ratio for realizing center segregation portion and non-segregation portion being less than to the steel of 1.20 is studied, and calculates and in carbon equivalent formula (CEQ=C+Mn/6+ (Cr+Mo+V)/5+ (Cu+Ni)/15), enrolls the segregation coefficient (segregationcoefficient) in the continuous casting steel billet of each composition calculated by computer simulation (computationsimulation) alone and the SP value (=Mn+Mo+11.3C+0.29 × (Cu+Ni)+0.60Cr+0.88V) obtained.The hardness ratio in the portion of center segregation shown in Fig. 2 and non-segregation portion and the relation of SP value.Its result, can distinguish to make the hardness ratio in center segregation portion and non-segregation portion be less than 1.20, needs to make SP value be less than 1.90.
The present invention is based on above-mentioned opinion to study further and form, purport of the present invention is as follows.
[1] a kind of effective hot-rolled steel sheet of high-strength line-pipe steel of hic resistance excellence, it is characterized in that, become to be grouped in mass %, containing C:0.02 ~ 0.06%, Si:0.05 ~ 0.25%, Mn:0.60 ~ 1.10%, below P:0.008%, below S:0.0010%, Nb:0.010 ~ 0.060%, Ti:0.001 ~ 0.020%, below Mo:0.05%, Cr:0.05 ~ 0.50%, Al:0.01 ~ 0.08%, Ca:0.0005 ~ 0.0050%, below O:0.005%, further containing being selected from below Cu:0.50%, below Ni:0.50%, more than a kind in below V:0.10%, remainder is made up of Fe and inevitable impurity, meet following formula (1), metal structure is bainite ferrite, the hardness in center segregation portion is less than 1.20 with the ratio of the hardness in non-segregation portion.
SP≤1.90 ……(1)
Wherein, SP is obtained by SP=Mn+Mo+11.3 × C+0.29 × (Cu+Ni)+0.60 × Cr+0.88 × V, and the symbol of element in formula represents the quality % of each element.
[2] according to the effective hot-rolled steel sheet of high-strength line-pipe steel of the hic resistance excellence recorded in above-mentioned [1], it is characterized in that, except mentioned component composition, also meet following formula (2).
1.2≤EC≤4.0 ……(2)
Here, EC is expressed as EC=[Ca] eff/ (1.25 × S), and [Ca] eff is obtained by Ca-(0.18+130 × Ca) × O.Should illustrate, the symbol of element Ca, S, O in formula represent the quality % of each element.
[3] according to the effective hot-rolled steel sheet of high-strength line-pipe steel of the hic resistance excellence recorded in above-mentioned [1] or [2], it is characterized in that, except mentioned component composition, the hardness in center segregation portion is less than 1.20 with the ratio of the hardness in non-segregation portion.
[4] a kind of manufacture method of the effective hot-rolled steel sheet of high-strength line-pipe steel of hic resistance excellence, it is characterized in that, the temperature of heating steel billet to 1100 that one-tenth of recording in above-mentioned [1] or [2] is grouped into DEG C ~ 1300 DEG C will be had, carry out roughing, then the mode being more than 20% with the accumulation draft of less than 930 DEG C (cumulative rolling reduction ratio) carries out finish rolling, afterwards, accelerating cooling (accelerated cooling) is carried out until 380 ~ 600 DEG C with the average cooling rate of 5 ~ 100 DEG C/s at thickness of slab center, thereafter wound into a roll.
According to the present invention, by the hardness making steel form optimization and segregation portion of strict control center, thus the hic resistance improved after the electricity seam steel pipe forming giving large plastix strain when shaping, can be manufactured under the severe rugged environment suitable with NACE solution and also the electricity of no problem use can to stitch steel pipe pipeline steel tube hot-rolled steel sheet.In addition, the hot-rolled steel sheet manufactured by the present invention also can be used for Spiral Steel Pipe pipeline steel tube (spiral steel pipe for linepipe).
Accompanying drawing explanation
Fig. 1 represents the hardness in hardness/non-segregation portion in center segregation portion and the figure of the relation of crack length ratio (CLR).
Fig. 2 is the figure of the relation of the hardness in the hardness/non-segregation portion representing SP value and center segregation portion.
Fig. 3 is the figure located representing the hardness in center segregation portion and the hardness in non-segregation portion.
Embodiment
Below the restriction reason of each constitutive requirements of the present invention is described.
1. be grouped into about one-tenth
First, the reason that the one-tenth defining steel of the present invention is grouped into is described.Should illustrate, composition % all represents quality %.
C：0.02～0.06％
C is the element of the high strength going far towards steel, containing more than 0.02% time play its effect, but the content more than 0.06%, then easily generate the second-phase as pearlitic structure, hic resistance is deteriorated.Therefore, C amount is set to the scope of 0.02 ~ 0.06%.Be preferably the scope of 0.03 ~ 0.05%.
Si：0.05～0.25％
Si is the element added in order to the amount of scaling (scale-off quantity) when solution strengthening and reduction hot rolling, containing more than 0.05% time play its effect, if but more than 0.25%, red scale (red scale) hypertrophy, and the inhomogeneous cooling (coolingununiformity) when producing hot rolling, the homogeneity (uniformity) of outward appearance and material is deteriorated.Therefore, Si amount is set to the scope of 0.05 ~ 0.25%.Be more preferably 0.10 ~ 0.25%.In addition, Si forms the oxide compound of MnSi system and makes electric seam welding connect toughness (toughness) variation in portion when electric seam welding connects, therefore preferred to make Mn/Si contain than the mode being 4.0 ~ 12.
Mn：0.60～1.10％
Mn is the element being contributed to intensity, toughness by the miniaturization of structure of steel, containing more than 0.60% time play its effect.On the other hand, the increase of Mn content encourages and forms fine martensitic stucture in center segregation portion, also encourages the generation becoming the MnS of the starting point of HIC, therefore needs its content to suppress below 1.10%.Therefore, Mn amount is set to the scope of 0.60 ~ 1.10%.Be preferably the scope of 0.75 ~ 1.05%.
Below P:0.008%
P is inevitable impurity element, and owing to making the hardness in center segregation portion significantly rise, hic resistance is deteriorated, and therefore preferably its content is low as far as possible, can allow to reach 0.008%.Further, in order to make P extremely low, and along with the cost increase that long-timeization because of refining time (refining time) causes, therefore more than 0.002% is preferably.
Below S:0.0010%
S and P is the element inevitably contained in steel equally, in steel, generate MnS, and therefore preferably its content is low as far as possible, can allow to reach 0.0010%.Be more preferably less than 0.0006%.
Nb：0.010～0.060％
Nb be manufacture hot-rolled steel sheet time rolling step (coiling process) in the fine precipitation of the form of Nb carbonitride and contribute to steel intensity improve element.In addition, be suppress the growth of austenite crystal when electric seam welding connects, contribute to the element of the raising of the toughness of weld part.Containing more than 0.010% time play its effect.On the other hand, if more than 0.060%, then easily become the thick Nb carbonitride of the starting point of HIC.Therefore, Nb amount is set to the scope of 0.010 ~ 0.060%.Be preferably the scope of 0.030 ~ 0.060%.
Ti：0.001～0.020％
Ti be in order to the N that the toughness of steel is significantly deteriorated is fixed as TiN thus innoxious and add element.Its effect is played when content is more than 0.001%.On the other hand, if more than 0.020%, then the amount of the Ti carbonitride of separating out along the cleavage surface of Fe increases, and makes the degraded toughness of steel.Therefore, Ti amount is set to the scope of 0.001 ~ 0.020%.Be preferably the scope of 0.005 ~ 0.015%.
Below Mo:0.05%
Mo improves hardening capacity and improves extremely effective element to the toughness of steel and intensity, but owing to forming martensitic stucture to center segregation portion's denseization, therefore hic resistance is deteriorated.Therefore, the content of Mo is preferably low as far as possible, can allow to reach 0.05%.
Be more preferably less than 0.01%.
Cr：0.05～0.50％
Cr improves the element that hardening capacity, the toughness contributing to steel and intensity improves, and plays effect, if add more than 0.50%, then form Cr oxide compound when electric seam welding connects and the toughness of weld part is significantly deteriorated during the addition of more than 0.05%.In order to suppress to form Cr oxide compound, Cr is measured be the scope of 0.05 ~ 0.50%.Be preferably the scope of 0.05 ~ 0.30%.
Al：0.01～0.08％
Al adds as reductor, if but be less than 0.01%, deoxidation is insufficient, and on the other hand, if more than 0.08%, then the thick Al system oxide amount remained in steel increases, hic resistance and degraded toughness.Therefore, Al amount is set to the scope of 0.01 ~ 0.08%.Be preferably the scope of 0.01 ~ 0.05%.
Ca：0.0005～0.0050％
Ca improves effective element by the morphology Control of sulfide-based inclusion to hic resistance, containing more than 0.0005% time play its effect.On the other hand, if more than 0.0050%, then not only effect is saturated, and also a large amount of oxide compound forming Ca, makes hic resistance be deteriorated.Therefore, Ca amount is set to the scope of 0.0005 ~ 0.0050%.Be preferably the scope of 0.0010 ~ 0.0030%.
Below O:0.005%
Oxygen, owing to making various oxide compound, makes hot workability, erosion resistance, toughness, hic resistance reduce, preferably reduces as much as possible, can allow to reach 0.005%.Be more preferably less than 0.0035%.
In the present invention, can in following scope further containing more than a kind in Cu, Ni, V.
Below Cu:0.50%
Cu contributes to the toughness of steel and the element of intensity raising by improving hardening capacity, denseization compared to center segregation portion with Mn with Mo with same effect is few, does not therefore make hic resistance be deteriorated and can strengthen steel, therefore can add according to strength grade.Containing more than 0.05% time play its effect, if more than 0.50%, its effect is saturated, above then causes extra cost increase containing it.Therefore, Cu amount is set to less than 0.50%.Be preferably less than 0.40%.
Below Ni:0.50%
Ni and Cu contributes to the toughness of steel and the element of intensity raising by improving hardening capacity, denseization compared to center segregation portion with Mn with Mo with same effect is few, therefore hic resistance is not made to be deteriorated and steel can be strengthened, so can add according to strength grade.Containing more than 0.05% time play its effect, but content is saturated more than 0.50% its effect, can cause extra cost increase above containing it.Therefore, Ni amount is set to less than 0.50%.Be preferably less than 0.40%.
Below V:0.10%
V is the element that the intensity being contributed to steel by solution strengthening (solute strengthening) and precipitation strength (precipitationstrengthening) when containing more than 0.005% is improved, but increase more than the hardness in 0.10% center segregation portion, hic resistance is deteriorated.Therefore, V amount is set to less than 0.10%.Be preferably less than 0.080%.
Below SP:1.90
In the present invention, the SP value of being tried to achieve by the content of each alloying element is made to meet following formula (1).
SP≤1.90 ……(1)
Wherein, SP is obtained by SP=Mn+Mo+11.3 × C+0.29 × (Cu+Ni)+0.60 × Cr+0.88 × V, and the symbol of element in formula represents the quality % of each element.In addition, the element do not added is set to 0.
SP value is can infer from the content of each alloying element the formula that the patten's design of the hardness in the center segregation portion of the hot-rolled steel sheet of the material becoming electricity seam steel pipe goes out, if SP value is more than 1.90, denseization then to the center segregation portion of each element becomes significantly, and the hardness in center segregation portion and the ratio of the hardness in non-segregation portion are satisfied is less than 1.20.In addition, SP value is lower, and the hardness in center segregation portion and the ratio of the hardness in non-segregation portion, also along with diminishing, so in order to make such as below CLR:5%, and when requiring higher hic resistance, must make the upper limit of SP value be 1.75.
EC：1.2～4.0
In the present invention, and then add the innoxious of the sulfide-based inclusion caused in order to more effectively carry out by Ca, preferred following shown EC value meets following formula (2).
1.2≤EC≤4.0 ……(2)
Here, EC is expressed as EC=[Ca] eff/ (1.25 × S).Wherein,
[Ca] eff is obtained by Ca-(0.18+130 × Ca) × O, and the symbol of element Ca, S, O in formula represent the quality % of each element.
Whether EC value represents the form controlling sulfide-based inclusion and the Ca added amount fully to add to and form the value of CaS, if EC value is less than 1.2, then Ca is not enough state, becomes the MnS of the starting point of HIC.On the other hand, if EC value is more than 4.0, then Ca system oxide compound generates in a large number, and the degree of cleaning of steel reduce and hic resistance is deteriorated.Therefore, preferably make EC value be 1.2 ~ 4.0 scope.Be more preferably the scope of 1.4 ~ 0.36.
Should illustrate, the remainder beyond above-mentioned element is made up of Fe and inevitable impurity.But, as long as do not hinder action effect of the present invention, do not limit containing other trace element.
2. about metal structure
Next, the metal structure of steel of the present invention is described.
In order to the intensity that gets both is the high strength of more than API X52 (YS: more than 380MPa) and the MIN toughness needed when can be used for pipeline steel tube (ductile brittle transition temperature in Charpy test is less than-60 DEG C), metal structure is necessary for bainite ferrite tissue.If organize phase owing to there is the different sorts such as ferrite or fine martensite, perlite and residual austenite in bainite ferrite tissue, then cause yield strength reduction, degraded toughness, hic resistance is deteriorated, and the tissue beyond bainite ferrite tissue divides rate more few better.But when the Line Integral rate beyond bainite ferrite tissue is extremely low, its impact is little of ignoring, and can allow the amount acquired a certain degree.Specifically, the structure of steel (ferrite, fine martensite, perlite, residual austenite etc.) beyond bainite ferrite tissue if total be less than 3%, then it can be considered bainite ferrite single phase structure, comprises in the present invention.
Above-described metal structure, by using the steel of above-mentioned composition, obtains by the method manufacture of the following stated.
3. about the hardness in center segregation portion
The relation of the hardness in the HIC test-results of electric slit-tube pipeline steel tube and the center segregation portion of steel plate is investigated, even if found that, the Vickers' hardness in center segregation portion is set to below Hv230, also has the situation that cannot realize CLR≤15%.This reason of investigation is considered from the homogeneous viewpoint of material, result as shown in Figure 1, by making the hardness in center segregation portion be less than 1.20 with the ratio (Vickers' hardness in the Vickers' hardness/non-segregation portion in center segregation portion) of the hardness in non-segregation portion, thus CLR is made to be less than 15%.Further, the composition ratio making the hardness in center segregation portion with the hardness in non-segregation portion being less than to 1.20 steel is studied, and as shown in Figure 2, makes the hardness in center segregation portion count less than 1.90 with the composition that the ratio of the hardness in non-segregation portion is less than the steel of 1.20 with SP value.
Should illustrate, about the hardness in center segregation portion, to structure observation test film, the corrosion of more than 30 seconds is implemented with 2% nital, after center segregation line is showed, as shown in Figure 3, respectively on the Line of Segregation of center and the place of distance center Line of Segregation 200 μm is measured to 15 points and tries to achieve respective arithmetical mean, as the hardness in center segregation portion and non-segregation portion.
4. about manufacturing condition
Below the manufacturing condition for realizing above-mentioned structure of steel is described.
Billet heating temperature is 1100 DEG C ~ 1300 DEG C.If be less than 1100 DEG C, then make the complete solid solution of carbide generated in steel be insufficient at continuous casting working procedure, can not get the intensity needed.On the other hand, if be heated beyond 1300 DEG C, then the remarkable coarsening of austenite crystal thus degraded toughness.Should illustrate, this temperature is the in-furnace temperature of process furnace, until steel billet center (center of slab) is heated to this temperature.
At finishing rolling step, the accumulative draft below 930 DEG C is needed to be implement finish rolling under the condition of more than 20%.If but accumulation draft is less than 20%, then the generation point of bainite ferrite tissue is not enough and become thick tissue, thus degraded toughness.If but accumulation draft is more than 80%, then not only its effect is saturated, also apply huge load to roller mill, thus preferably the upper limit of accumulation draft is less than 80%.
The average cooling rate at thickness of slab center is 5 ~ 100 DEG C/s.If be less than the speed of cooling of 5 DEG C/s, even if then add the element of raising hardening capacity of Cu, Ni and Cr and so on, because the Line Integral rate of ferrite and/or pearlitic structure is more than more than 3%, therefore need the cooling rate speed of 5 DEG C/more than s.On the other hand, during more than 100 DEG C/s, the Line Integral rate of martensitic stucture is more than 3%.The speed of cooling at thickness of slab center calculates as follows: use the cooling power (cooling capacity) of the conveying (run-out) investigated in advance (heat passes coefficient (heat-transfercoefficient)) and in transport platform, utilize the surface temperature of radiating the steel plate that thermometer (radiation thermometer) measures to carry out Calculation of Heat Transfer (heat-transfer calculation), trying to achieve the temperature history (temperature history) at thickness of slab center.
The temperature range that cooling stops is set to 380 DEG C ~ 600 DEG C.If more than 600 DEG C, the Line Integral rate of ferrite and pearlite tissue is more than 3%, and intensity reduces because of the coarsening of the precipitation strength particle of Nb carbonitride and so on.On the other hand, when lower than 380 DEG C, the resistance to deformation (deformation resistance) of steel plate increases, and be not only difficult to wound into rolls, the precipitation strength particle of Nb carbonitride and so on is not also separated out, and therefore intensity reduces.
Embodiment 1
For the steel of the composition shown in table 1, be wound into the web-like carrying out hot rolling by the hot-rolled condition shown in table 2 and cooling conditions, make the hot-rolled steel sheet of the thickness of slab shown in table 2.Should illustrate, steel grade G ~ K is individual components, SP value etc. is extraneous comparative steel of the present invention.
Take test film from the hot-rolled steel sheet obtained, implement structure observation, tension test, Charpy impact test, measurement of hardness and HIC test, evaluate tensile properties, toughness and hic resistance.
Structure observation test film is taked from the hot-rolled steel sheet obtained, rolling direction cross section is ground, corroded, take more than 5 visuals field by opticmicroscope (multiplying power 400 times) and scanning electronic microscope (electronscanning microscope) (multiplying power 1000 times) in thickness of slab central position, observe the structure of steel (ferrite, fine martensite, perlite and residual austenite etc.) had beyond amorphous kind, bainite ferrite tissue.
For tension test, to the hot-rolled steel sheet obtained, in the mode that the direction (C direction) orthogonal with rolling direction is long side direction, based on the regulation of API-5L, implement tension test in room temperature, try to achieve yielding stress YS (deformation stress of norminal strain 0.5%) and tensile strength TS.
For Charpy impact test, V nick-break test sheet is taked from the thickness of slab central part of the hot-rolled steel sheet obtained in the mode that the direction (C direction) orthogonal with rolling direction is long side direction, based on scope enforcement Charpy impact test (Charpyimpact test) being defined in-140 DEG C ~ 0 DEG C of JIS Z 2242, measure and absorb energy (absorbed energy) and brittle rupture rate (percentbrittle fracture), obtain the temperature (fracture transition temperature (fracture transition temperature)) that brittle rupture rate is 50%.In addition, test film is at each temperature set to 3, obtains obtained absorption energy and the arithmetical av of brittle rupture rate.
For the hardness in center segregation portion, with 2% nital, structure observation test film is implemented to the corrosion of more than 30 seconds, after Line of Segregation is showed, measure on Line of Segregation respectively and each 15 points in place of distance Line of Segregation 200 μm, obtain respective arithmetical av, as the hardness (Fig. 3) in segregation portion and non-segregation portion.Should illustrate, measurement of hardness uses Vickers hardness tester, carries out with test force 0.3kgf.Hardness ratio is calculated divided by non-segregation portion hardness segregation portion hardness.
For HIC test, the mode of the rolling direction being steel plate to make long side direction takes the HIC test film of steel plate thickness of slab × 20mm width × 100mm length from the hot-rolled steel sheet obtained, based on the regulation of NACE TM 0284, evaluate hic resistance by solution A.Should illustrating, test blade number is set to 10, in order to reflect the impact of plastix strain during electricity seam steel pipe forming, giving the compressive set of 10% in advance at width.Its result, in total Test sheet, judges that the volume of crack length ratio (CLR)≤15% is hic resistance good (zero).Judge that the volume of CLR > 15% in arbitrary test film is hic resistance bad (×).
The obtained results are shown in table 3.
The MIN toughness for pipeline steel tube of the high strength with YS >=380MPa and less than vTrs=-60 DEG C is and the steel plate that hardness ratio is less than 1.20, hic resistance is good in example of the present invention.On the other hand, at extraneous comparative example of the present invention, can not get desired toughness, or hic resistance reduces, and cannot guarantee as the characteristic desired by the hot-rolled steel sheet of the high strength electricity seam steel pipe of hic resistance excellence.
Claims (1)
1. the effective hot-rolled steel sheet of high-strength line-pipe steel, it is characterized in that, become to be grouped in mass %, containing C:0.02 ~ 0.06%, Si:0.05 ~ 0.25%, Mn:0.60 ~ 1.10%, below P:0.008%, below S:0.0010%, Nb:0.010 ~ 0.060%, Ti:0.001 ~ 0.020%, below Mo:0.05%, Cr:0.05 ~ 0.50%, Al:0.01 ~ 0.08%, Ca:0.0005 ~ 0.0050%, below O:0.005%, further containing being selected from below Cu:0.50%, below Ni:0.50%, more than a kind in below V:0.10%, remainder is made up of Fe and inevitable impurity, meet following formula (1), metal structure is bainite ferrite, the hardness in center segregation portion is less than 1.20 with the ratio of the hardness in non-segregation portion,
SP≤1.90……(1)
Wherein, SP is obtained by SP=Mn+Mo+11.3 × C+0.29 × (Cu+Ni)+0.60 × Cr+0.88 × V, and the symbol of element in formula represents the quality % of each element.
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| PCT/JP2014/000320 WO2014115549A1 (en) | 2013-01-24 | 2014-01-23 | Hot-rolled steel plate for high-strength line pipe |
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| US (1) | US20150368736A1 (en) |
| EP (1) | EP2927339B1 (en) |
| JP (1) | JP5884202B2 (en) |
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Cited By (4)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN105132833A (en) * | 2015-10-10 | 2015-12-09 | 武汉钢铁(集团)公司 | Economical type high-strength undersea pipeline steel and production method |
| CN107974613A (en) * | 2017-11-23 | 2018-05-01 | 武汉钢铁有限公司 | The production method of the X80 level pipe line steels of resisting sulfide stress corrosion cracking |
| CN110475894A (en) * | 2017-03-30 | 2019-11-19 | 杰富意钢铁株式会社 | Acid resistance line-pipes high-strength steel sheet and its manufacturing method and the high tensile steel tube for using acid resistance line-pipes high-strength steel sheet |
| CN111270137A (en) * | 2020-02-17 | 2020-06-12 | 本钢板材股份有限公司 | Acid corrosion resistant pipeline steel X52MS hot-rolled coil and preparation method thereof |
Families Citing this family (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN104404383A (en) * | 2014-11-28 | 2015-03-11 | 钢铁研究总院 | Ultra-low carbon hydrogen sulfide corrosion resistance X80 pipeline steel and preparation method |
| KR102498135B1 (en) * | 2020-12-18 | 2023-02-08 | 주식회사 포스코 | High-strength steel material having excellent resistance of sulfide stress crack, and method for manufacturing thereof |
| CN113406291A (en) * | 2021-06-29 | 2021-09-17 | 西安热工研究院有限公司 | Quality verification method of structural steel plate for wind power tower |
Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH07216500A (en) * | 1994-01-28 | 1995-08-15 | Sumitomo Metal Ind Ltd | High strength steel material excellent in corrosion resistance and its production |
| US20070217942A1 (en) * | 2004-02-04 | 2007-09-20 | Sumitomo Metal Industries, Ltd. | Steel Product for Use as Line Pipe Having High Hic Resistance and Line Pipe Produced Using Such Steel Product |
| JP2011063840A (en) * | 2009-09-16 | 2011-03-31 | Sumitomo Metal Ind Ltd | Steel sheet having excellent hic resistance and uoe steel pipe |
| CN102301015A (en) * | 2009-01-30 | 2011-12-28 | 杰富意钢铁株式会社 | Heavy gauge, high tensile strength, hot rolled steel sheet with excellent HIC resistance and manufacturing method therefor |
| CN102834539A (en) * | 2010-04-09 | 2012-12-19 | 杰富意钢铁株式会社 | High-strength steel sheet having excellent hot rolling workability, and process for production thereof |
| CN102844126A (en) * | 2010-04-16 | 2012-12-26 | 杰富意钢铁株式会社 | Process for producing hot-rolled steel sheet and process for producing hot-dip galvanized steel sheet |
Family Cites Families (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH0726176B2 (en) * | 1991-02-28 | 1995-03-22 | 株式会社神戸製鋼所 | Steel plate with which HAZ cracks are less likely to occur in the high heat input welding corner joints of steel box columns |
| JP2647302B2 (en) | 1992-03-30 | 1997-08-27 | 新日本製鐵株式会社 | Method for producing high-strength steel sheet with excellent resistance to hydrogen-induced cracking |
| US5545269A (en) * | 1994-12-06 | 1996-08-13 | Exxon Research And Engineering Company | Method for producing ultra high strength, secondary hardening steels with superior toughness and weldability |
| JP3613395B2 (en) * | 2002-03-28 | 2005-01-26 | 日本高周波鋼業株式会社 | Hot work tool steel |
| JP3869747B2 (en) * | 2002-04-09 | 2007-01-17 | 新日本製鐵株式会社 | High-strength steel plate, high-strength steel pipe and manufacturing method excellent in deformation performance |
| JP2006063351A (en) | 2004-08-24 | 2006-03-09 | Sumitomo Metal Ind Ltd | High strength steel plate with excellent hydrogen induced cracking resistance, its manufacturing method, and steel pipe for line pipe |
| BRPI0617763A2 (en) * | 2005-10-24 | 2011-08-02 | Exxonmobil Upstream Res Co | high strength double phase steel with low deformation ratio, high hardness and superior casting capacity |
| JP5348382B2 (en) * | 2008-09-30 | 2013-11-20 | Ｊｆｅスチール株式会社 | A steel plate for high toughness linepipe with a low yield stress reduction due to the Bauschinger effect and a method for producing the same. |
| JP5640792B2 (en) * | 2011-02-15 | 2014-12-17 | Ｊｆｅスチール株式会社 | High toughness UOE steel pipe excellent in crushing strength and manufacturing method thereof |
| JP5776377B2 (en) * | 2011-06-30 | 2015-09-09 | Ｊｆｅスチール株式会社 | High-strength hot-rolled steel sheet for welded steel pipes for line pipes with excellent sour resistance and method for producing the same |
-
2014
- 2014-01-23 KR KR1020157017737A patent/KR101718267B1/en active IP Right Grant
- 2014-01-23 EP EP14743980.6A patent/EP2927339B1/en active Active
- 2014-01-23 US US14/763,403 patent/US20150368736A1/en not_active Abandoned
- 2014-01-23 JP JP2014558503A patent/JP5884202B2/en active Active
- 2014-01-23 WO PCT/JP2014/000320 patent/WO2014115549A1/en active Application Filing
- 2014-01-23 CN CN201480005063.4A patent/CN104937125B/en active Active
Patent Citations (6)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH07216500A (en) * | 1994-01-28 | 1995-08-15 | Sumitomo Metal Ind Ltd | High strength steel material excellent in corrosion resistance and its production |
| US20070217942A1 (en) * | 2004-02-04 | 2007-09-20 | Sumitomo Metal Industries, Ltd. | Steel Product for Use as Line Pipe Having High Hic Resistance and Line Pipe Produced Using Such Steel Product |
| CN102301015A (en) * | 2009-01-30 | 2011-12-28 | 杰富意钢铁株式会社 | Heavy gauge, high tensile strength, hot rolled steel sheet with excellent HIC resistance and manufacturing method therefor |
| JP2011063840A (en) * | 2009-09-16 | 2011-03-31 | Sumitomo Metal Ind Ltd | Steel sheet having excellent hic resistance and uoe steel pipe |
| CN102834539A (en) * | 2010-04-09 | 2012-12-19 | 杰富意钢铁株式会社 | High-strength steel sheet having excellent hot rolling workability, and process for production thereof |
| CN102844126A (en) * | 2010-04-16 | 2012-12-26 | 杰富意钢铁株式会社 | Process for producing hot-rolled steel sheet and process for producing hot-dip galvanized steel sheet |
Cited By (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN105132833A (en) * | 2015-10-10 | 2015-12-09 | 武汉钢铁(集团)公司 | Economical type high-strength undersea pipeline steel and production method |
| CN110475894A (en) * | 2017-03-30 | 2019-11-19 | 杰富意钢铁株式会社 | Acid resistance line-pipes high-strength steel sheet and its manufacturing method and the high tensile steel tube for using acid resistance line-pipes high-strength steel sheet |
| CN110475894B (en) * | 2017-03-30 | 2022-03-22 | 杰富意钢铁株式会社 | High-strength steel sheet for acid-resistant line pipe, method for producing same, and high-strength steel pipe using high-strength steel sheet for acid-resistant line pipe |
| CN107974613A (en) * | 2017-11-23 | 2018-05-01 | 武汉钢铁有限公司 | The production method of the X80 level pipe line steels of resisting sulfide stress corrosion cracking |
| CN111270137A (en) * | 2020-02-17 | 2020-06-12 | 本钢板材股份有限公司 | Acid corrosion resistant pipeline steel X52MS hot-rolled coil and preparation method thereof |
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| Publication number | Publication date |
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| US20150368736A1 (en) | 2015-12-24 |
| JPWO2014115549A1 (en) | 2017-01-26 |
| WO2014115549A1 (en) | 2014-07-31 |
| EP2927339B1 (en) | 2016-11-02 |
| EP2927339A1 (en) | 2015-10-07 |
| CN104937125B (en) | 2018-01-09 |
| JP5884202B2 (en) | 2016-03-15 |
| EP2927339A4 (en) | 2015-12-16 |
| KR101718267B1 (en) | 2017-03-20 |
| KR20150087424A (en) | 2015-07-29 |
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