CN107109566A - The excellent steel plate of hydrogen induced cracking resistance and line-pipes steel pipe - Google Patents

The excellent steel plate of hydrogen induced cracking resistance and line-pipes steel pipe Download PDF

Info

Publication number
CN107109566A
CN107109566A CN201580070001.6A CN201580070001A CN107109566A CN 107109566 A CN107109566 A CN 107109566A CN 201580070001 A CN201580070001 A CN 201580070001A CN 107109566 A CN107109566 A CN 107109566A
Authority
CN
China
Prior art keywords
slab
concentration
steel plate
hic
decrements
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Pending
Application number
CN201580070001.6A
Other languages
Chinese (zh)
Inventor
田代喜郎
田代喜一郎
加藤拓
冈佑
冈佑一
佐藤进佑
川野晴弥
三宅孝司
木村世意
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Kobe Steel Ltd
Original Assignee
Kobe Steel Ltd
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Kobe Steel Ltd filed Critical Kobe Steel Ltd
Priority claimed from PCT/JP2015/085869 external-priority patent/WO2016104526A1/en
Publication of CN107109566A publication Critical patent/CN107109566A/en
Pending legal-status Critical Current

Links

Classifications

    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/58—Ferrous alloys, e.g. steel alloys containing chromium with nickel with more than 1.5% by weight of manganese
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0221—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the working steps
    • C21D8/0226—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips
    • C21D8/0247—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment
    • C21D8/0263—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips characterised by the heat treatment following hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/10—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies
    • C21D8/105—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of tubular bodies of ferrous alloys
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
    • C21D9/08—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for tubular bodies or pipes
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/005—Ferrous alloys, e.g. steel alloys containing rare earths, i.e. Sc, Y, Lanthanides
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/16—Ferrous alloys, e.g. steel alloys containing copper
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/02—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips

Landscapes

  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Manufacturing & Machinery (AREA)
  • Heat Treatment Of Steel (AREA)
  • Treatment Of Steel In Its Molten State (AREA)

Abstract

Realize hydrogen induced cracking resistance excellent steel plate and steel pipe.It is not used in after rolling carrying out hydrogen induced cracking experiment in addition, realizing, the steel plate and steel pipe of hydrogen induced cracking resistance can be just evaluated according to the inside quality of slab.The excellent steel plate of the hydrogen induced cracking resistance, it is characterized in that, C, Si, Mn, P, S, Al, Ca, N and O as defined in meeting, additionally containing more than one the element selected in the group constituted from defined REM and Zr, surplus is made up of iron and inevitable impurity, the Ca and S ratio (Ca/S) is more than 2.0, and the Ca, the S and the O meet (Ca-1.25S)/O≤1.80, in addition, the Ca concentration of molten steel subtracts the Ca decrements of the Ca concentration of slab in threshold value Ca out of tundishdropθHereinafter, threshold value CadropθThe maximum Ca decrements of hydrogen induced cracking do not occur for steel plate obtained from being the rolling slab.

Description

The excellent steel plate of hydrogen induced cracking resistance and line-pipes steel pipe
Technical field
The present invention relates to the hydrogen induced cracking resistance of suitable natural gas Crude Oil Transportation line pipe and storage tank etc. and toughness are excellent Different steel plate and the hydrogen induced cracking resistance and the line-pipes steel pipe of tenacity excellent obtained using the steel plate.
Background technology
Mainly in the conveying line pipe and storage tank of oil coal gas etc., along with the resource inferior containing hydrogen sulfide Exploitation, it is necessary to the so-called resistance to SO_2 such as hydrogen induced cracking resistance and anti-stress-corrosion crack.Hereinafter, there will be the resistance to SO_2 Steel plate be referred to as " sulfur resistive steel plate ".On hydrogen induced cracking (Hydrogen Induced Cracking, hereinafter referred to as " HIC "), Understand to be accompanied by corrosion reaction that above-mentioned hydrogen sulfide etc. brings and invade the hydrogen inside steel, be with MnS, Nb (C, N) First non-metallic inclusion etc. aggregation, the crackle occurred due to gasification.
Known HIC easily occurs in the segregation portion for including center segregation, underbead crack etc. of slab, particularly easily with MnS etc. field trash is starting point.Therefore, in the past it is proposed that there is several technologies on improving hic resistance.For example in patent There are a kind of steel disclosed in document 1, it is by suppressing Mn, Nb, Ti of thickness of slab central part degree of segregation, so as to improve hic resistance Property.Have a kind of method disclosed in patent document 2 in addition, its according to the parameter type that is made up of Ca and O and S content, suppress with MnS and Ca systems oxysulfide is the HIC of starting point.
By these methods, although many HIC are inhibited, but still suffer from fine HIC and locally largely send out Raw situation.
On the other hand, steel plate by melting, casting, hot rolling and after obtaining, HIC examinations can be implemented before being delivered as product Test.But, HIC experiments are distinguished by result to be needed to spend several weeks.If in addition, above-mentioned HIC experiment in occur HIC, it is above-mentioned Steel plate cannot function as the excellent product delivery of hydrogen induced cracking resistance, but need to manufacture again, i.e., proceeded by again from melting, and Tested for the HIC that resulting product is carried out again.If so, then manufacturing cycle long life, as delivery period delay etc. The reason for.
Therefore consider, if tested after above-mentioned hot rolling without HIC, but the stage of the slab after the casting is just Hic resistance can be evaluated, then can significantly shorten the manufacturing cycle.HIC as described above because (center segregation, inside are split in segregation portion Line) and the generation by starting point of MnS etc. field trash, it is believed that, if can be evaluated in the stage of slab these, Hic resistance just can be evaluated based on this evaluation result.
For example, after rolling in the existing method of progress HIC experiments, following very long works can be undergone from casting to delivery Sequence A-1.In contrast, hic resistance can be evaluated if the stage in slab, then such as following process B -1, just it can omit " (being used for what HIC was tested) sample adjustment → HIC experiments " when carrying out HIC experiments, therefore, it is possible to make product deliver goods as early as possible.
Process A-1：Casting → rolling → (being used for what HIC was tested) sample adjustment → HIC experiments → delivery
Process B -1：Evaluation → rolling → delivery of casting → hic resistance
In addition, the result of HIC experiments is when being NG, in existing method, from casting to melting again can undergo it is very long under The process A-2 stated.If in contrast, as so following process Bs -2, can just evaluate hic resistance in the stage of slab, then Even if its evaluation is NG, " the rolling → (being used for what HIC was tested) sample adjustment → HIC in following process A-2 can be also omitted Experiment ", can start melting again as early as possible.
Process A-2：Casting → rolling → (being used for what HIC was tested) sample adjustment → HIC experiment → meltings again
Process B -2：The evaluation of casting → hic resistance → melting again
As such method, in patent document 3, a kind of Phase Evaluation underbead crack side of having in slab is disclosed Method.In this method, according to the evaluation result of underbead crack, judgement could carry out HCR (Hot Charge Rolling：Hot charging Rolling) operation.
In addition, though not evaluating CaO field trashes, but there is a kind of evaluate before the rolling to cast disclosed in patent document 4~8 The method of the quality of piece.For example, in patent document 4~7, object amount, amount of element are mingled with according to molten steel in slab and tundish Deng the quality for evaluating slab.In addition, in patent document 8, the quality of slab is evaluated according to the analysis result of molten steel in tundish (once judging), when the judgement precision is unsatisfactory for defined precision, the quality of slab is evaluated according to the analysis result of slab sample (secondary to judge).
Xian You Ji Intraoperative documents
Patent document
Patent document 1：Japanese Unexamined Patent Publication 2010-209461 publications
Patent document 2：Japanese Unexamined Patent Publication 06-136440 publications
Patent document 3：Japanese Unexamined Patent Publication 2006-198649 publications
Patent document 4：Japanese Unexamined Patent Application 62-277539 publications
Patent document 5：Japanese Unexamined Patent Publication 2002-214222 publications
Patent document 6：Japanese Unexamined Patent Publication 10-122854 publications
Patent document 7：Japanese Unexamined Patent Publication 10-249505 publications
Patent document 8：Japanese Unexamined Patent Publication 2000-292418 publications
Patent document 3~8, does not evaluate CaO field trashes, but be used as the evaluation method of CaO field trashes as described above, it is contemplated that As patent document 3~8, according to be mingled with object amount and amount of element etc. of molten steel in slab and tundish evaluated.
In order in the Phase Evaluation CaO field trashes of slab, it is necessary to CaO accumulation zones occur position analysis CaO amounts or Ca Concentration.But, there is deviation on the width, thickness direction and casting direction of slab in the position that CaO accumulation zones occur, Therefore, it is difficult to predict its position.Even if in addition, the defined part of analysis slab, its analysis result also just may not can say it is CaO The CaO amounts of accumulation zone.It is thus impossible to evaluate CaO field trashes according to the analysis result of slab.
Also contemplate for being mingled with object amount and amount of element etc. according to molten steel in tundish and evaluating CaO field trashes.But, CaO Field trash also can aggegation aggregation after injection mold.Therefore, according to the CaO amounts or Ca concentration of molten steel in tundish, even if It is evaluated as that CaO accumulation zones are not present, and thereafter, due to CaO field trash aggegations, it is possible to occurring HIC.
The content of the invention
Formed currently invention addresses above-mentioned such situation, it is intended that realizing the excellent steel of hydrogen induced cracking resistance Plate and steel pipe, are tested, but can just evaluate the steel plate of hic resistance according to the inside quality of slab in addition, realizing without HIC And steel pipe.
The excellent steel plate of the hydrogen induced cracking resistance of the invention of above-mentioned problem is can solve the problem that, is had the feature that, with matter % meters are measured, are met
C：0.02~0.15%,
Si：0.02~0.50%,
Mn：0.6~2.0%,
P：Higher than 0% and below 0.030%,
S：Higher than 0% and below 0.003%,
Al：0.010~0.08%,
Ca：0.0003~0.0060%,
N：0.001~0.01% and
O：Higher than 0% and below 0.0045%, in addition, also contain from
REM：Higher than 0% and below 0.02%, and
Zr：More than one the element selected in the group constituted higher than 0% and below 0.010%, surplus by iron and Inevitable impurity is constituted,
The Ca and S ratio (Ca/S) is more than 2.0, and
The Ca, the S and the O meet (Ca-1.25S)/O≤1.80,
In addition, subtracting Ca decrements obtained by the Ca concentration of slab from the Ca concentration of molten steel in tundish in threshold value CadropθHereinafter, threshold value CadropθThe maximum Ca that hydrogen induced cracking does not occur for steel plate obtained from being the rolling slab is reduced Amount.
The threshold value CadropθIt can also be the value tried to achieve in advance by following (i)~(iii) method.
(i) the Ca concentration and the Ca concentration of slab of molten steel in tundish are measured, from the Ca concentration of molten steel in the tundish In subtract the Ca concentration of the slab, calculate Ca decrements.
(ii) rolling carries out hydrogen in the slab with being cast under the slab identical casting condition for resulting steel plate Cause cracking test.
(iii) according to the hydrogen induced cracking result of the test by above-mentioned (i) Ca decrements measured and above-mentioned (ii), try to achieve not Occur the maximum Ca decrements of hydrogen induced cracking.
With the slab cast under the slab identical casting condition or the plate for measuring the Ca decrements Base.
The Ca concentration of the slab, can also in the slab in a thickness direction at different 2 more than position adjust Ca concentration is looked into, it is the minimum Ca concentration among the resulting Ca concentration of more than 2.
The threshold value CadropθCan also be 4ppm (quality ppm).
The steel plate, as other elements, can also contain among following (A) and (B) any more than 1.
(A) in terms of quality %, from B：Higher than 0% and below 0.005%, V：Higher than 0% and below 0.1%, Cu：It is high In 0% and below 1.5%, Ni：Higher than 0% and below 1.5%, Cr：Higher than 0% and below 1.5%, Mo：Higher than 0% And below 1.5% and Nb：More than one the element selected in the group constituted higher than 0% and below 0.06%
(B) in terms of quality %, from Ti：Higher than 0% and below 0.03% and Mg：The institute higher than 0% and below 0.01% More than one the element selected in the group of composition
Above-mentioned steel plate is suitable as line-pipes and pressure vessel is used.In addition in the present invention, also including by above-mentioned steel plate The line-pipes steel pipe of formation.
In accordance with the invention it is possible to provide hydrogen induced cracking resistance really excellent steel plate and steel pipe.Furthermore it is possible to provide to enter Row HIC is tested, and the steel plate and steel pipe of hic resistance can be just evaluated according to the inside quality of slab.It is suitable for natural gas Pressure vessel of the conveying line pipe and storage tank of crude oil etc. etc..
Brief description of the drawings
Fig. 1 is the schematic diagram for the flowing for illustrating CaO field trashes.
Fig. 2 is the figure for the Ca concentration distributions for representing various slabs.
Fig. 3 (a) is the profile of slab, and Fig. 3 (b) is the profile of product.
Fig. 4 is the profile of slab.
Fig. 5 is the figure in the tune Check faces for illustrating slab.
Fig. 6 shows the threshold value determination result of the first embodiment of embodiment, is the Ca concentration for representing molten steel in tundish CaTD1With the Ca concentration Cs a of slabS1And the figure of the relation of HIC result of the tests.
Fig. 7 shows the threshold value determination result of the second embodiment in embodiment, is to represent that the Ca of molten steel in tundish is dense Spend CaTD1With the minimum value Ca of the Ca concentration of slabmin1And the figure of the relation of HIC result of the tests.
Embodiment
The present inventors, study with keen determination repeatedly in order to solve the problem.First the present inventors to be conceived to HIC easy Occur by starting point of MnS field trashes.Its result is expected, by making to contain the rare earth as the element with desulfidation in steel Dvielement or Zr, can suppress MnS generation, improve hydrogen induced cracking resistance.In addition, in order to effectively play the desulfidation, Its aftermentioned appropriate content is also found.
Secondly, the present inventors are also conceived to, and the CaO aggregations portion produced when HIC is easily manufactured using slab occurs as starting point. Its result finds, if focus on evaluating whether there is CaO aggregations portion " subtract slab from the Ca concentration of molten steel in tundish Ca concentration obtained by Ca decrements ", in the stage of slab, by the Ca decrements bring into as defined in below threshold value, then can The high steel plate of hydrogen induced cracking resistance is obtained, is furthermore possible to make product deliver goods as early as possible.It is described in detail after relevant this point.
Illustrated firstly for composition composition.Further, following quantity relating, " % " means " quality % ", " ppm " meaning Think of is " quality ppm ".
In order to ensure excellent hic resistance, it is necessary to control the composition of steel to constitute.In addition, for example as line-pipes steel Other characteristics required by material, in order to ensure high intensity and excellent weldability etc., it is also desirable to make the composition of steel plate constitute such as It is following.Hereinafter, headed by foregoing REM and Zr, the regulation reason for each composition is illustrated.
(composition composition)
[C：0.02~0.15%]
C be for ensuring that the integral element required for the intensity of mother metal and weld part, it is necessary to be allowed to containing More than 0.02%.C amounts are preferably more than 0.03%, more preferably more than 0.05%.On the other hand, if C amounts are excessive, HAZ is tough Property and weldability deterioration.If other C amounts are superfluous, hold as HIC starting point and the NbC and island-like martensite in destruction progress path Easily generation.Therefore C amounts are needed for less than 0.15%.Preferably less than 0.12%, more preferably less than 0.10%.
[Si：0.02~0.50%]
Si has deoxidation, and is effective element for the intensity raising of mother metal and weld part.In order to obtain this A little effects, it is more than 0.02% to make Si amounts.Si amounts are preferably more than 0.05%, more preferably more than 0.15%.But, if Si amounts Excessively, then weldability and toughness deterioration.If other Si amounts are superfluous, island-like martensite generation, HIC is in progress.Therefore Si Amount needs to suppress below 0.50%.Si amounts are preferably less than 0.45%, more preferably less than 0.35%.
[Mn：0.6~2.0%]
It is effective element that Mn is improved for the intensity of mother metal and weld part, is allowed in the present invention containing more than 0.6%. Mn amounts are preferably more than 0.8%, more preferably more than 1.0%.But, if Mn amounts are excessive, MnS is generated, not only resistant to hydrogen fracturing Line is deteriorated, and HAZ toughness and weldability are also deteriorated.Therefore the upper limit for making Mn amounts is 2.0%.Mn amounts be preferably 1.8% with Under, more preferably less than 1.5%, more preferably less than 1.2%.
[P：Higher than 0% and below 0.030%]
P be in steel unavoidably by comprising element, if P amounts are higher than 0.030%, the toughness in mother metal and HAZ portions Deterioration is notable, and hydrogen induced cracking resistance is also deteriorated.Therefore in the present invention, P amounts are suppressed below 0.030%.P amounts are preferably Less than 0.020%, more preferably less than 0.010%.
[S：Higher than 0% and below 0.003%]
If S is excessive, a large amount of generation MnS, it is the element for making hydrogen induced cracking resistance significantly deteriorate, therefore in the present invention In, the upper limit for making S amounts is 0.003%.S amounts are preferably less than 0.002%, more preferably less than 0.0015%, further preferably For less than 0.0010%.Like this from the viewpoint of hydrogen induced cracking resistance raising, it is desirable to be the few methods of S.
[Al：0.010~0.08%]
Al is strong deoxidant element, if Al amounts are few, the Ca concentration in oxide rises, i.e. Ca systems field trash is by easy shape Into in steel plate skin section, fine HIC occurs.Therefore in the present invention, it is necessary to make Al be more than 0.010%.Al amounts are preferably More than 0.020%, more preferably more than 0.030%.On the other hand, if Al content is excessive, Al oxide cluster-shaped generation And the starting point as hydrogen induced cracking.Therefore Al amounts are needed for less than 0.08%.Al amounts are preferably less than 0.06%, more preferably Less than 0.05%.
[Ca：0.0003~0.0060%]
Ca has the effect of the form of control sulfide, by forming CaS, the effect with the formation for suppressing MnS.In order to This effect is obtained, it is necessary to make Ca amounts be more than 0.0003%.Ca amounts are preferably more than 0.0005%, more preferably 0.0010% More than.On the other hand, if Ca amounts largely occur higher than 0.0060%, HIC using Ca systems field trash as starting point.Therefore in the present invention In, the upper limit for making Ca amounts is 0.0060%.Ca amounts are preferably less than 0.0045%, more preferably less than 0.0035%, further Preferably less than 0.0025%.
[N：0.001~0.01%]
N is separated out in structure of steel as TiN, is suppressed the coarsening of the austenite crystal in HAZ portions, is additionally promoted ferrite Phase transformation, is the element for improving the toughness in HAZ portions.In order to obtain this effect, it is necessary to make N contain more than 0.001%.N amounts are excellent Elect more than 0.003%, more preferably more than 0.0040% as.If but N amounts are excessive, due to solid solution N presence, HAZ toughness Deteriorate on the contrary, therefore N amounts are needed for less than 0.01%.Preferably less than 0.008%, more preferably less than 0.0060%.
[O：Higher than 0% and below 0.0045%]
From the viewpoint of cleanliness factor is improved, it is desirable to aspect low O (oxygen), O is largely contained sometimes, except toughness is bad Beyond change, HIC, hydrogen induced cracking resistance deterioration can also occur by starting point of oxide.From this viewpoint, O amounts needs are Less than 0.0045%, preferably less than 0.0030%, more preferably less than 0.0020%.
[Ca/S (mass ratio)：More than 2.0]
It has been observed that S forms MnS as sulfide-based field trash, HIC occurs by starting point of the MnS.Therefore, Ca is added, Sulfide-based field trash in steel is controlled into form as CaS, to realize S for the innoxious of hic resistance.In order to fully send out The action effect is waved, it is necessary to make Ca/S be more than 2.0.Ca/S is preferably more than 2.5, and more preferably more than 3.0.Further, according to Ca amounts specified in the present invention and S amounts, the Ca/S upper limit is 17 or so.
[(Ca-1.25S)/O≤1.80]
Occur to suppress the HIC caused by Ca systems oxysulfide, effectively suppress also special among Ca systems field trash The fit CaO of aggegation is not formed not easily.Then therefore, subtracting the Ca amounts existed as sulfide (CaS) in total Ca amounts from steel Ca amounts (Ca-1.25S) afterwards, it is necessary to make it not superfluous relative to O amounts.If Ca amounts (Ca-1.25S) are superfluous relative to O amounts, CaO is easily then formed as oxide system field trash, the aggegation fit (thick Ca systems field trash) of the CaO is easily in steel plate Skin section is largely formed.These thick Ca systems field trashes turn into HIC starting point, therefore in order to obtain excellent hic resistance, need It is less than 1.80 to make (Ca-1.25S)/O.(Ca-1.25S)/O is preferably less than 1.40, and more preferably less than 1.30, enter one Step is preferably less than 1.20, particularly preferably less than 1.00.Further, from suppression easily formation aggegation zoarium same with CaO Al2O3From the viewpoint of, (Ca-1.25S)/O lower limit is 0.1 or so.
[REM：Higher than 0% and below 0.02%]
REM (Rare Earth Metal, rare earth element), it has been observed that suppress MnS generation using desulfidation, it is right It is effective element in improving hydrogen induced cracking resistance.In order to play such effect, preferably REM is set to contain more than 0.0002%. REM amounts are more preferably more than 0.0005%, more preferably more than 0.0010%.On the other hand, even if largely containing REM Have, effect is also saturation.Therefore the upper limit of REM amounts is needed for 0.02%.From the blocking of submersed nozzle when suppressing casting, carry From the viewpoint of high production rate, it is less than 0.015%, more preferably less than 0.010% preferably to make REM amounts, more preferably Less than 0.0050%.Further, in the present invention, above-mentioned so-called REM, mean lanthanide series (15 kinds of elements from La to Lu) with Sc (scandium) and Y (yttrium).
[Zr：Higher than 0% and below 0.010%]
Zr improves hic resistance by desulfidation, and forms oxide and imperceptibly disperse, and contributes to HAZ tough Property improve element.In order to play these effects, it is more than 0.0003% preferably to make Zr amounts.Zr amounts be more preferably 0.0005% with On, more preferably more than 0.0010%, it is still more preferably more than 0.0015%.On the other hand, if add superfluously Zr, then form thick field trash, deteriorates hydrogen induced cracking resistance and base metal tenacity.Therefore Zr amounts are needed for less than 0.010%. Zr amounts are preferably less than 0.0070%, more preferably less than 0.0050%, more preferably less than 0.0030%.
The composition of the steel (steel plate, steel pipe) of the present invention, as described above, surplus is made up of iron and inevitable impurity.Separately Outside, in addition to above-mentioned element,
(a) by again containing selected in the group that is constituted from B, V, Cu, Ni, Cr, Mo and Nb of following amounts more than one Element, then can further improve intensity and toughness, or,
(b) by containing more than one the element selected in the group constituted from the Ti and Mg of following amounts, then can again HAZ toughness is improved, and promotes desulfurization and further improves hic resistance.Hereinafter, it is described in detail for these elements.
[B：Higher than 0% and below 0.005%]
B improves hardenability, improves the intensity of mother metal and weld part, and in welding, cooled down in heated HAZ portions During combined with N and separate out BN, promote from the ferrite transformation of austenite crystal intragranular, therefore improve HAZ toughness.To be terrible To this effect, B amounts are preferably made to contain more than 0.0002%.B amounts are more preferably more than 0.0005%, more preferably More than 0.0010%.But, if B content is excessive, the toughness deterioration in mother metal and HAZ portions, or cause the deterioration of weldability, therefore B amounts are preferably less than 0.005%.B amounts are more preferably less than 0.004%, more preferably less than 0.0030%.
[V：Higher than 0% and below 0.1%]
V is effective element for the raising of intensity, in order to obtain this effect, is preferably allowed to containing more than 0.003%. More preferably more than 0.010%.On the other hand, if V content is higher than 0.1%, weldability and base metal tenacity are deteriorated.Therefore V amounts Preferably less than 0.1%, more preferably less than 0.08%.
[Cu：Higher than 0% and below 1.5%]
Cu improves hardenability, is effective element for improving intensity.In order to obtain this effect, preferably contain Cu More than 0.01%.Cu amounts are more preferably more than 0.05%, more preferably more than 0.10%.But, if Cu contents are higher than 1.5%, then toughness deterioration, therefore preferably less than 1.5%.Cu amounts are more preferably less than 1.0%, more preferably 0.50% Below.
[Ni：Higher than 0% and below 1.5%]
Ni is effective element for the raising of mother metal and the strength and toughness of weld part.It is excellent in order to obtain this effect Choosing makes Ni amounts be more than 0.01%.Ni amounts are more preferably more than 0.05%, more preferably more than 0.10%.But, if greatly Amount contains Ni, then extremely expensive as structural steel, therefore from the viewpoint of economy, Ni amounts are preferably less than 1.5%. Ni amounts are more preferably less than 1.0%, more preferably less than 0.50%.
[Cr：Higher than 0% and below 1.5%]
Cr is effective element for the raising of intensity, in order to obtain this effect, is preferably allowed to containing more than 0.01%. Cr amounts are more preferably more than 0.05%, more preferably more than 0.10%.On the other hand, if Cr amounts are higher than 1.5%, HAZ Toughness is deteriorated.Therefore Cr amounts are preferably less than 1.5%.Cr amounts be more preferably less than 1.0%, more preferably 0.50% with Under.
[Mo：Higher than 0% and below 1.5%]
Mo is effective element for the raising of the intensity and toughness of mother metal.In order to obtain this effect, preferably make Mo amounts For more than 0.01%.Mo amounts are more preferably more than 0.05%, more preferably more than 0.10%.But, if Mo amounts are higher than 1.5%, then HAZ toughness and weldability deterioration.Therefore Mo amounts are preferably less than 1.5%, more preferably less than 1.0%, further Preferably less than 0.50%.
[Nb：Higher than 0% and below 0.06%]
Nb will not deteriorate weldability, and be effective element for improving intensity and base metal tenacity.In order to obtain this Effect, it is more than 0.002% preferably to make Nb amounts.Nb amounts are more preferably more than 0.010%, more preferably more than 0.020%. But, if Nb amounts are higher than 0.06%, mother metal and HAZ toughness deterioration.Therefore, in the present invention, it is preferred to make the upper limit of Nb amounts For 0.06%.Nb amounts be more preferably less than 0.050%, more preferably less than 0.040%, still more preferably for Less than 0.030%.
[Ti：Higher than 0% and below 0.03%]
Ti is separated out in steel as TiN, the coarsening of the austenite crystal in HAZ portions when preventing from welding, and promotes iron Ferritic phase transformation, therefore be effective element for improving the toughness in HAZ portions.In addition, because Ti also shows desulfidation, institute It is also effective element with the raising for hic resistance.In order to obtain these effects, preferably Ti is set to contain more than 0.003%.Ti Amount more preferably more than 0.005%, more preferably more than 0.010%.On the other hand, if Ti contents become excessive, by The toughness in mother metal and HAZ portions is caused to deteriorate in solid solution Ti increase and the TiC increase separated out, therefore preferably less than 0.03%. Ti amounts are more preferably less than 0.02%.
[Mg：Higher than 0% and below 0.01%]
It is effective element that Mg is improved in toughness in the miniaturization by crystal grain, additionally shown is desulfidation, because This is also effective element in the raising of hic resistance.In order to obtain these effects, preferably Mg is set to contain more than 0.0003%. Mg amounts are more preferably more than 0.001%.On the other hand, even if containing Mg superfluously, its effect is also saturation, therefore Mg amounts is upper Limit is preferably 0.01%.Mg amounts are more preferably less than 0.005%.
The steel plate of the present invention is the high steel plate of hydrogen induced cracking resistance, and the Ca concentration of molten steel subtracts the Ca of slab out of tundish Ca decrements are in threshold value Ca obtained by concentrationdropθBelow.So-called threshold value Ca hereindropθ, mean try to achieve in advance, rolling institute The maximum Ca decrements of hydrogen induced cracking do not occur for steel plate obtained from stating slab.
[Ca decrements]
As described above, by making the Ca concentration of the molten steel out of tundish subtract Ca decrements obtained by the Ca concentration of slab in rule Below fixed threshold value, the high steel plate of hydrogen induced cracking resistance just can be obtained, additionally is able to make product deliver as early as possible, this is said It is bright.Hereinafter, first from using above-mentioned Ca decrements as evaluation index the reasons why, proceeds by explanation.
The present inventors are conceived to after MnS field trashes, in order to suppress MnS generation, on via double refining by Ca It is added in molten steel and is studied.
Additions of the Ca into molten steel in molten steel where appropriate, generate CaO-Al2O3Field trash.Because CaO-Al2O3With The wetability of molten steel is good, thus will not the aggegation in molten steel, but fine state is presented, hic resistance will not be caused not Profit influence.
But, when additions of the Ca into molten steel is incorrect, for example, having exceeded suppression and the Al of MnS generations2O3Modification Required allowance and when having carried out the addition of surplus, then in molten steel, except CaO-Al2O3Beyond field trash, also generate Pure CaO field trashes.Pure CaO field trashes are because poor with the wetability of molten steel, the easy aggegation in molten steel.Aggegation The CaO of merging turns into thick field trash and induces HIC.
The CaO field trashes of coarsening, because its density ratio molten steel is small, most float separation.But, as shown in figure 1, One part is while as the molten steel stream in mold is drilled into the depths of slab, while by buoyancy, being solidified shell and catching and shape Into CaO accumulation zones.CaO accumulation zones turn into HIC starting point.
Therefore, if predetermining appropriate additions of the good Ca into molten steel, it can suppress because CaO field trashes cause HIC occur.It is mingled with object amount and its composition and sulphur concentration for this reason, it may be necessary to hold exactly in the molten steel before Ca additions.But In practical operation, and these can not possibly be held in advance, therefore make Ca additions be sufficient for suppressing MnS generations Amount.As a result, Ca additions are easily superfluous, CaO accumulation zones are easily formed.
If above-mentioned CaO accumulation zones always occur in same position, by analyzing the Ca concentration of this position, just can Hold the concentration class of CaO field trashes.In addition, whether according to CaO concentration class, can speculate has CaO accumulation zones in slab.
But the position that CaO accumulation zones occur, it has been observed that according to the casting condition (row of casting speed and submersed nozzle Angle portalled etc.) it is different and different on the thickness direction of slab.For example, as shown in Fig. 2 in casting condition (casting The angle of the tap of speed and submersed nozzle) in different 3 slabs (A~C), the position for the high Ca concentration that accumulation zone occurs Put (a~c) different.In this way, because the position of CaO accumulation zones can not be predicted, being evaluated according to concentration class (Ca concentration) Whether CaO accumulation zones have any problem.
Therefore the present inventors change viewpoint on the tune Check positions of Ca concentration, are conceived to the position of low Ca concentration.If CaO accumulation zones occur, then in CaO accumulation zones, Ca concentration is uprised, on the other hand, the position not occurred in CaO accumulation zones, then Think that Ca concentration ratios are relatively low.While this point is considered, while " the arbitrary thickness side of slab when investigation CaO accumulation zones occur To the Ca concentration of position " with the relation of " the Ca concentration of molten steel in tundish ".Its result is understood, in no generation CaO accumulation zones Position, therefore " the Ca concentration of slab " " subtract ' the Ca concentration of slab than relatively low from ' the Ca concentration of molten steel in tundish ' Value ' ", i.e. " the Ca concentration reduction levels from tundish to slab " become big.
So, when described " the Ca concentration reduction levels from tundish to slab " are big, it is believed that do not gather in the position Collect band, but there are CaO accumulation zones in other position, therefore, it is possible to be evaluated as HIC.On the other hand, it is described " from tundish To the Ca concentration reduction levels of slab " hour, the Ca concentration of tundish and the Ca concentration of slab are almost without difference, that is, can It is speculated as, does not have the position of high Ca concentration in slab.In this case, it is believed that without occurring CaO accumulation zones in slab, therefore HIC, which can be evaluated as, to be occurred.
In the present invention, so subtracted using associated with whetheing there is CaO accumulation zones from " the Ca concentration of molten steel in tundish " The value (hereinafter referred to as " Ca decrements ") of " the Ca concentration of slab " is gone, hic resistance is evaluated.
[decision of the threshold value of Ca decrements]
Next, whether the steel plate being just used for obtained by judging plays the Ca decrements of excellent hic resistance Threshold value Cadropθ, i.e. what HIC maximum Ca decrements did not occurred for steel plate obtained from rolled slab asks method to illustrate.
Above-mentioned threshold value CadropθIt can try to achieve in advance, but its method is not particularly limited.As trying to achieve threshold value CadropθSide Method, can enumerate and be tried to achieve in advance in following (i)~(iii) method.
(i) the Ca concentration and the Ca concentration of slab of molten steel in tundish are measured, from the Ca concentration of molten steel in the tundish The Ca concentration of the slab is subtracted, Ca decrements are calculated.
(ii) rolling carries out hydrogen in the slab with being cast under the slab identical casting condition for resulting steel plate Cause cracking test.
(iii) according to the Ca decrements and the hydrogen induced cracking result of the test of above-mentioned (ii) measured in above-mentioned (i), try to achieve The maximum Ca decrements that hydrogen induced cracking does not occur.
As trying to achieve above-mentioned threshold value CadropθMethod, specifically by taking following first embodiments and second embodiment as an example, It is described below.
(first embodiment)
(the tune Check of the Ca concentration of molten steel in tundish)
Molten steel in tundish is extracted, its Ca concentration (Ca is analyzedTD1).Because molten steel is supplied often from coating is poured in tundish, So Ca concentration (CaTD1) no matter extraction time is all constant.
(the tune Check of the Ca concentration of slab)
Then, the Ca concentration (Ca of slab is investigatedS1).As shown in Fig. 3 (a), from slab away from benchmark side surface in thickness side The region R4 (hereinafter referred to as " benchmark side region R4 ") of upward D/2 scope extracts sample, analysis Ca concentration Cs aS1." reference side Region R4 ", is the scope away from anti-benchmark side surface more than D/2 and below D on the thickness direction of slab such as shown in Fig. 3 (a).
It has been observed that because the density of the density ratio molten steel of CaO field trashes is small, the CaO field trashes in molten steel by with Buoyancy caused by the density contrast of molten steel and float.In the continuous casting machine of bending section and horizontal part is formed with, as shown in figure 1, If CaO field trashes float, caught by the solidified shell of anti-reference side, therefore CaO accumulation zones occur in the anti-reference side of slab, Reference side does not occur.
Therefore in the present invention, such as above-mentioned Fig. 3 (a), away from CaO accumulation zones do not occur " away from benchmark side surface in thickness side In upward D/2 scope (benchmark side region R4) ", i.e., embodiment described later, in the centrally directed reference side table from slab thickness D Ca concentration Cs a is investigated to -0.50D scope in faceS1.According to benchmark side region R4 Ca concentration Cs aS1, CaO can be calculated and gathered " Ca decrement " of the collection band without the position occurred, CaO accumulation zones are whether there is therefore, it is possible to evaluate exactly.
Then, from " the Ca concentration Cs a in tundishTD1" subtract " the Ca concentration Cs a of slabS1", calculate " Ca decrements Cadrop1”。Cadrop1It is expressed from the next.
Cadrop1=CaTD1- CaS1
(rolling)
Hot rolling is with measuring above-mentioned Ca concentration Cs aS1Slab identical casting condition under block, manufacture threshold value survey The steel plate of amount.It can for example enumerate and be rolled by following condition.That is, heat above-mentioned slab and make up to 1050~1250 DEG C Afterwards, more than 900 DEG C are calculated as with the surface temperature of steel plate, it is such as following by calculating the steel plate mean temperature tried to achieve more than 1000 DEG C Accumulation reduction ratio be more than 40%, and make mill train that the reduction ratio of every a time is more than 10% more than two passages to enter Row hot rolling.Thereafter, hot rolling then by 700 DEG C less than 900 DEG C of accumulation reduction ratio is carried out in the way of more than 20%, makes to roll End temp processed is 700 DEG C less than 900 DEG C.Thereafter, the water cooling since more than 650 DEG C of temperature, at 350~600 DEG C At a temperature of stop, afterwards, then be air-cooled to room temperature.Above-mentioned steel plate mean temperature is tried to achieve as follows.Namely based in rolling The data of cooling means (water cooling or air cooling) between mill train table and passage etc., the method for being suitable to calculate with calculus of finite differences etc. is calculated The temperature of the arbitrary position in thickness of slab direction, regard the average value of the temperature at the surface from steel disc to the back side tried to achieve as steel plate Mean temperature.
(HIC experiments)
Then, HIC experiments are carried out for steel plate, investigation whether there is HIC., can shown in the embodiment of HIC experiments as be described hereinafter Enumerate the method progress with NACE standard TM0284-2003 defineds.
The subject area of the HIC experiments, is the article areas R40 corresponding to anti-benchmark side region shown in such as Fig. 3 (b) Among remove the region R41 of mid-depth portion neighborhood.This is due to that as described shown in Fig. 1, the CaO accumulation zones of coarsening easily exist The anti-reference side of slab is formed, the HIC caused by CaO, is easily occurred in the region corresponding to anti-reference side neighborhood.Further, Easily occurs the HIC caused by segregation in mid-depth portion, so the HIC due to CaO can not be evaluated as.Therefore, removing Whether the region R41 investigation HIC of mid-depth portion neighborhood occurs.
(decision of threshold value)
Then, according to " the Ca decrements Cadrop1" and " HIC result of the tests ", determine the Ca decrements that HIC does not occur Threshold value Cadropθ.Contrast multiple Ca decrements Cadrop1With HIC result of the tests, maximum Ca when HIC is not occurred completely is reduced Amount is used as " threshold value Cadropθ”.Especially by the measurement result and result of the test using multiple slabs, it can obtain more accurately Threshold value, can reduce the erroneous judgement whether HIC occurs.
(second embodiment)
Next, one side reference picture 4, while the computational methods for Ca decrements are different from the first embodiment Second embodiment is illustrated.Then explanation is simplified for being constituted with above-mentioned first embodiment identical.In addition in institute State in Fig. 4, identical symbol is also used for being constituted with above-mentioned first embodiment identical, and suitably the description thereof will be omitted.
(the tune Check of the Ca concentration of molten steel in tundish)
Investigate the Ca concentration (Ca of molten steel in tundishTD1)。
(the tune Check of the Ca concentration of slab)
Then, in the slab cast with same furnace charge, as shown in figure 4, thickness direction it is different 2 at more than tune Check Sample is extracted in position, analyzes the Ca concentration of each sample.From the Ca concentration (Ca of resulting more than 2S1、CaS2...) middle selection is most Small Ca concentration (Camin1)。
Then, using from " the Ca concentration Cs a in tundishTD1" in subtracted " the minimum Ca concentration Cs a of slabmin1" value, Calculate " Ca decrements Cadrop11”。Cadrop11It is expressed from the next
Cadrop11=CaTD1- Camin1
In the gamut of the thickness direction of slab, when the tune Check positions for making Ca concentration are at 1, if the position is aggregation Band, then can detect that substantially high Ca concentration.Because the Ca decrements calculated by high Ca concentration are small, it is judged as not sending out Raw CaO accumulation zones, are evaluated as not occurring HIC.However, it is possible to think actually there is accumulation zone, HIC can occur it is positive because in This.
Therefore in the present embodiment, different 2 on the thickness direction of slab at more than position investigation Ca concentration.Cause It is present in the specific thickness direction position determined by casting condition for CaO accumulation zones, so by changing in a thickness direction Check positions are adjusted, just can make not occur CaO accumulation zones position to be included in and adjust in Check objects.
In addition, the Ca concentration (Ca of more than 2S1、CaS2...) in, the Ca concentration comprising accumulation zone and no generation accumulation zone Position Ca concentration, but pass through selection wherein minimum Ca concentration (Camin1), it just can select and not occur accumulation zone The Ca concentration of position.Concentration can calculate the Ca decrements on the position that accumulation zone does not occur accordingly, therefore, it is possible to exactly Evaluate the presence or absence of CaO accumulation zones.
Here, in the formation mechanism of CaO accumulation zones, CaO field trashes and Al2O3Field trash is identical, Al2O3Field trash it is poly- The thickness of collection band is reported as 10mm (documents：ISIJ International, Vol.43 (2003), No.10, p.1548- 1555).Report can speculate that the thickness of the accumulation zone of CaO field trashes is also 10mm accordingly.So, if as shown in figure 4, making Ca dense Each tune Check positions of degree in a thickness direction separately must be longer than 10mm, even if then adjusting one of Check positions to be accumulation zone, others are adjusted Check positions also can be the position for not having accumulation zone.For this reason, at 2 more than tune Check positions, preferably exist respectively Interval is more than 10mm on thickness direction.Further, in Fig. 4, represent to make tune Check positions be the thickness direction of 2 tune Check positions at 2 Situation apart from l higher than 10mm (2 are adjusted the thickness direction of Check positions apart from l ＞ 10mm).
In addition as shown in figure 1, in the bending section neighborhood of casting path, CaO field trashes are captured on a large scale, therefore in Fig. 4 In the shown width two ends D/2 away from slab region R1, R2, CaO accumulation zones occur on a large scale in a thickness direction.Cause This, in region R1, R2, the tune Check positions of Ca concentration is changed even in thickness direction, accumulation zone can not be investigated and do not send out by still suffering from The possibility of raw position.Therefore, make Ca concentration adjust the Check positions to be preferably, it is main only leniently surface side it is cooled, from width side D/2 width W-D region R3 is removed to two ends.
(rolling)
Hot rolling is with measuring above-mentioned Ca concentration Cs aS1Deng slab identical casting condition under the slab that casts, manufacture threshold It is worth measuring steel plate..
(HIC experiments)
Then HIC experiments are carried out for steel plate, " the region R41 " corresponding to anti-reference side neighborhood whether there is HIC hairs for investigation It is raw.HIC is tested, and shown in embodiment as be described hereinafter, can be enumerated in the method for NACE standard TM0284-2003 defineds Carry out.
(decision of threshold value)
Then, according to " Ca decrements Cadrop11" and " HIC result of the tests ", determine the threshold for the Ca decrements that HIC does not occur Value Cadropθ.In the present embodiment, maximum Ca decrements when HIC is not occurred completely are " threshold value Cadropθ”。
[measurement of the Ca decrements of determine object furnace charge]
Adjust the Ca concentration Cs a of molten steel in the tundish of Check determine object furnace chargesTD11.For example it is same with the second embodiment Sample, in the slab cast by same furnace charge, to investigating Ca concentration, the Ca more than 2 more than on thickness direction different 2 Concentration (CaS11、CaS12...) the minimum Ca concentration (Ca of middle selectionmin11).Tune Check positions more than at 2, respectively preferably in thickness side Being spaced upwards must be longer than 10mm.
Then, from " the Ca concentration Cs a in tundishTD11" subtract " the minimum Ca concentration Cs a of slabmin11", calculate judgement pair " the Ca decrements Ca of elephantdrop”。CadropIt is expressed from the next.
Cadrop=CaTD11- Camin11
[evaluation of the Ca decrements of determine object furnace charge]
Contrast the Ca of above-mentioned determine objectdropWith threshold value Cadropθ, CadropIn threshold value CadropθWhen following, resulting steel Plate is judged as that hic resistance is excellent, CadropHigher than threshold value CadropθWhen, resulting steel plate is judged as that hic resistance is poor.
The tune Check positions (adjusting Check faces) of slab are preferably constant region but it is also possible to be non-constant area.So-called " non-constant area ", It is exactly the part that casting condition is cast in change, so-called casting initial stage when casting speed rises, and casting speed can be set forth in Part of casting of so-called casting latter stage during the decline of degree etc..When adjusting Check in non-constant area, as shown in figure 5, it is preferred that adjusting Check and reality Apply the part of the position adjoining of HIC experiments.Because this part shows the hic resistance same with HIC result of the tests, can More accurately evaluated.
The present invention steel plate, be as its rolling before state slab stage, subtract from the Ca concentration in tundish The Ca concentration of slab is gone, " Ca decrements Ca is calculateddrop", " Ca decrements Cadrop" meet Cadrop≤ threshold value CadropθSteel plate. The steel plate of the present invention, meets above-mentioned Cadrop≤ threshold value Cadropθ, it is believed that without generation CaO accumulation zones in slab, therefore HIC will not Occur.
In this way, in the present embodiment, the evaluation of hic resistance uses " the Ca concentration reduction levels from tundish to slab ". Because hereby it is possible to the inside quality (concentration class of CaO field trashes) of accurate evaluation slab, can using the evaluation result as Basis and in the Phase Evaluation hic resistance of slab.Thereby, it is possible to omit the HIC experiments for needing to spend several weeks, so can be significantly Shorten from the cycle for being fabricated onto delivery.
The application advocate based on Japan's patent application filed in 26 days December in 2014 the 2014-266491st and The interests of the priority of Japan's patent application filed in 13 days October in 2015 the 2015-202378th.December 26 in 2014 The full content of the specification of Japan's patent application the 2014-266491st filed in day and everyday Shen October 13 in 2015 Please Japan's patent application the 2015-202378th specification full content, quoted for the reference of the application.
Embodiment
Hereinafter, enumerate embodiment and further illustrate the present invention, but the present invention is not limited by following embodiments certainly, in energy Enough meet the scope of the forward and backward objective stated, naturally it is also possible to suitably changed implementation, these are all contained in the technology of the present invention In the range of.
(1) cast
In table 1-1~table 4 and Fig. 6,7, the experiment condition and experimental result for decision threshold are shown.By continuous Casting, obtains slab thickness D for 280mm, and width of plate slab W is 2100mm slab.The casting condition of first embodiment is shown In table 1-1 and table 1-2, the casting condition of second embodiment is shown in table 2-1 and table 2-2.In the present embodiment, In order to obtain X65 grades of API (The American Petroleum Institute) steel plate, and APIX70 grades of steel plate, point Not carry out 25 batches of furnace charges manufacture.
Mutual, illustrate the condition shown in table 1-1, table 1-2, table 2-1 and table 2-2.
The composition ＞ of molten steel in ＜ tundish
C, Mn, Nb, P, Ca concentration are measured by emission spectrometry method.Because S concentration is low, by emission spectrum point Analysis method measures difficulty.Therefore, the measurement of S concentration uses burning-infrared absorption.
＜ casting conditions ＞
Specific water
Specific water=(from mold underface to total secondary cooling water [L/ of the unit interval of conticaster finishing roll Min.])/(the casting slab quality [kg/min.] of unit interval)
Casting speed
On the drawing speed [m/min.] of slab, according to the roller (home roll contacted with slab：メ ジ ャ ー ロ ー Le) Diameter (girth) is calculated with rotating speed (rotating speed of unit interval).
(2) the tune Check of Ca decrements
The Ca concentration Cs a of molten steel in the molten steel in tundish, investigation tundish is extracted for the 10m moment in the total length of slabTD1。 After casting, the Ca concentration Cs a of Check slabs is adjustedS1Or Camin1.In table 1-1 and table 1-2, the benchmark side region R4 of slab is shown in Tune Check positions and Ca concentration Cs a during investigation Ca concentrationS1.In table 3-1, table 3-2 and table 4, the thickness direction of slab is shown in At different 2~10 (total N number=2~10 shown in table 3-1, table 3-2 and table 4) investigate Ca concentration when tune Check positions and Ca concentration everywhere.Among table 3-1, table 3-2 and table 4, experiment No.51~57,69~100 are measured at 2.Experiment No.58~64 are investigated at 3~8 respectively, and experiment No.65~68 are adjusted at Check 10.Then show the minimum Ca among multiple Ca concentration Concentration (Ca minimums).It is the position that interval exceedes 10mm in a thickness direction respectively at described 2~10.
[table 1-1]
[table 1-2]
[table 2-1]
[table 2-2]
[table 3-1]
[table 3-2]
[table 4]
*：It is just (-) towards benchmark side surface just (+) to be towards anti-benchmark side surface from mid-depth
(3) roll
Thereafter, above-mentioned slab is heated to make up to after 1050~1250 DEG C, with the surface temperature of steel plate be calculated as 900 DEG C with On, such as following is more than 40% by calculating accumulation reduction ratio of the steel plate mean temperature tried to achieve more than 1000 DEG C, and is made Per a time reduction ratio be more than 10% mill train more than two passages to carry out hot rolling, thereafter, then with more than 700 DEG C and Accumulation reduction ratio less than 900 DEG C carries out hot rolling for more than 20% mode, rolling is terminated surface temperature for 850 DEG C.Afterwards, The surface temperature since cooling：950 DEG C are risen, with average cooling rate：10 DEG C/s is begun to cool down, and is stopped in 350~600 DEG C of temperature Only, hereafter, then be air-cooled to room temperature, obtain being made up of various composition, size be 9~50mm thickness of slab × 2000~3500mm it is wide × The steel plate of 12000~35000mm length.
(4) HIC is tested
For decision threshold t θ, in the present embodiment, HIC experiments are carried out after rolling.
(a) sample is cut from each steel plate after rolling, implements HIC experiments.HIC experiments follow NACE standard The method of TM0284-2003 defineds is implemented.
(b) after HIC experiments, sample is cut off at 3, with each section of micro- sem observation (3 sections), confirmation whether there is HIC.See It is " in article areas R40 " corresponding with anti-benchmark side region, to remove the mid-depth away from product shown in Fig. 3 (b) to examine region Along the region R41 of the scope of thickness of slab ± 5.3%.
(5) decision of the threshold value of Ca decrements
Fig. 6 shows the threshold value determination result of first embodiment, and Check " molten steel in tundish is adjusted in (2) described in expression Ca concentration Cs aTD1" and table 1-1 and table 1-2 " the Ca concentration Cs a of slabS1", the relation with HIC result of the tests.Other Fig. 7 shows Show the threshold value determination result of second embodiment, Check " the Ca concentration Cs a of molten steel in tundish is adjusted in (2) described in expressionTD1" and The minimum Ca concentration Cs a of table 3-1, table 3-2 and table 4 slabmin1, the relation with HIC result of the tests.
According to described Fig. 6, in the decision method of first embodiment, when Ca decrements are below 4ppm, HIC is not sent out It is raw.On the other hand, when Ca decrements are higher than 4ppm, the situation of HIC generations and situation about not occurring mix.Thus result can Know, HIC generations can be suppressed really, when being Ca decrements≤4ppm.Therefore, will in the embodiment of first embodiment The threshold value of Ca decrements is used as 4ppm, i.e. Cadropθ=4ppm.
In addition, according to Fig. 7, in the decision method of second embodiment, when to be also Ca decrements be below 4ppm, HIC Do not occur.On the other hand, when Ca decrements are higher than 4ppm, the situation that HIC occurs mixes with situation about not occurring.Thus result Understand, HIC generations can be suppressed really, when being Ca decrements≤4ppm.Therefore, in the embodiment of second embodiment, Also it regard the threshold value of Ca decrements as 4ppm, i.e. Cadropθ=4ppm.
Further, " threshold value of Ca decrements " is unrelated with intensity level, is determined completely by product.Because thick CaO is easy The degree for causing HIC to occur, the intensity level with product is not related.
(6) evaluation of determine object slab
Use above-mentioned threshold value, the hic resistance of the determine object slab of the composition composition shown in evaluation table 5.
The steel of composition composition shown in melting table 5, by continuously casting, obtains slab thickness D for 280mm, width of plate slab W For 2100mm slab.
Investigate the Ca concentration Cs a of molten steel in the tundish of determine object furnace chargeTD11, and try to achieve the slab of determine object Minimum Ca concentration (Camin11), the Ca decrements Ca of the slab of determine object is calculated in the above described mannerdrop.Then, using by upper State the threshold value Ca that first and second embodiment of (5) is tried to achievedropθ=4ppm, the Ca decrements Ca of the slab of determine objectdropFor Below 4ppm when, HIC does not occur caused by CaO, i.e. hic resistance evaluation is judged as OK, Ca decrements CadropIt is higher than During 4ppm, HIC caused by CaO occurs, i.e. hic resistance evaluation is judged as NG.The result is shown in table 6.
Thereafter, heat above-mentioned slab to make up to after 1050~1250 DEG C, in " hot rolling cooling means " column of table 6 As being shown as " TMCP " or " QT ", by the hot rolling cooling means of 2 patterns, the steel plate (9 of various composition composition is obtained ~90mm thickness of slab × 2000~3500mm is wide × 12000~35000mm length)." TMCP ", is the land surface pyrometer with steel plate It is more than 40% by calculating accumulation reduction ratio of the steel plate mean temperature tried to achieve more than 1000 DEG C for more than 900 DEG C, and The mill train that the reduction ratio for making every a time is more than 10% thereafter, then makes more than 700 DEG C more than two passages to carry out hot rolling And hot rolling is carried out for more than 20% less than 900 DEG C of accumulation reduction ratio, make rolling terminate surface temperature to be after 850 DEG C, from cold But surface temperature is started：950 DEG C are risen, with average cooling rate：10 DEG C/s is begun to cool down, and is stopped in 350~600 DEG C of temperature, Then the method that is air-cooled to room temperature thereafter,." QT ", is to be air-cooled to after hot rolling, is heated to more than 850 DEG C and less than 950 DEG C Temperature quenched after, with 600~700 DEG C progress temper methods.
Use above-mentioned steel plate, it then follows the method for NACE standard TM0284-2003 defineds implements HIC experiments, really Recognizing in hic resistance experiment has flawless.Its result is shown in table 6.
[table 5]
[table 6]
It is known as below by table 5 and table 6.Steel grade No.1~7,10~16 meet defined composition composition, and the Ca of slab Decrement suppresses below threshold value, is the excellent steel plate of the invention of hic resistance.
In contrast, in steel grade No.9 and 18, the Ca decrements of slab exceed threshold value, therefore the hic resistance evaluation of slab For NG.In the HIC experiments carried out in addition after rolling, crackle occurs for steel plate, confirms hic resistance poor.Other steel grade No.9 and 18 be that the chemical composition composition of steel plate departs from the defined example of the present invention.That is, in steel grade No.9 steel plate, REM and Zr are 0%, also, (Ca-1.25S)/O value departs from regulation, therefore hic resistance is poor.Steel grade No.18 is because of (Ca-1.25S)/O's Value departs from regulation, so hic resistance is poor.Must be smaller than threshold value although the Ca decrements that steel grade No.8 and 17 is slab suppress, The chemical composition composition of steel plate departs from the defined example of the present invention.That is, in steel grade No.8, REM and Zr are 0%, also, (Ca/ S value) departs from regulation, therefore hic resistance is poor.Other steel grade No.17 is because the value of (Ca/S) departs from regulation, hic resistance Difference.
Be evaluated as in the hic resistance of slab in OK example, to the steel plate as product since casting, i.e. by The cycle (casting → rolling → delivery) of sulfur resistive steel plate delivery is 19 days.If in contrast, using the steel plate obtained after rolling HIC experiments are carried out, hic resistance is evaluated, then the cycle (casting → rolling → HIC experiments → delivery) to delivery since casting need to To be up to the cycle of 28 days.In the present embodiment, because the experiments of the HIC after the rolling can be omitted, since casting Cycle to delivery can significantly shorten to 19 days from 28 days.
In addition, the hic resistance of slab is evaluated as in NG example, when the stage of slab starts melting again, opened from casting Begin to as product steel plate, i.e. by the cycle (casting → melting → rolling → delivery again) deliver to sulfur resistive steel plate be 54 My god.In contrast, carrying out HIC experiments using the steel plate obtained by after rolling, the hic resistance of product is evaluated, if result is to comment Valency is NG, then just starts melting again after above-mentioned HIC experiments are carried out, therefore to the steel plate delivery as product since casting Cycle (casting → rolling → HIC experiment → melting → rolling → HIC experiments → deliveries again) needs the cycle up to 72 days.At this In embodiment, because the experiments of the HIC after the rolling can be omitted, even if need melting again, to hair since casting The cycle of goods also can significantly shorten to 54 days from 72 days.
As more than, according to the present invention, because the HIC experiments after without being rolled, in the stage of the slab as slab Hic resistance can be just evaluated, delivery cycle is manufactured so can significantly shorten.Further, in the present embodiment, for determining slab Hic resistance evaluation threshold value HIC experiments, the HIC experiments with confirmation are identical, thus decision method of the invention it may be said that Precision is very high.

Claims (10)

1. the excellent steel plate of a kind of hydrogen induced cracking resistance, it is characterised in that met in terms of quality %
C：0.02~0.15%,
Si：0.02~0.50%,
Mn：0.6~2.0%,
P：Higher than 0% and below 0.030%,
S：Higher than 0% and below 0.003%,
Al：0.010~0.08%,
Ca：0.0003~0.0060%,
N：0.001~0.01% and
O：Higher than 0% and below 0.0045%,
Also contain from
REM：Higher than 0% and below 0.02% and
Zr：More than one the element selected in the group constituted higher than 0% and below 0.010%, surplus is by iron and can not The impurity avoided is constituted,
The Ca and S ratio is that Ca/S is more than 2.0, and
The Ca, the S and the O meet (Ca-1.25S)/O≤1.80,
And then, the Ca concentration of molten steel subtracts Ca decrements obtained by the Ca concentration of slab in threshold value Ca out of tundishdropθHereinafter, Threshold value CadropθThe maximum Ca decrements of hydrogen induced cracking do not occur for steel plate obtained from being the rolling slab.
2. steel plate according to claim 1, wherein, the threshold value CadropθIt is the method in advance by following (i)~(iii) The value tried to achieve：
(i) the Ca concentration and the Ca concentration of slab of molten steel in tundish are measured, and is subtracted from the Ca concentration of molten steel in the tundish Go the Ca concentration of the slab and calculate Ca decrements；
(ii) slab of the rolling to be cast with the slab identical casting condition, hydrogen induced cracking is carried out for resulting steel plate Experiment；
(iii) according to the hydrogen induced cracking result of the test by (i) Ca decrements measured and (ii), try to achieve and do not send out The maximum Ca decrements of raw hydrogen induced cracking.
3. steel plate according to claim 2, wherein, it is described with the slab cast with the slab identical casting condition Measured the slab of Ca decrements.
4. according to steel plate according to any one of claims 1 to 3, wherein, the Ca concentration of the slab is in the slab It is minimum among the resulting Ca concentration of more than 2 in position investigation Ca concentration more than at different 2 on thickness direction Ca concentration
5. according to steel plate according to any one of claims 1 to 3, wherein, the threshold value CadropθIt is 4ppm.
6. according to steel plate according to any one of claims 1 to 3, wherein, as other elements, also contained in terms of quality % From
B：Higher than 0% and below 0.005%,
V：Higher than 0% and below 0.1%,
Cu：Higher than 0% and below 1.5%,
Ni：Higher than 0% and below 1.5%,
Cr：Higher than 0% and below 1.5%,
Mo：Higher than 0% and below 1.5% and
Nb：More than one the element selected in the group constituted higher than 0% and below 0.06%.
7. according to steel plate according to any one of claims 1 to 3, wherein, as other elements, also contained in terms of quality % From
Ti：Higher than 0% and below 0.03% and
Mg：More than one the element selected in the group constituted higher than 0% and below 0.01%
8. according to steel plate according to any one of claims 1 to 3, it is line-pipes.
9. according to steel plate according to any one of claims 1 to 3, it is used for pressure vessel.
10. a kind of line-pipes steel pipe, it is formed by steel plate according to any one of claims 1 to 3.
CN201580070001.6A 2014-12-26 2015-12-22 The excellent steel plate of hydrogen induced cracking resistance and line-pipes steel pipe Pending CN107109566A (en)

Applications Claiming Priority (5)

Application Number Priority Date Filing Date Title
JP2014-266491 2014-12-26
JP2014266491 2014-12-26
JP2015202378A JP2016125137A (en) 2014-12-26 2015-10-13 Steel sheet and steel pipe for line pipe excellent in hydrogen-induced crack resistance
JP2015-202378 2015-10-13
PCT/JP2015/085869 WO2016104526A1 (en) 2014-12-26 2015-12-22 Steel plate having excellent hydrogen-induced cracking resistance and steel pipe for line pipe

Publications (1)

Publication Number Publication Date
CN107109566A true CN107109566A (en) 2017-08-29

Family

ID=56359036

Family Applications (1)

Application Number Title Priority Date Filing Date
CN201580070001.6A Pending CN107109566A (en) 2014-12-26 2015-12-22 The excellent steel plate of hydrogen induced cracking resistance and line-pipes steel pipe

Country Status (4)

Country Link
EP (1) EP3239319A4 (en)
JP (1) JP2016125137A (en)
KR (1) KR20170093964A (en)
CN (1) CN107109566A (en)

Families Citing this family (4)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP2016125139A (en) * 2014-12-26 2016-07-11 株式会社神戸製鋼所 Steel sheet and steel pipe for line pipe excellent in hydrogen-induced crack resistance
JP2016125140A (en) * 2014-12-26 2016-07-11 株式会社神戸製鋼所 Steel sheet and steel pipe for line pipe excellent in hydrogen-induced crack resistance and toughness
JP6869151B2 (en) * 2016-11-16 2021-05-12 株式会社神戸製鋼所 Steel pipes for steel plates and line pipes and their manufacturing methods
CN111220614B (en) * 2018-11-27 2023-05-09 宝山钢铁股份有限公司 Method for rapidly evaluating quality of molten steel

Citations (8)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH075968B2 (en) * 1990-02-13 1995-01-25 新日本製鐵株式会社 Method for producing steel sheet excellent in hydrogen-induced cracking resistance, sulfide stress corrosion cracking resistance and low temperature toughness
JP2002348609A (en) * 2001-03-23 2002-12-04 Nkk Corp Method for manufacturing steel with high strength for line pipe superior in hic resistance
JP2009120899A (en) * 2007-11-14 2009-06-04 Sumitomo Metal Ind Ltd Steel for steel pipe excellent in sour resistance and production method therefor
JP2012036462A (en) * 2010-08-09 2012-02-23 Nippon Steel Corp Steel material excelling in hydrogen-induced cracking resistance
WO2013147197A1 (en) * 2012-03-30 2013-10-03 新日鐵住金株式会社 High-strength steel pipe for line pipe having excellent hydrogen-induced cracking resistance, high-strength steel pipe for line pipe using same, and method for manufacturing same
JP2013213242A (en) * 2012-03-30 2013-10-17 Kobe Steel Ltd Steel sheet excellent in hydrogen-induced cracking resistance and production method therefor
JP2013237101A (en) * 2012-04-20 2013-11-28 Kobe Steel Ltd Steel having excellent hydrogen induced cracking resistance and method for producing the same
JP2014214371A (en) * 2013-04-30 2014-11-17 株式会社神戸製鋼所 Steel sheet excellent in sour resistance and haz toughness

Family Cites Families (12)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH06293915A (en) * 1993-04-07 1994-10-21 Nippon Steel Corp Production of low alloy steel plate for line pipe excellent in co2 corrosion resistance and sour resistance
JPH0941083A (en) * 1995-07-28 1997-02-10 Nkk Corp Resistance welded tube excellent in hic resistance and sscc resistance and its production
JP5098256B2 (en) * 2006-08-30 2012-12-12 Ｊｆｅスチール株式会社 Steel sheet for high-strength line pipe with low yield stress reduction due to the Bauschinger effect with excellent hydrogen-induced cracking resistance and method for producing the same
JP4719313B2 (en) * 2008-06-06 2011-07-06 新日本製鐵株式会社 Steel plate and line pipe steel pipe with excellent sour resistance
JP5423324B2 (en) * 2009-02-12 2014-02-19 新日鐵住金株式会社 Steel plate for high-strength line pipe and steel pipe for high-strength line pipe with excellent resistance to hydrogen-induced cracking
JP5423323B2 (en) * 2009-02-12 2014-02-19 新日鐵住金株式会社 Steel plate for high-strength line pipe and steel pipe for high-strength line pipe with excellent resistance to hydrogen-induced cracking
JP5278188B2 (en) * 2009-06-19 2013-09-04 新日鐵住金株式会社 Thick steel plate with excellent resistance to hydrogen-induced cracking and brittle crack propagation
JP2014173892A (en) * 2013-03-06 2014-09-22 Kobe Steel Ltd METHOD OF DETERMINING QUALITY OF SOUR-RESISTANT STEEL SLAB USING Ca CONCENTRATION ANALYSIS RESULTS AT DIFFERENT PLATE THICKNESS POSITIONS IN THE SLAB
JP2014173893A (en) * 2013-03-06 2014-09-22 Kobe Steel Ltd METHOD OF DETERMINING QUALITY OF SOUR-RESISTANT SLAB USING Ca CONCENTRATION ANALYSIS RESULT AT PLATE THICKNESS POSITION WITHIN SPECIFIC RANGE IN THE SLAB
JP6169025B2 (en) * 2013-03-29 2017-07-26 株式会社神戸製鋼所 Steel plates and line pipe steel pipes with excellent hydrogen-induced crack resistance and toughness
JP6165088B2 (en) * 2013-03-29 2017-07-19 株式会社神戸製鋼所 Steel sheets and line pipe steel pipes with excellent resistance to hydrogen-induced cracking and toughness of weld heat affected zone
JP6316548B2 (en) * 2013-07-01 2018-04-25 株式会社神戸製鋼所 Steel plates and line pipe steel pipes with excellent hydrogen-induced crack resistance and toughness

Patent Citations (9)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JPH075968B2 (en) * 1990-02-13 1995-01-25 新日本製鐵株式会社 Method for producing steel sheet excellent in hydrogen-induced cracking resistance, sulfide stress corrosion cracking resistance and low temperature toughness
JP2002348609A (en) * 2001-03-23 2002-12-04 Nkk Corp Method for manufacturing steel with high strength for line pipe superior in hic resistance
JP2009120899A (en) * 2007-11-14 2009-06-04 Sumitomo Metal Ind Ltd Steel for steel pipe excellent in sour resistance and production method therefor
JP2012036462A (en) * 2010-08-09 2012-02-23 Nippon Steel Corp Steel material excelling in hydrogen-induced cracking resistance
WO2013147197A1 (en) * 2012-03-30 2013-10-03 新日鐵住金株式会社 High-strength steel pipe for line pipe having excellent hydrogen-induced cracking resistance, high-strength steel pipe for line pipe using same, and method for manufacturing same
JP2013213242A (en) * 2012-03-30 2013-10-17 Kobe Steel Ltd Steel sheet excellent in hydrogen-induced cracking resistance and production method therefor
CN103361549A (en) * 2012-03-30 2013-10-23 株式会社神户制钢所 Steel plate with excellent hydrogen induced cracking resistance, and manufacturing method of the same
JP2013237101A (en) * 2012-04-20 2013-11-28 Kobe Steel Ltd Steel having excellent hydrogen induced cracking resistance and method for producing the same
JP2014214371A (en) * 2013-04-30 2014-11-17 株式会社神戸製鋼所 Steel sheet excellent in sour resistance and haz toughness

Also Published As

Publication number Publication date
EP3239319A1 (en) 2017-11-01
KR20170093964A (en) 2017-08-16
JP2016125137A (en) 2016-07-11
EP3239319A4 (en) 2018-06-27

Similar Documents

Publication Publication Date Title
CN107109595A (en) The steel plate and line-pipes steel pipe of hydrogen induced cracking resistance and tenacity excellent
US8221562B2 (en) Compact strip or thin slab processing of boron/titanium steels
RU2637202C2 (en) Sheet steel for a thick-strengthen high-strengthening pipe threading with excellent resistance to acid environment, resistance to smoke and low-temperature viscosity and also a main pipe
CN105074036B (en) The steel plate and pipeline steel tube of the tenacity excellent of hydrogen induced cracking resistance and welding heat affected zone
CN105164294B (en) Hypoxemia clean steel and the pure product made from steel of hypoxemia
CN105008570B (en) Heavy wall high tenacity high-tensile steel and its manufacture method
CN107109565A (en) The excellent steel plate of hydrogen induced cracking resistance and line-pipes steel pipe
CN107109566A (en) The excellent steel plate of hydrogen induced cracking resistance and line-pipes steel pipe
RU2666811C1 (en) Rail
CN105452512A (en) Seamless steel pipe for line pipe, and method for producing same
JP2006063351A (en) High strength steel plate with excellent hydrogen induced cracking resistance, its manufacturing method, and steel pipe for line pipe
CN104185690A (en) Rail
AU2022249476A1 (en) Steel pipe for high-pressure hydrogen, high-pressure hydrogen vessel, and method for manufacturing said steel pipe
CN107109594A (en) The excellent steel plate of hydrogen induced cracking resistance and line-pipes steel pipe
JP4254551B2 (en) High strength steel plate for line pipe with excellent HIC resistance and method for producing the same
CN111455275A (en) Seamless steel tube for oil-gas well perforating gun and manufacturing method thereof
CN109952387A (en) Steel plate and line-pipes steel pipe and its manufacturing method
WO2020189232A1 (en) Rail
WO2016104527A1 (en) Steel plate having excellent hydrogen-induced cracking resistance and steel pipe for line pipe
JP2006111928A (en) Thick steel plate for line pipe and its production method
JP2020084250A (en) Steel material for seamless steel pipe
CN106536775B (en) Mechanical structure rolling bar steel and its manufacture method
WO2016104528A1 (en) Steel plate having excellent toughness and resistance to hydrogen-induced cracking, and steel pipe for line pipe
WO2016104526A1 (en) Steel plate having excellent hydrogen-induced cracking resistance and steel pipe for line pipe
WO2016104529A1 (en) Steel plate having excellent resistance to hydrogen-induced cracking, and steel pipe for line pipe

Legal Events

Date Code Title Description
PB01 Publication
PB01 Publication
SE01 Entry into force of request for substantive examination
SE01 Entry into force of request for substantive examination
WD01 Invention patent application deemed withdrawn after publication

Application publication date: 20170829

WD01 Invention patent application deemed withdrawn after publication