CN104937124A - HOT-ROLLED STEEL PLATE FOR HIGH-STRENGTH LINE PIPE AND HAVING TENSILE STRENGTH OF AT LEAST 540 MPa - Google Patents

HOT-ROLLED STEEL PLATE FOR HIGH-STRENGTH LINE PIPE AND HAVING TENSILE STRENGTH OF AT LEAST 540 MPa Download PDF

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CN104937124A
CN104937124A CN201480004904.XA CN201480004904A CN104937124A CN 104937124 A CN104937124 A CN 104937124A CN 201480004904 A CN201480004904 A CN 201480004904A CN 104937124 A CN104937124 A CN 104937124A
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steel
hot
strength
rolled steel
hic
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后藤聪太
丰田俊介
冈部能知
冈崎雪彦
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JFE Steel Corp
JFE Engineering Corp
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NKK Corp
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    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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    • C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
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    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
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    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
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    • C21D9/50—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for welded joints
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    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
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    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
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    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/002—Bainite

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  • Heat Treatment Of Steel (AREA)

Abstract

The objective of the present invention is to provide a hot-rolled steel plate that is for a high-strength line pipe, has superior HIC resistance and is favorable as an element of a high-strength seam-welded line pipe that is API X70 or higher. The hot-rolled steel plate for a high-strength line pipe has a tensile strength of at least 540 MPa and 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, 0.020-0.060% of Nb, 0.001-0.020% of Ti, 0.01-0.08% of Al, and 0.0005-0.0050% of Ca, and furthermore at least one element selected from among no greater than 0.50% of Cu, no greater than 0.50% of Ni, no greater than 0.50% of Cr, no greater than 0.50% of Mo, and no greater than 0.10% of V, the remainder comprising Fe and unavoidable impurities; satisfying 0.60 <= CP <= 0.90; and furthermore satisfying CM <= 3.05.

Description

The effective hot-rolled steel sheet of high-strength line-pipe steel of more than tensile strength 540MPa
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 70, the pipeline steel tube electricity consumption seam tube material be suitable as the Energy resources of conveying crude oil or Sweet natural gas and so on uses.
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, the deviation (deviation) of wall thickness (wall thickness) and circularity (roundness) 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 rollforming), 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.The pipeline steel tube used in such place, except desired strength, toughness and weldability, also requires 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, Patent Document 3 discloses a kind of by making the Nb concentration being arranged in the region of the distance of 5% of thickness of slab from the central part in thickness of slab direction to thickness of slab direction be 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 utilize 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, although it is innoxious to utilize method disclosed in patent documentation 1 ~ 3 can carry out to a certain degree to HIC starting point, but particularly for the high tensile steel plate of more than API X70, because the susceptibility (sensitivity) to HIC increases, if so only control inclusion amount and size, sufficient effect cannot be obtained.
In addition, use the method effectively utilizing Cr and Mo disclosed in patent documentation 4, if excessive interpolations Cr and Mo, then have the generation of growth encourage martensite in center segregation portion, hic resistance reduces this problem.
The present invention carries out in view of above-mentioned problem, its object is to provide a kind of be suitable as the material of the high strength electricity slit-tube pipeline steel tube of more than API X70, the effective hot-rolled steel sheet of high-strength line-pipe steel of hic resistance excellence.
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 completes based on following consideration; in the effective hot-rolled steel sheet of high-strength line-pipe steel of more than the TS:540MPa that HIC susceptibility is high; the hardening capacity in center segregation portion is improved by adjustment steel composition; by the tissue particle in center segregation portion; improve HIC and expand resistance (propagation resistance of HIC); thus when there are some and becoming the inclusion of HIC generation starting point, crack length ratio C LR is suppressed to less.That is, purport of the present invention is as follows.
[1] the effective hot-rolled steel sheet of high-strength line-pipe steel of the hic resistance excellence of a kind of more than tensile strength 540MPa, 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:0.020 ~ 0.060%, Ti:0.001 ~ 0.020%, Al:0.01 ~ 0.08%, Ca:0.0005 ~ 0.0050%, further containing being selected from below Cu:0.50%, below Ni:0.50%, below Cr:0.50%, below Mo:0.05%, more than a kind in below V:0.10%, remainder is made up of Fe and inevitable impurity, and meet following formula (1).
0.60≤CP≤0.90……(1)
Should illustrate, CP is obtained by CP=4.46 × C+2.37 × Mn/6+ (1.18 × Cr+1.95 × Mo+1.74 × V)/5+ (1.74 × Cu+1.70 × Ni)/15, 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 of more than the tensile strength 540MPa recorded in above-mentioned [1], it is characterized in that, except mentioned component composition, also meet following formula (2).
CM≤3.05……(2)
Here, CM is obtained by CM=2.37 × Mn+2.34 × Mo+0.59 × Cr+0.17 × Ni, and the symbol of element in formula represents 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 of more than the tensile strength 540MPa recorded in above-mentioned [1] or [2], it is characterized in that, except mentioned component composition, the metal structure in center segregation portion is in the bainite ferrite tissue of Line Integral rate more than 95% (bainitic-ferrite microstructure), and the median size of bainite ferrite tissue is less than 8.0 μm.
[4] manufacture method of the effective hot-rolled steel sheet of high-strength line-pipe steel of the hic resistance excellence of a kind of more than tensile strength 540MPa, 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 10 ~ 100 DEG C/s at thickness of slab center, thereafter wound into a roll.
According to the present invention, the high tensile hot rolled steel sheet of hic resistance excellence can be manufactured, even if when there are some inclusiones in this hot-rolled steel sheet, also HIC can be suppressed by the tissue in control center's segregation portion imperceptibly, even if also can no problemly use under the severe rugged environment suitable with NACE solution, be applicable to API X70 with the seam steel pipe pipeline steel tube that powers on.In addition, the hot-rolled steel sheet manufactured by the present invention also can be used for the Spiral Steel Pipe pipeline steel tube (spiral steel pipe forlinepipe) of more than API X70.
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, plays its effect containing more than 0.02%, but the content more than 0.06%, then easily generate the second-phase as pearlitic structure (pearlitemicrostructure), 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 0.80 ~ 1.10%.Be more preferably 0.80 ~ 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：0.020～0.060％
Nb to separate out with the form of Nb carbonitride in the rolling step (coiling process) when manufacturing hot-rolled steel sheet and the element that improves of the intensity contributing to steel imperceptibly.In addition, be the element suppressing the growth of austenite crystal when electric seam welding connects, contribute to the toughness raising of weld part.Containing more than 0.020% 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 0.020 ~ 0.060%.Be preferably the scope of 0.030 ~ 0.050%.
Ti：0.001～0.020％
Ti be in order to the N that the toughness of steel is significantly worsened 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%.
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, and makes 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 to 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%.
In the present invention, can in following scope further containing more than a kind in Cu, Ni, Cr, Mo, 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, and its above content then causes extra cost increase.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, and its above content can cause extra cost increase.Therefore, Ni amount is less than 0.50%.Be preferably less than 0.40%.
Below Cr:0.50%
Cr improves the element that hardening capacity, the toughness contributing to steel and intensity improves, containing more than 0.05% time play its effect, but form Cr oxide compound when electric seam welding connects the toughness of weld part significantly worsened.In order to suppress to form Cr oxide compound, Cr amount is set to less than 0.50%.Be preferably less than 0.30%.
Below Mo:0.50%
Mo improves hardening capacity and extremely contributes to the element that the toughness of steel and intensity improves, containing more than 0.05% time play its effect, if but in the scope more than 0.50%, its effect is saturated, its above content causes extra cost increase.Therefore, Mo amount is less than 0.50%.Be preferably less than 0.30%.
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%.
CP：0.60～0.90
In the present invention, the CP value obtained by the content of each alloying element is made to meet following formula (1).
0.60≤CP≤0.90……(1)
Should illustrate, CP is obtained by CP=4.46 × C+2.37 × Mn/6+ (1.18 × Cr+1.95 × Mo+1.74 × V)/5+ (1.74 × Cu+1.70 × Ni)/15, and the symbol of element in formula represents the quality % of each element.In addition, the element do not added is set to 0.
CP value is the index of the hardening capacity representing center segregation portion, by being that the mode of more than 0.60 adjusts steel composition with CP value, can obtain the fine bainite ferrite tissue of less than 8.0 μm in center segregation portion.On the other hand, if CP value is more than 0.90, then hardening capacity excessively improves, and center segregation portion hardness rises.Therefore, CP value is set to 0.60 ~ 0.90.Be more preferably 0.70 ~ 0.90.
Below CM:3.05
The fine martensitic stucture generated in center segregation portion makes hic resistance be deteriorated.The element contributing to the generation of fine martensitic stucture is Mn, Mo, Cr, Ni, and the value quantized by the disturbance degree of these elements to fine martensite growing amount is CM value.In order to make the fine martensitic stucture generated in center segregation portion be less than 5% in Line Integral rate, then the following CM value illustrated will meet following formula (2).
CM≤3.05……(2)
Here, CM is obtained by CM=2.37 × Mn+2.34 × Mo+0.59 × Cr+0.17 × Ni, and the symbol of element in formula represents the quality % of each element.Be more preferably less than 2.95.
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 of other trace element.
2. about metal structure
Next, the metal structure of steel of the present invention is described.
The metal structure of steel of the present invention must become tissue and the bainite ferrite tissue of tenacity excellent.If there is the different sorts such as fine martensite or top bainite, perlite to organize phase in bainite ferrite tissue, then form the trap point of hydrogen, therefore hic resistance reduces.Therefore, the tissue beyond bainite ferrite tissue divides rate more few better.But, due to the Line Integral rate beyond bainite ferrite tissue extremely low when, its impact is little of ignoring, so can allow the amount acquired a certain degree.Specifically, if the structure of steel (fine martensite, top bainite, perlite etc.) beyond bainite ferrite tissue the total less than 5% of the Line Integral rate shared by center segregation portion, then comprises in the present invention.
The median size of bainite ferrite tissue: less than 8.0 μm
In order to obtain the sufficient toughness (vTrs≤-80 DEG C) as pipeline steel tube purposes, the median size making bainite ferrite is needed to be less than 8.0 μm.In addition, in order to improve HIC crack propagation resistance, median size is also preferably made to be less than 8.0 μm.Be preferably less than 6.0 μm.
3. about manufacturing condition
Then, 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 10 ~ 100 DEG C/s.If be less than the speed of cooling of 10 DEG C/s, even if the hardening capacity of then adding Cu, Ni, Cr and so on improves element, also because the Line Integral rate of ferrite and/or pearlitic structure is more than 5%, and need the cooling rate speed of 10 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 5%.The speed of cooling at thickness of slab center calculates as follows: use the surface temperature of the steel plate that the cooling power (cooling capacity) of the conveying (run-out) investigated in advance (heat passes coefficient (heat-transfer coefficient)) and transport platform utilize radiation thermometer (radiation thermometer) to measure to carry out Calculation of Heat Transfer (heat-transfer calculation), obtain 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, because of the coarsening of the precipitation strength particle of Nb carbonitride and so on, intensity reduces.And then promote denseization of carbon in center segregation portion, become and easily generate fine martensite, top bainite and perlite.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.
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, more than 30 seconds are flooded at 2% nital, after Line of Segregation (segregation line) is showed, with scanning electronic microscope (electron scanning microscope) (multiplying power 2000 times), more than 5 visuals field are taken to segregation position, measures the Line Integral rate being harmful to the 2nd phase of the kind of tissue, bainite ferrite particle diameter, fine martensite, top bainite and perlite and so on.Structure of steel judges according to the structure observation test film taked from 1/4t position, thickness of slab direction.
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, obtain yielding stress YS (deformation stress during 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%.Should illustrate, test film is at each temperature set to 3, obtain obtained absorption energy and the arithmetical av of brittle rupture rate.
Should illustrate, fracture transition temperature (vTrs) is less than-80 DEG C and be set to good (zero).
For HIC test, the mode becoming the rolling direction of steel plate with 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 present invention's example is all have the high strength of TS >=540MPa and the steel plate of good hic resistance.On the other hand, at extraneous comparative example of the present invention, can not get desired intensity, 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 (2)

1. the effective hot-rolled steel sheet of the high-strength line-pipe steel of more than a tensile strength 540MPa, 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:0.020 ~ 0.060%, Ti:0.001 ~ 0.020%, Al:0.01 ~ 0.08%, Ca:0.0005 ~ 0.0050%, further containing being selected from below Cu:0.50%, below Ni:0.50%, below Cr:0.50%, below Mo:0.50%, more than a kind in below V:0.10%, remainder is made up of Fe and inevitable impurity, and meet following formula (1) and formula (2),
0.60≤CP≤0.90……(1)
Wherein, CP is obtained by CP=4.46 × C+2.37 × Mn/6+ (1.18 × Cr+1.95 × Mo+1.74 × V)/5+ (1.74 × Cu+1.70 × Ni)/15, and the symbol of element in formula represents the quality % of each element,
CM≤3.05……(2)
Here, CM is obtained by CM=2.37 × Mn+2.34 × Mo+0.59 × Cr+0.17 × Ni, and the symbol of element in formula represents the quality % of each element.
2. the effective hot-rolled steel sheet of the high-strength line-pipe steel of more than tensile strength 540MPa according to claim 1, it is characterized in that, except described one-tenth is grouped into, the metal structure in center segregation portion is the bainite ferrite tissue in Line Integral rate more than 95%, and the median size of bainite ferrite tissue is less than 8.0 μm.
CN201480004904.XA 2013-01-24 2014-01-23 HOT-ROLLED STEEL PLATE FOR HIGH-STRENGTH LINE PIPE AND HAVING TENSILE STRENGTH OF AT LEAST 540 MPa Pending CN104937124A (en)

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Cited By (6)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN105112808A (en) * 2015-10-10 2015-12-02 武汉钢铁(集团)公司 High-strength marine riser steel and production method
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
CN108998746A (en) * 2017-12-25 2018-12-14 武汉科技大学 A kind of X70 grade pipe line steel of high Properties of HIC resistance and preparation method thereof
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Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2005264217A (en) * 2004-03-17 2005-09-29 Jfe Steel Kk Thick hot rolled steel plate having excellent hic resistance and its production method
JP2006274338A (en) * 2005-03-29 2006-10-12 Jfe Steel Kk Hot rolled steel sheet for sour resistant high strength electric resistance welded pipe having excellent hic resistance and weld zone toughness, and method for producing the same
CN100354436C (en) * 2004-02-24 2007-12-12 杰富意钢铁株式会社 Hot-rolled steel sheet for high-strength electric-resistancewelded pipe having sour-gas resistance and excellent weld toughness, and method for manufacturing the same
JP2012241266A (en) * 2011-05-24 2012-12-10 Jfe Steel Corp Steel pipe for sour resistant line pipe having high compressive strength and method for producing the same

Family Cites Families (15)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
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
JPH06271974A (en) * 1993-03-18 1994-09-27 Nippon Steel Corp Line pipe excellent in hydrogen induced cracking resistance
JPH06306530A (en) * 1993-04-26 1994-11-01 Nippon Steel Corp Low-medium strength uoe line pipe excellent in sulfide stress cracking resistance in weld zone
JPH07216500A (en) * 1994-01-28 1995-08-15 Sumitomo Metal Ind Ltd High strength steel material excellent in corrosion resistance and its production
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
JPH0941083A (en) * 1995-07-28 1997-02-10 Nkk Corp Resistance welded tube excellent in hic resistance and sscc resistance and its production
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
JP4341396B2 (en) * 2003-03-27 2009-10-07 Ｊｆｅスチール株式会社 High strength hot rolled steel strip for ERW pipes with excellent low temperature toughness and weldability
WO2005075694A1 (en) 2004-02-04 2005-08-18 Sumitomo Metal Industries,Ltd. Steel product for line pipe excellent in resistance to hic and line pipe produced by using the steel product
JP4375087B2 (en) * 2004-03-31 2009-12-02 Ｊｆｅスチール株式会社 High strength and high toughness hot-rolled steel strip with excellent material homogeneity and manufacturing method thereof
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
EP1951519A4 (en) * 2005-10-24 2008-12-31 Exxonmobil Upstream Res Co High strength dual phase steel with low yield ratio, high toughness and superior weldability
CN102301015B (en) * 2009-01-30 2013-11-06 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
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

Patent Citations (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN100354436C (en) * 2004-02-24 2007-12-12 杰富意钢铁株式会社 Hot-rolled steel sheet for high-strength electric-resistancewelded pipe having sour-gas resistance and excellent weld toughness, and method for manufacturing the same
JP2005264217A (en) * 2004-03-17 2005-09-29 Jfe Steel Kk Thick hot rolled steel plate having excellent hic resistance and its production method
JP2006274338A (en) * 2005-03-29 2006-10-12 Jfe Steel Kk Hot rolled steel sheet for sour resistant high strength electric resistance welded pipe having excellent hic resistance and weld zone toughness, and method for producing the same
JP2012241266A (en) * 2011-05-24 2012-12-10 Jfe Steel Corp Steel pipe for sour resistant line pipe having high compressive strength and method for producing the same

Cited By (7)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
CN105112808A (en) * 2015-10-10 2015-12-02 武汉钢铁(集团)公司 High-strength marine riser steel and production method
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
CN109536847A (en) * 2017-09-21 2019-03-29 上海梅山钢铁股份有限公司 390MPa grades of welded tube hot rolled steel plates of yield strength and its manufacturing method
CN109536847B (en) * 2017-09-21 2020-12-08 上海梅山钢铁股份有限公司 Hot rolled steel plate for welded pipe with yield strength of 390MPa and manufacturing method thereof
CN108998746A (en) * 2017-12-25 2018-12-14 武汉科技大学 A kind of X70 grade pipe line steel of high Properties of HIC resistance and preparation method thereof
CN112752857A (en) * 2018-09-28 2021-05-04 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
CN111378893A (en) * 2018-12-28 2020-07-07 上海梅山钢铁股份有限公司 Hot-rolled steel plate for longitudinal welded pipe with yield strength of 290MPa

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