CN105838992A - High-strength steel sheet and high-strength steel pipe having excellent hydrogen-induced cracking resistance for use in line pipe - Google Patents
High-strength steel sheet and high-strength steel pipe having excellent hydrogen-induced cracking resistance for use in line pipe Download PDFInfo
- Publication number
- CN105838992A CN105838992A CN201610208070.5A CN201610208070A CN105838992A CN 105838992 A CN105838992 A CN 105838992A CN 201610208070 A CN201610208070 A CN 201610208070A CN 105838992 A CN105838992 A CN 105838992A
- Authority
- CN
- China
- Prior art keywords
- segregation
- pipe
- steel
- hydrogen
- degree
- 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
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
- C22C38/54—Ferrous alloys, e.g. steel alloys containing chromium with nickel with boron
-
- 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
- C22C38/001—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
- C22C38/005—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
- C22C38/06—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
- 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
- C22C38/32—Ferrous alloys, e.g. steel alloys containing chromium with boron
Abstract
Provided are a steel sheet and a steel pipe having excellent HIC resistance that are ideal for, for instance, a line pipe used to convey petroleum or natural gas. The steel sheet and the steel pipe are formed from steel having a steel composition that comprises C: 0.02-0.08%, Si: 0.01-0.5%, Mn: 1.0-1.6%, Nb: 0.001-0.10%, Ca: 0.0001-0.0050%, N: 0.0010-0.0050%, and O: 0.0001-0.0030%, P: 0.01% or less, S: 0.0020% or less, Al: 0.030% or less, and Ti: 0.030% or less and that satisfies S/Ca<0.5, and having an unpressed portion of the part where center segregation occurs that is 0.1 mm or less in length.
Description
The application is Application No. 201080007523.9, invention entitled " hydrogen-induced cracking resistance is excellent
The effective steel plate of high-strength line-pipe and the effective steel pipe of high-strength line-pipe ", filing date in February, 2010
12 days, enter National Phase in China the application for a patent for invention that date is on August 12nd, 2011 point
Case application.
Technical field
The resistant to hydrogen that the present invention relates to be best suited for the purposes of the line pipe etc. of oil, natural gas etc. causes
(resistant to hydrogen induction is anti-thread breakage for cracking behavior；It is referred to as hic resistance) excellent line-pipes steel plate and line pipe
Use steel pipe.
Background technology
More comprising the hydrogen sulfide (H containing moisture2The conveying pipe of oil S), natural gas etc.
In spool, worry the generation of hydrogen induced cracking (referred to as HIC).Its reason is because containing moisture
H2In S environment (referred to as Sulphur Contaminated Environment), hydrogen easily invades steel from surface.
HIC results from the MnS of extension in the center segregation portion being especially in the presence of in steel, gathering
In the steel such as the oxidation system field trash in the carbonitride of Ti and/or Nb or oxide buildup band
The hydrogen that the surrounding of defect assembles.
I.e., within sulfur, the hydrogen gathering around defect invaded in steel becomes gas, its pressure
Power exceedes the Fracture Toughness (K of steelIC) time, crack.If additionally, the center segregation portion of steel,
The peripheries of field trash etc. harden, then crackle easily extends.
Therefore, in the line pipe used under Sulphur Contaminated Environment, since the past, just suppression has been taked to prolong
The gathering of the generation of the MnS stretched, the carbonitride of suppression Ti, Nb and oxide etc. or suppression
The countermeasure of the formation etc. of the hardening phase caused because of center segregation.
Such as, Mn is easily at the element of center segregation of steel plate, it is proposed that suppression Mn's is inclined
The method (such as, patent documentation 1～3) of analysis.Patent documentation 1 proposes the Mn in suppression segregation portion
Content is relative to the steel plate of the ratio of the average Mn content in steel.It addition, patent documentation 2 and 3 proposes
In addition to limiting the size of Mn segregation point, it is further defined by the P concentration in segregation portion, and effectively profit
With the double-strength pipe spool of Ca.
It addition, it is proposed that in addition to the segregation being conceived to Mn, be also conceived to the segregation of Nb
The hot rolled steel plate (such as, patent documentation 4) that hic resistance is excellent.Additionally, it is proposed that suppression Ti,
The method (such as, patent documentation 5,6) of the field trash of the carbide of Nb, nitride etc..
Prior art literature
Patent documentation 1: Japanese Unexamined Patent Publication 6-220577 publication
Patent documentation 2: Japanese Unexamined Patent Publication 6-256894 publication
Patent documentation 3: Japanese Unexamined Patent Publication 6-271974 publication
Patent documentation 4: Japanese Unexamined Patent Publication 2002-363689 publication
Patent documentation 5: Japanese Unexamined Patent Publication 2006-63351 publication
Patent documentation 6: Japanese Unexamined Patent Publication 2008-7841 publication
Summary of the invention
About suppression Mn segregation and make use of Ca MnS morphology Control exploitation oneself just existed in the past
Carry out energetically, but known ought only control (the maximum Mn content in segregation portion)/(average in steel
Mn content) and/or during the size of Mn segregation point, it is impossible to enough fully prevent HIC, need it
Tighter control.
If additionally, eliminate the segregation of Mn, the segregation of Nb just becomes problem.Understand for this Nb
Segregation, utilize (the maximum Nb content in segregation portion)/(the average Nb content in steel) control
And be insufficient to, it is necessary to more strictly control.Even if it addition, controlling the field trash of Nb-Ti-C-N system
Length, (Ti, Nb) (C, N) be surface density and the length of field trash, HIC can not be prevented
Generation.
The present invention completes in view of such practical situation, its problem be to provide be best suited for oil,
The line-pipes steel plate that the hic resistance of the steel pipe that the line pipe of natural gas etc. etc. are used is excellent
With line-pipes steel pipe.
The present inventors are for excellent for obtaining the hydrogen-induced cracking resistance that tensile strength is more than 500MPa
The effective steel plate of high-strength line-pipe and the effective steel pipe of high-strength line-pipe required for condition attentively grind
Study carefully, to such an extent as to invent new pipe for ultrahigh-strength line steel plate and the effective steel pipe of high-strength line-pipe.This
Bright main idea is as follows.
(1) the effective steel plate of high-strength line-pipe that a kind of hydrogen-induced cracking resistance is excellent, it is characterised in that with
Quality % is counted, and contains:
C:0.02～0.08%,
Si:0.01～0.5%,
Mn:1.0～1.6%,
Nb:0.001～0.10%,
Ca:0.0001～0.0050%,
N:0.0010～0.0050%,
O:0.0001～0.0030%,
And be limited to:
Below P:0.01%,
Below S:0.0020%,
Below Al:0.030%,
Below Ti:0.030%,
The content of S, Ca meets S/Ca ＜ 0.5,
Its surplus is made up of Fe and inevitable impurity element,
Further, the length of the non-nip portion in center segregation portion is limited in below 0.1mm.
(2) according to the effective steel plate of high-strength line-pipe that the hydrogen-induced cracking resistance described in above-mentioned (1) is excellent,
It is characterized in that, in terms of quality %, contain:
Ni:0.01～2.0%,
Cu:0.01～1.0%,
Cr:0.01～1.0%,
Mo:0.01～1.0%,
W:0.01～1.0%,
V:0.01～0.10%,
Zr:0.0001～0.050%,
Ta:0.0001～0.050%,
One or more among B:0.0001～0.0020%,
Its surplus is made up of Fe and inevitable impurity.
(3) according to the double-strength pipe spool that the hydrogen-induced cracking resistance described in above-mentioned (1) or (2) is excellent
With steel plate, it is characterised in that in terms of quality %, possibly together with:
REM:0.0001～0.01%,
Mg:0.0001～0.01%,
Y:0.0001～0.005%,
Hf:0.0001～0.005%,
One or more among Re:0.0001～0.005%.
(4) according to the double-strength pipe spool that the hydrogen-induced cracking resistance described in above-mentioned (1) or (2) is excellent
With steel plate, it is characterised in that
It is further limited to:
Maximum Mn degree of segregation: less than 2.0,
Nb degree of segregation: less than 4.0,
Ti degree of segregation: less than 4.0.
(5) according to described in above-mentioned (1) or (2) the excellent high-strength line-pipe of hydrogen-induced cracking resistance
Effective steel plate, it is characterised in that the maximum hardness in center segregation portion is below 300Hv.
(6) the effective steel pipe of high-strength line-pipe that a kind of hydrogen-induced cracking resistance is excellent, it is characterised in that with
Quality % is counted, and mother metal contains:
C:0.02～0.08%,
Si:0.01～0.5%,
Mn:1.0～1.6%,
Nb:0.001～0.10%,
Ca:0.0001～0.0050%,
N:0.0010～0.0050%,
O:0.0001～0.0030%,
And be limited to:
Below P:0.01%,
Below S:0.0020%,
Below Al:0.030%,
Below Ti:0.030%,
The content of S, Ca meets S/Ca ＜ 0.5,
Its surplus is made up of Fe and inevitable impurity element,
Further, the length of the non-nip portion in the center segregation portion of mother metal is limited in below 0.1mm.
(7) according to the effective steel pipe of high-strength line-pipe that the hydrogen-induced cracking resistance described in above-mentioned (6) is excellent,
It is characterized in that, in terms of quality %, mother metal contains:
Ni:0.01～2.0%,
Cu:0.01～1.0%,
Cr:0.01～1.0%,
Mo:0.01～1.0%,
W:0.01～1.0%,
V:0.01～0.10%,
Zr:0.0001～0.050%,
Ta:0.0001～0.050%,
One or more among B:0.0001～0.0020%.
Its surplus is made up of Fe and inevitable impurity,
(8) according to the double-strength pipe spool that the hydrogen-induced cracking resistance described in above-mentioned (6) or (7) is excellent
With steel pipe, it is characterised in that in terms of quality %, mother metal possibly together with:
REM:0.0001～0.01%,
Mg:0.0001～0.01%,
Y:0.0001～0.005%,
Hf:0.0001～0.005%,
One or more among Re:0.0001～0.005%.
(9) according to the double-strength pipe spool that the hydrogen-induced cracking resistance described in above-mentioned (6) or (7) is excellent
With steel pipe, it is characterised in that
It is further limited to: mother metal
Maximum Mn degree of segregation: less than 2.0,
Nb degree of segregation: less than 4.0,
Ti degree of segregation: less than 4.0.
(10) according to the high-strength line-pipe that the hydrogen-induced cracking resistance described in above-mentioned (6) or (7) is excellent
Effective steel pipe, it is characterised in that the maximum hardness in the center segregation portion of mother metal is below 300Hv.
In accordance with the invention it is possible to manufacture the degree of segregation reduction of Mn, Nb, Ti, center segregation portion not
The length of nip portion and the line-pipes that rising is suppressed, hydrogen-induced cracking resistance is excellent of maximum hardness
Steel plate and line-pipes steel pipe etc., contribution industrially is the most notable.
Accompanying drawing explanation
Fig. 1 is the relation of the CAR in ratio S/Ca Yu the HIC test of the content representing S and Ca
Figure.
Detailed description of the invention
The present inventors use various line-pipes steel plates, carry out NACE (U.S. corrosion engineering teacher
Association, National Association of Corrosion and Engineer) test, have rated with or without
The generation of HIC.NACE test is to be the solution of 2.7 at 5%NaCl solution+0.5% acetic acid, pH
In make hydrogen sulfide gas saturated, whether generate the test method of crackle after investigating 96 hours.
After test, produce test specimen from the steel plate creating crackle, observe the generating unit of HIC in detail
Position.Its result is distinguished, the non-nip portion in center segregation portion is the starting point of the HIC of particular importance.
The non-nip portion in this center segregation portion, it is necessary to its length is suppressed at below 0.1mm.This is base
Regulation in following situation: utilize scanning electron microscope (SEM) to observe and produce after above-mentioned NACE tests
The section of the crackle of the test specimen of HIC, the minima of the length of non-nip portion is more than 0.1mm.
The non-nip portion of what is called, is the space produced in steel billet when solidification, by hot rolling not pressing,
Also phenomenon remaining in steel plate, in the case of size is big, can be examined by the non-demolition of ultrasound wave etc.
Look into and measure its length.
In the reason of the center segregation portion non-nip portion of remaining, it is hydrogen contained in steel billet before hot rolling.
After carrying out steel-smelting by converter and double refining, when casting continuously, steel solidifies, cold
But shrinking, the most particularly central part at steel billet produces space.It is the situation of negative pressure in this space
Under, if the hydrogen content of steel billet is many, then during hydrogen enters space.Melting is being carried out by double refining
Time, hydrogen major part contained in steel still remains in the space of the steel billet after continuous casting.
When the heating of hot rolling, steel billet be organized as austenite, hydrogen be difficult to steel billet external diffusion release.
It is that face-centered cubic is brilliant that its reason is because austenite, can the more reason of the hydrogen amount of solid solution.If by steel billet
Heat and implement pressure, then the space of steel billet diminishes, but the pressure of hydrogen contained in space and space
Size inversely proportionally uprise.Therefore, even if can not be by space pressing by hot rolling, meeting exists
The non-nip portion of remaining in steel plate.
Having investigated the relation of the length of the hydrogen content in steel and non-nip portion in minute detail, result specify that:
When by hydrogen content suppression at below 2.5ppm, remain in the non-nip portion in the center segregation portion of steel plate
Length become below 0.1mm.Therefore, in order to the length of the non-nip portion in center segregation portion is suppressed
At below 0.1mm, it is necessary to the hydrogen content in steel is limited in below 2.5ppm.It addition, hydrogen point
Analysis is to use combustion method to measure the analysis of the steel of sampling after double refining.
It addition, when, after hot rolling, steel plate is cooled, and metal structure becomes ferrite, shellfish from austenite phase
When family name's body, martensite, pearlite etc., hydrogen is to outside dispersal events.Therefore the hydrogen in steel plate is retained in
Content reduces compared with the hydrogen content after double refining.
The present inventors and then the generation starting point about HIC be repeated research it was found that except this
In addition, the precipitate of Ti, Nb that (a) extends MnS, (b) have accumulated and (c) gather
The oxide collected also becomes the starting point of HIC, if they are also carried out suppression, then can prevent significantly
The only generation of the HIC of line-pipes steel plate and line-pipes steel pipe.
In order to suppress the thick MnS extended, it is necessary to S amount is set below 0.002%, by S
It is set below 0.5 with the ratio S/Ca of the content of Ca.
Fig. 1 represents the CAR (crackle area occupation ratio) in the HIC test of 0.04%C-1.25%Mn steel
Relation with S/Ca.Distinguish as shown in Figure 1, if the ratio of S/Ca is more than 0.5, then open
Beginning to produce HIC, therefore S/Ca have to be lower than 0.5.
It addition, for the gathering of inhibited oxidation thing, it is necessary to O amount is set to less than 0.0030%, Al
Amount is set to less than 0.030%.Specify that: if O amount is many, the thickest oxide is easily assembled,
If adding the Al more than 0.030%, then the cluster of the oxide of Al is easily assembled.
And find: in order to suppress the thick MnS extended, preferably by steel plate and the maximum of steel pipe
Mn degree of segregation is set to less than 2.0；And, in addition, Ti, the Nb assembled by suppression
Carbonitride, can significantly prevent the product of the HIC of line-pipes steel plate and line-pipes steel pipe
Raw.
In order to suppress the gathering of the carbonitride of Ti, Nb, preferably meet following condition: measured by N
Being set to less than 0.0050%, C amount is set to less than 0.06%, and the degree of segregation of Nb and Ti is set to 4.0
Below.
Here, so-called maximum Mn degree of segregation is in the Mn content of steel plate and steel pipe, center segregation
The maximum Mn amount in portion relative to the ratio of the average Mn amount in addition to center segregation portion, i.e. (in
The maximum Mn amount in heart segregation portion)/the value of (the average Mn amount in addition to center segregation portion).
Similarly, Nb degree of segregation and Ti degree of segregation steel plate and steel pipe, center segregation portion flat
Nb amount (Ti amount) of homogenizing measures (Ti amount) relative to the average Nb in addition to center segregation portion
Ratio.
Maximum Mn degree of segregation can pass through EPMA (electron probe microanalyzer, Electron
Probe Micro Analyzer) or can image procossing EPMA measurement result CMA (calculate
Machine auxiliary microscopic analyzer, Computer Aided Micro Analyzer) measure steel plate and steel pipe
The distribution of Mn concentration is tried to achieve.
Now, the numerical value of maximum Mn degree of segregation is according to the probe diameter of EPMA (or CMA)
And change.Present inventors found that, by probe diameter (beam diameter) is set to 2 μm, Ke Yihe
Evaluate the segregation of Mn suitablely.It practice, be measured as in the following manner.
Use EPMA, with the beam diameter of 50 μm measure 20mm width (HIC specimen width) ×
The concentration distribution of the Mn measured in region of 20mm thickness (HIC specimen thickness).Then, exist
The position (center segregation portion) of Mn amount the denseizationest, then measure 1mm (width) with the beam diameter of 2 μm
The Mn concentration in the region of × 1mm (thickness).Then, the distribution of this Mn concentration maximum is tried to achieve
Mn degree of segregation.Now, the data of 500 point × 500 are accumulated.By among these 250000
Big Mn concentration is defined as maximum relative to the ratio of the average Mn concentration in addition to center segregation portion
Mn degree of segregation also obtains its value.
It addition, can also be likewise by EPMA or CMA for Nb degree of segregation and Ti degree of segregation
Measure the distribution of Nb concentration and the distribution of Ti concentration respectively and try to achieve.Understand for Nb degree of segregation and Ti
Degree of segregation can also suitably evaluate segregation likewise by beam diameter is set to 2 μm.
It practice, about Nb, Ti degree of segregation, by EPMA, measure with the beam diameter of 50 μm
The mensuration region of 20mm width (HIC specimen width) × 20mm thickness (HIC specimen thickness)
In Nb, Ti respective concentration distribution, after trying to achieve average Nb concentration and average Ti concentration, at Nb
The position (center segregation portion) of amount, Ti amount the denseizationest, then it is (wide to measure 1mm with the beam diameter of 2 μm
Degree) concentration of Nb and Ti in region of × 1mm (thickness).Now, it is taken at what plate laterally measured
The meansigma methods of 500, derives average Nb and the Ti concentration in center segregation portion.Then, by center
The average Nb concentration (Ti concentration) in segregation portion is fixed relative to the ratio of average Nb concentration (Ti concentration)
Justice is for Nb degree of segregation (Ti degree of segregation) and obtains its value.
It addition, if there is the field trash of MnS etc., the degree of segregation of the most each element becomes greatly on apparent,
Therefore in the case of encountering field trash, remove its value be evaluated.
Furthermore it is preferred that inhibit the steel plate of the segregation of Mn, Nb, Ti and the center segregation portion of steel pipe
Maximum hardness is below 300Hv.By the upper limit of center segregation portion maximum hardness is set to 300Hv,
Can positively prevent the generation of HIC.Mn, Nb are the elements improving hardenability, and Ti contributes to
Precipitation strength, therefore by suppressing the segregation of these elements, it is possible to the hardening in suppression center segregation portion.
It addition, center segregation portion is the concentration maximum of the Mn measured by EPMA and/or CMA
Position, the maximum hardness in center segregation portion, by utilizing 3% nitric acid+97% nital
After corrosion, based on JIS Z 2244, carry out Vickers hardness test with the load of 25g and measure.
Hereinafter, the present invention for completing based on above such result of study is described in detail.
Restriction reason firstly, for the matrix constituent in the steel plate of the present invention and steel pipe describes.
Hereinafter, the % of the content of element means quality %.
C:C is the element of intensity improving steel, as its effective lower limit must add 0.02% with
On.On the other hand, if C measures more than 0.08%, then promote the generation of carbide, damage hic resistance
Property, therefore the upper limit is set to 0.08%.It addition, for the fall suppressing HIC, weldability and toughness
Low, preferably C amount is less than 0.06%.
Si:Si is deoxidant element, it is necessary to add more than 0.01%.On the other hand, if Si amount exceedes
0.5%, then make the toughness of welding heat affected zone (HAZ) reduce, therefore the upper limit is set to 0.5%.
Mn:Mn is to improve intensity and the element of toughness, it is necessary to add more than 1.0%.On the other hand,
If Mn measures more than 1.6%, then make HAZ toughness reduce, therefore the upper limit is set to 1.6%.Separately
Outward, in order to suppress HIC, preferably Mn amount is set below 1.5%.
Nb:Nb is to form carbide, nitride, contributes to the element of the raising of intensity.For terrible
To its effect, it is necessary to add the Nb of more than 0.001%.But, if excessively adding Nb, then
Nb degree of segregation increases, and causes the gathering of the carbonitride of Nb, and hic resistance reduces.Therefore, exist
In the present invention, the upper limit that Nb measures is set to 0.10%.Furthermore, it is contemplated that in the case of HIC,
Nb amount is preferably less than 0.05%.
N:N is the element forming the nitride such as TiN, NbN, during in order to utilize nitride to make heating
Austenite particle diameter fine, it is necessary to by N measure lower limit be set to 0.0010%.But, if N
Content is more than 0.0050%, then the carbonitride of Ti and Nb is easily assembled, and damages hic resistance.
Therefore, the upper limit that N measures is set to 0.0050%.It addition, in the case of requiring toughness etc., in order to
The coarsening of suppression TiN, is preferably set to less than 0.0035% by N amount.
P:P is impurity, if content is more than 0.01%, then damages hic resistance, and HAZ
Toughness reduces.Therefore, the content of P is limited in less than 0.01%.
Generate the MnS extended along rolling direction when S:S is hot rolling, make the element that hic resistance reduces.
Therefore, in the present invention, it is necessary to reduce S amount, its content is limited in less than 0.0020%.It addition,
In order to improve toughness, preferably S amount is less than 0.0010%.S amount is the fewest more good, it can be difficult to make it
Less than 0.0001%, from the viewpoint of manufacturing cost, preferably comprise more than 0.0001%.
Ti:Ti is the refinement being used for crystal grain usually used as deoxidizer and/or nitride forming element
Element, but in the present invention, be the element making hic resistance and toughness reduce because carbonitride is formed.
Therefore, the content of Ti is limited in less than 0.030%.
Al:Al is deoxidant element, but in the present invention, if addition is more than 0.030%, can be true
Recognize the gathering cluster of Al oxide, be therefore limited in less than 0.030%.In the case of requiring toughness,
Preferably the upper limit that Al measures is set to less than 0.017%.There is no particular limitation for the lower limit of Al amount, but
In order to reduce the oxygen amount in molten steel, preferably add the Al of more than 0.0005%.
O:O is impurity, for the gathering of inhibited oxidation thing, improves hic resistance, is limited by content
Below 0.0030%.For the generation of inhibited oxidation thing, improve mother metal and HAZ toughness, preferably
O amount is set to less than 0.0020%.
Ca:Ca is to generate sulfide CaS, suppresses the generation of the MnS extended along rolling direction, aobvious
Write the element that ground contributes to the improvement of hic resistance.The addition of Ca, less than 0.0001%, obtains
Less than effect, therefore lower limit is set to 0.0001%.Preferably comprise more than 0.0005%.The opposing party
Face, if the addition of Ca is more than 0.0050%, then oxide buildup, damage hic resistance, because of
The upper limit is set to 0.0050% by this.
In the present invention, form CaS by adding Ca, fix S, therefore the content of S and Ca
S/Ca ratio be important indicator.If S/Ca ratio is more than 0.5, then generate MnS, when rolling
Form the MnS extended.Its result, hic resistance deteriorates.Therefore, the value of S/Ca ratio is set to
Less than 0.5.
It addition, in the present invention, as improving the element of intensity and toughness, can add Ni, Cu,
One or more element among Cr, Mo, W, V, Zr, Ta, B.
Ni:Ni is the effective element of the improvement to toughness and intensity, must add to obtain its effect
More than 0.01%, but add then hic resistance and the weldability reduction more than 2.0%, the most excellent
Selecting its upper limit is 2.0%.
Cu:Cu is not reduce toughness the effective element of rising to intensity, but less than 0.01%
Words then do not have effect, if it exceeds 1.0% easily cracks when heating steel billet or when welding.Cause
This, preferably its content is 0.01～1.0%.
Cr:Cr in order to improve the intensity of steel by precipitation strength, and interpolation more than 0.01% is relatively effective, but
If added in large quantities, then making hardenability increase, producing bainite structure, making toughness reduce.Therefore,
Preferably its upper limit is 1.0%.
Mo:Mo is to improve hardenability, and forms carbonitride thus improve the element of intensity, for
Obtain its effect, preferably add more than 0.01%.On the other hand, if it exceeds 1.0% ground adds in a large number
Adding Mo, then cost increase, therefore preferred upper limit is 1.0%.If it addition, the intensity of steel rises,
The most sometimes hic resistance and toughness reduce, and the most preferred upper limit is set to 0.20%.
W:W is the effective element of the raising to intensity, preferably adds more than 0.01%.On the other hand,
If adding the W more than 1.0%, then occasionally resulting in the reduction of toughness, therefore preferred upper limit is 1.0%.
V:V is to form carbide, nitride, contributes to the element of the raising of intensity, in order to obtain
Effect, preferably adds more than 0.01%.On the other hand, if adding the V more than 0.10%, then have
Time cause the reduction of toughness, therefore preferred upper limit is 0.10%.
Zr, Ta:Zr and Ta are to be identically formed carbide, nitride with V, contribute to intensity
The element improved, in order to obtain its effect, preferably adds more than 0.0001%.On the other hand, if
Excessively add Zr and Ta more than 0.050%, then occasionally result in the reduction of toughness, therefore preferably its
The upper limit is 0.050%.
B:B is the cyrystal boundary segregation at steel, aids significantly in the element of the raising of hardenability.For terrible
To its effect, preferably add the B of more than 0.0001%.It addition, B generates BN, solid solution N is made to drop
Low, also contribute to the element of the raising of the toughness of welding heat affected zone, the most more preferably add
More than 0.0005%.On the other hand, if excessively adding B, then to the segregation excess of crystal boundary, have
Time cause the reduction of toughness, therefore preferred upper limit is 0.0020%.
And then, for the field trash of control oxide and sulfide etc., it is also possible to containing REM, Mg,
One or more in Zr, Ta, Y, Hf, Re.
REM:REM is the element added as deoxidizer and desulfurizing agent, preferably adds 0.0001%
Above.On the other hand, if added more than 0.010%, then produce thick oxide, sometimes make to resist
The toughness of HIC, mother metal and HAZ reduces, and preferred addition is less than 0.010%.
Mg:Mg is the element added as deoxidizer and desulfurizing agent, particularly produces fine oxygen
Compound, it helps the raising of HAZ toughness.In order to obtain this effect, preferably add 0.0001%
Above Mg.On the other hand, if adding the Mg more than 0.010%, the then easy coagulation of oxide
And coarsening, occasionally result in the reduction of the toughness of the deterioration of hic resistance, mother metal and HAZ.Therefore,
The addition of preferably Mg is less than 0.010%.
Y, Hf, Re:Y, Hf, Re are to be equally generated sulfide with Ca, and suppression is along rolling side
To the generation of the MnS of elongation, contribute to the element of the raising of hic resistance.Such in order to obtain
Effect, preferably adds Y, Hf, Re of more than 0.0001%.On the other hand, if Y, Hf, Re
Amount more than 0.0050%, then oxide increases and occurs coagulation, coarsening to damage hic resistance,
Therefore preferably addition is less than 0.0050%.
The side of a length of below 0.01mm below for the non-nip portion in the center segregation portion making steel plate
Method illustrates.
As described above, the reason in the center segregation portion non-nip portion of remaining is institute in steel billet before hot rolling
The hydrogen contained.Therefore, by reducing the hydrogen amount in double refining, can make in the space of steel billet contained
The pressure of hydrogen reduces.If making the H content in double refining is less than 0.00025%, then hot rolling
After, basic not non-nip portion, even if its existence also is able to make its a length of below 0.1mm.
In order to reduce the hydrogen amount in double refining, the hydrogen dividing potential drop of atmosphere when preferably making to carry out double refining
Reduce.Such as, by being blown into noble gas and nitrogen etc. in atmosphere, it is possible to make hydrogen dividing potential drop reduce.
And then, in the present invention, by the maximum Mn degree of segregation in the mother metal of steel plate and steel pipe, Nb
Degree of segregation and Ti degree of segregation are set to less than 2.0, less than 4.0 and less than 4.0.
By maximum Mn degree of segregation is set to less than 2.0, the generation of thick MnS can be suppressed,
It is possible to prevent the generation of HIC with the MnS extended along rolling direction as starting point.If it addition,
Nb degree of segregation is set to less than 4.0, then suppresses the generation of the Nb (C, N) that have accumulated, if will
Ti degree of segregation is set to less than 4.0, then suppress the generation of the TiN that have accumulated, be possible to prevent hic resistance
Deterioration.
Maximum Mn degree of segregation is that the maximum Mn in the center segregation portion of steel plate and steel pipe measures relative to removing
The ratio of the average Mn amount beyond center segregation portion, can by being set to 2 μm by beam diameter
EPMA or CMA measures the Mn concentration distribution of steel plate and steel pipe and tries to achieve.For Nb degree of segregation
Also it is same with Ti degree of segregation, by beam diameter being set to EPMA or CMA of 2 μm respectively
Measure the distribution of Nb concentration and Ti concentration is distributed, try to achieve the equalization in the center segregation portion of steel plate and steel pipe
Nb amount relative to the average Nb amount in addition to center segregation portion ratio (Nb degree of segregation),
The Ti of the equalization in the center segregation portion of steel plate and steel pipe measures relative in addition to center segregation portion
The ratio (Ti degree of segregation) of average Ti amount.
Below for for suppressing the method for maximum Mn degree of segregation, Nb degree of segregation and Ti degree of segregation to enter
Row explanation.
In order to suppress the segregation of Mn, Nb and Ti, slighter compress during the final solidification in casting continuously
It is best suitable for.Slighter compress during final solidification is to cast the uneven, solidifying of cooling to eliminate to result from
Gu portion and do not solidify mixing of portion and implement, it thus can be made the most finally to solidify.
In continuously casting, generally, steel billet is water cooled, but horizontal end cooling is fast, horizontal in
The cooling in centre portion is reinforced.Therefore, even if solidifying in the horizontal end of steel billet and central part,
Slow in 1/4 horizontal solidification, the inside remaining at steel billet does not solidifies portion.Therefore, sometimes at steel billet
Horizontal, solidification portion and the portion that do not solidifies become uneven, such as, solidification portion and do not solidify the interface in portion
Shape laterally becoming W type.If it occur that the most uneven such solidification, then encourage
Segregation, makes HIC-resistance deteriorate.
On the other hand, if slighter compress when finally solidifying in casting continuously, then portion is not solidified
It is extruded, can laterally homogeneously solidify.If it addition, after laterally producing uneven solidification
Apply slighter compress, then the deformation drag in solidification portion of resulting from is big, becomes effectively to extrude and does not coagulates
Gu portion.
Therefore, in order to not produce the solidification of such W type, preferably finally solidify position according to strand
The horizontal distribution of center solid rate control drafts while carrying out slighter compress.By in this wise
Carry out, even if laterally center segregation also can be suppressed, make maximum Mn degree of segregation, Nb degree of segregation, Ti
Degree of segregation is less.
Containing the steel of above-mentioned composition, it is smelted in steel making working procedure, then passes through and cast and shape continuously
Become steel billet, this steel billet reheated and implements heavy plate rolling, being formed as steel plate.
In this manufacturing process, if the reheating temperature of steel billet is set to more than 950 DEG C, will tie again
The pressure ratio of brilliant humidity province is set to more than 2, the pressure ratio in non-recrystallization zone is set to more than 3 and enters
Row heavy plate rolling, then can make average original austenite particle diameter become below 20 μm.And then, rolling
Water-cooled is carried out after end, but preferably: from the beginning of the temperature of more than 750 DEG C carry out water-cooled, 400～500
DEG C temperature range carry out the stopping of water-cooled.
It addition, recrystallization temperature district is the temperature range producing recrystallization after rolling, for the present invention
Steel composition for, about more than 900 DEG C.On the other hand, non-recrystallization temperature district is in rolling
The most do not produce the temperature range of recrystallization and ferrite transformation, for the composition of the steel of the present invention,
It is about 750～900 DEG C.Rolling in recrystallization temperature district is referred to as recrystallization rolling or roughing,
Rolling in non-recrystallization temperature district is referred to as the rolling of non-recrystallization or finish rolling.
After the rolling of non-recrystallization, by starting water-cooled from the temperature of more than 750 DEG C, and water-cooled is stopped
Temperature is set to more than 400 DEG C, the most as described below, it is possible to make the highest hardness of center segregation
For below 300Hv.First, if water-cooled being started temperature be set below 750 DEG C, then open in cooling
More generating ferrite before beginning, C (carbon) discharges to austenite from ferrite.Thereafter, if
Cooling, then concentrate the martensite that austenite phase transition is the hard containing more C amount having C.
Therefore, if water-cooled being started temperature be set to more than 750 DEG C, the generation of the martensite of suppression hard,
Then hardness can be suppressed at below 300Hv.If it addition, water-cooled being stopped temperature being set to 400 DEG C
Above, then the martensite generation decomposed of the hard after phase transformation, similarly hardness suppression can be existed
Below 300Hv.It addition, if water-cooled stopping temperature is too high, intensity reduces, the most preferably 500
Below DEG C.
Embodiment
Then, the present invention is illustrated in greater detail by embodiment.
Melting has the steel of the chemical composition shown in table 1, and by casting continuously, making thickness is 240mm
Steel billet.It addition, be also shown for the assay value of the hydrogen content of molten steel in Table 1.In casting continuously,
Implement slighter compress during final solidification.The heating steel billet to 1000～1250 DEG C that will obtain, is exceeding
The recrystallization temperature district of 900 DEG C carries out hot rolling, then carries out the non-recrystallization temperature district at 750～900 DEG C
Hot rolling.After hot rolling, more than 750 DEG C, start water-cooled, stop water-cooled the temperature of 400～500 DEG C,
Make the steel plate of the various thicknesss of slab shown in table 2.
And then, it is tubulose by C punching press, U punching press, O punching press by steel formability, end face is carried out
Tack welding, is made for steel pipe after carrying out expander after interior outside is formally welded.It addition, formally weld
Connect and have employed submerged arc welding.
Tensile test specimen, HIC test specimen, macroscopic view test specimen is produced, for each from the steel plate obtained and steel pipe
Test.HIC test is carried out based on NACETM0284.It addition, use macroscopic view test specimen, pass through EPMA
Determine the degree of segregation of Mn, Nb, Ti.The mensuration of the degree of segregation that employing EPMA is carried out, with 50 μm
Beam diameter implement in the mensuration area of full thickness × 20mm width, measure Mn, Nb, Ti dense
Degree distribution, then, the dense position (center segregation portion) changed of each element in specimen thickness direction,
With the beam diameter of 2 μm in the concentration of each element of area test of 1mm × 1mm.
And then, the Vickers hardness of center segregation is determined based on JIS Z 2244.The mensuration of Vickers hardness
It is that load is set to 25g, in the distribution of the Mn concentration of the thickness direction determined by EPMA
The highest position of Mn concentration carry out.
Table 2 represent utilize the thickness of slab of steel plate that the steel 1～34 of table 1 respectively obtains, maximum Mn degree of segregation,
Nb degree of segregation, Ti degree of segregation, the length of non-nip portion, the maximum hardness in center segregation portion, tension
Intensity and the area occupation ratio (CAR) of crackle tried to achieve by HIC test.
It addition, table 3 represents the wall thickness of the steel pipe respectively obtained by the steel 1～34 of table 1, formally welding
Heat input, the area occupation ratio of the crackle tried to achieve by HIC test.It addition, the maximum Mn segregation of steel pipe
Degree, Nb degree of segregation, Ti degree of segregation, the length of non-nip portion, center segregation portion maximum hardness with
Steel plate is equal, and the tensile strength of steel pipe is than steel plate big 1～about 5%.
Steel 1～23 is the example of the present invention, these steel the steel plate obtained, and maximum Mn degree of segregation is
Less than 1.6, Nb degree of segregation be less than 4.0, Ti degree of segregation be less than 4.0, center segregation portion
High rigidity is below 300Hv, does not produce because HIC tests the crackle caused.These steel plates are made
Steel pipe for blank is also same.
On the other hand, steel 24～34 represents the comparative example beyond the scope of the present invention.I.e., substantially, become
Certain element in/is beyond the scope of the present invention, and therefore in HIC tests, CAR exceedes
3%.
Table 2
Table 3
Claims (10)
1. the effective steel plate of high-strength line-pipe that a hydrogen-induced cracking resistance is excellent, it is characterised in that with matter
Amount % meter, contains:
C:0.02～0.08%,
Si:0.01～0.5%,
Mn:1.0～1.6%,
Nb:0.001～0.10%,
Ca:0.0001～0.0050%,
N:0.0010～0.0050%,
O:0.0001～0.0030%,
And be limited to:
Below P:0.01%,
Below S:0.0020%,
Below Al:0.030%,
Below Ti:0.030%,
The content of S, Ca meets S/Ca ＜ 0.5,
Its surplus is made up of Fe and inevitable impurity element,
Further, the length of the non-nip portion in center segregation portion is limited in below 0.1mm.
The effective steel plate of high-strength line-pipe that hydrogen-induced cracking resistance the most according to claim 1 is excellent,
It is characterized in that, in terms of quality %, contain:
Ni:0.01～2.0%,
Cu:0.01～1.0%,
Cr:0.01～1.0%,
Mo:0.01～1.0%,
W:0.01～1.0%,
V:0.01～0.10%,
Zr:0.0001～0.050%,
Ta:0.0001～0.050%,
One or more among B:0.0001～0.0020%,
Its surplus is made up of Fe and inevitable impurity.
The high-strength line-pipe tube steel that hydrogen-induced cracking resistance the most according to claim 1 and 2 is excellent
Plate, it is characterised in that in terms of quality %, possibly together with:
REM:0.0001～0.01%,
Mg:0.0001～0.01%,
Y:0.0001～0.005%,
Hf:0.0001～0.005%,
One or more among Re:0.0001～0.005%.
The high-strength line-pipe tube steel that hydrogen-induced cracking resistance the most according to claim 1 and 2 is excellent
Plate, it is characterised in that
It is further limited to:
Maximum Mn degree of segregation: less than 2.0,
Nb degree of segregation: less than 4.0,
Ti degree of segregation: less than 4.0.
The high-strength line-pipe tube steel that hydrogen-induced cracking resistance the most according to claim 1 and 2 is excellent
Plate, it is characterised in that the maximum hardness in center segregation portion is below 300Hv.
6. the effective steel pipe of high-strength line-pipe that a hydrogen-induced cracking resistance is excellent, it is characterised in that with matter
Amount % meter, mother metal contains:
C:0.02～0.08%,
Si:0.01～0.5%,
Mn:1.0～1.6%,
Nb:0.001～0.10%,
Ca:0.0001～0.0050%,
N:0.0010～0.0050%,
O:0.0001～0.0030%,
And be limited to:
Below P:0.01%,
Below S:0.0020%,
Below Al:0.030%,
Below Ti:0.030%,
The content of S, Ca meets S/Ca ＜ 0.5,
Its surplus is made up of Fe and inevitable impurity element,
Further, the length of the non-nip portion in the center segregation portion of mother metal is limited in below 0.1mm.
The effective steel pipe of high-strength line-pipe that hydrogen-induced cracking resistance the most according to claim 6 is excellent,
It is characterized in that, in terms of quality %, mother metal contains:
Ni:0.01～2.0%,
Cu:0.01～1.0%,
Cr:0.01～1.0%,
Mo:0.01～1.0%,
W:0.01～1.0%,
V:0.01～0.10%,
Zr:0.0001～0.050%,
Ta:0.0001～0.050%,
One or more among B:0.0001～0.0020%.
Its surplus is made up of Fe and inevitable impurity,
8. according to the high-strength line-pipe tube steel that the hydrogen-induced cracking resistance described in claim 6 or 7 is excellent
Pipe, it is characterised in that in terms of quality %, mother metal possibly together with:
REM:0.0001～0.01%,
Mg:0.0001～0.01%,
Y:0.0001～0.005%,
Hf:0.0001～0.005%,
One or more among Re:0.0001～0.005%.
9. according to the high-strength line-pipe tube steel that the hydrogen-induced cracking resistance described in claim 6 or 7 is excellent
Pipe, it is characterised in that
It is further limited to: mother metal
Maximum Mn degree of segregation: less than 2.0,
Nb degree of segregation: less than 4.0,
Ti degree of segregation: less than 4.0.
10. effective according to the high-strength line-pipe that the hydrogen-induced cracking resistance described in claim 6 or 7 is excellent
Steel pipe, it is characterised in that the maximum hardness in the center segregation portion of mother metal is below 300Hv.
Applications Claiming Priority (5)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP2009-030314 | 2009-02-12 | ||
| JP2009030314 | 2009-02-12 | ||
| JP2009-253147 | 2009-11-04 | ||
| JP2009253147A JP5423323B2 (en) | 2009-02-12 | 2009-11-04 | Steel plate for high-strength line pipe and steel pipe for high-strength line pipe with excellent resistance to hydrogen-induced cracking |
| CN2010800075239A CN102317491A (en) | 2009-02-12 | 2010-02-12 | High-strength steel sheet and high-strength steel pipe having excellent hydrogen-induced cracking resistance for use in line pipe |
Related Parent Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN2010800075239A Division CN102317491A (en) | 2009-02-12 | 2010-02-12 | High-strength steel sheet and high-strength steel pipe having excellent hydrogen-induced cracking resistance for use in line pipe |
Publications (1)
| Publication Number | Publication Date |
|---|---|
| CN105838992A true CN105838992A (en) | 2016-08-10 |
Family
ID=42561894
Family Applications (2)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN201610208070.5A Pending CN105838992A (en) | 2009-02-12 | 2010-02-12 | High-strength steel sheet and high-strength steel pipe having excellent hydrogen-induced cracking resistance for use in line pipe |
| CN2010800075239A Pending CN102317491A (en) | 2009-02-12 | 2010-02-12 | High-strength steel sheet and high-strength steel pipe having excellent hydrogen-induced cracking resistance for use in line pipe |
Family Applications After (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| CN2010800075239A Pending CN102317491A (en) | 2009-02-12 | 2010-02-12 | High-strength steel sheet and high-strength steel pipe having excellent hydrogen-induced cracking resistance for use in line pipe |
Country Status (5)
| Country | Link |
|---|---|
| JP (1) | JP5423323B2 (en) |
| KR (2) | KR20110104111A (en) |
| CN (2) | CN105838992A (en) |
| BR (1) | BRPI1008563A2 (en) |
| WO (1) | WO2010093057A1 (en) |
Cited By (2)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN108456834A (en) * | 2018-03-05 | 2018-08-28 | 石英楠 | A kind of high-strength line-pipe steel and preparation method thereof with the precipitate containing Ti |
| CN113025902A (en) * | 2021-03-04 | 2021-06-25 | 东北大学 | Hot-rolled seamless steel tube with excellent toughness and manufacturing method thereof |
Families Citing this family (22)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| 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 |
| CA2755271A1 (en) * | 2009-03-12 | 2010-09-16 | Sumitomo Metal Industries, Ltd. | Hic-resistant thick steel plate and uoe steel pipe |
| BR112012004577A2 (en) * | 2009-09-02 | 2016-04-05 | Nippon Steel Corp | high strength pipeline steel and high strength pipeline steel with excellent low temperature toughness |
| WO2011030768A1 (en) * | 2009-09-09 | 2011-03-17 | 新日本製鐵株式会社 | Steel sheet for high-strength line pipe having excellent low-temperature toughness, and steel pipe for high-strength line pipe |
| JP5299579B2 (en) | 2010-09-03 | 2013-09-25 | 新日鐵住金株式会社 | High-strength steel sheet with excellent fracture and HIC resistance |
| JP5857491B2 (en) * | 2011-07-19 | 2016-02-10 | Ｊｆｅスチール株式会社 | Low yield ratio resistant HIC welded steel pipe with excellent weld toughness after SR and method for producing the same |
| JP5853456B2 (en) * | 2011-07-19 | 2016-02-09 | Ｊｆｅスチール株式会社 | Low yield ratio resistant HIC welded steel pipe with excellent weld toughness after SR and method for producing the same |
| 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 |
| JP5824401B2 (en) * | 2012-03-30 | 2015-11-25 | 株式会社神戸製鋼所 | Steel sheet with excellent resistance to hydrogen-induced cracking and method for producing the same |
| BR112014031808B1 (en) | 2012-06-18 | 2019-05-14 | Jfe Steel Corporation | METHOD FOR PRODUCING HIGH RESISTANCE, ACID RESISTANT AND THICK DRIVING TUBES. |
| RU2621093C2 (en) | 2012-07-09 | 2017-05-31 | ДжФЕ СТИЛ КОРПОРЕЙШН | Thick-walled high tensile sulphurous-gas resistant main pipe and method for its manufacture |
| KR101461730B1 (en) * | 2012-12-21 | 2014-11-14 | 주식회사 포스코 | Hot-rolled steel sheet having excellent hydrogen induced crack resistance and low temperature impact toughness and method of manufacturing the same |
| KR101490561B1 (en) * | 2012-12-21 | 2015-02-05 | 주식회사 포스코 | Hot-rolled steel sheet having excellent hydrogen induced crack resistance and yield ratio and method of manufacturing the same |
| CN103146997B (en) * | 2013-03-28 | 2015-08-26 | 宝山钢铁股份有限公司 | A kind of low-alloy high-flexibility wear-resistant steel plate and manufacture method thereof |
| CN103215513B (en) * | 2013-04-25 | 2016-03-30 | 宝山钢铁股份有限公司 | A kind of anticorrosive gathering-line pipe and manufacture method thereof |
| JP6584912B2 (en) * | 2014-12-26 | 2019-10-02 | 株式会社神戸製鋼所 | Steel plate and line pipe steel pipe with excellent hydrogen-induced crack resistance |
| JP2016125137A (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 |
| JP6642118B2 (en) * | 2016-03-02 | 2020-02-05 | 日本製鉄株式会社 | Sour-resistant steel plate |
| 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 |
| KR101889189B1 (en) * | 2016-12-22 | 2018-08-16 | 주식회사 포스코 | Ts 450mpa grade heavy guage steel sheet having excellent resistance to hydrogen induced cracking and method of manufacturing the same |
| CN109694991A (en) * | 2017-10-20 | 2019-04-30 | 鞍钢股份有限公司 | A kind of tank plate that hydrogen induced cracking resistance can be excellent |
| KR101999027B1 (en) * | 2017-12-26 | 2019-07-10 | 주식회사 포스코 | Steel for pressure vessel having excellent resistance to hydrogen induced cracking and method of manufacturing the same |
Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH06220577A (en) * | 1993-01-26 | 1994-08-09 | Kawasaki Steel Corp | High tensile strength steel excellent in hic resistance and its production |
| JP2004003015A (en) * | 2002-04-26 | 2004-01-08 | Jfe Steel Kk | High-strength steel sheet for line pipe superior in hic resistance, and manufacturing method therefor |
| 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 |
| CN1894434A (en) * | 2003-12-19 | 2007-01-10 | 新日本制铁株式会社 | Steel plates for ultra-high-strength linepipes and ultra-high-strength linepipes having excellent low-temperature toughness and manufacturing methods thereof |
| CN102317491A (en) * | 2009-02-12 | 2012-01-11 | 新日本制铁株式会社 | High-strength steel sheet and high-strength steel pipe having excellent hydrogen-induced cracking resistance for use in line pipe |
Family Cites Families (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH04259352A (en) * | 1991-02-14 | 1992-09-14 | Nkk Corp | Steel excellent in hydrogen-induced cracking resistance and its manufacture |
| JPH06256894A (en) * | 1993-03-08 | 1994-09-13 | Nippon Steel Corp | High strength line pipe excellent in hydrogen induced cracking resistance |
| JP4508087B2 (en) * | 2005-11-17 | 2010-07-21 | 住友金属工業株式会社 | Continuous casting method and continuous cast slab |
-
2009
- 2009-11-04 JP JP2009253147A patent/JP5423323B2/en active Active
-
2010
- 2010-02-12 BR BRPI1008563A patent/BRPI1008563A2/en not_active Application Discontinuation
- 2010-02-12 KR KR1020117018676A patent/KR20110104111A/en active Application Filing
- 2010-02-12 CN CN201610208070.5A patent/CN105838992A/en active Pending
- 2010-02-12 KR KR1020137023805A patent/KR101524397B1/en active IP Right Grant
- 2010-02-12 CN CN2010800075239A patent/CN102317491A/en active Pending
- 2010-02-12 WO PCT/JP2010/052483 patent/WO2010093057A1/en active Application Filing
Patent Citations (5)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPH06220577A (en) * | 1993-01-26 | 1994-08-09 | Kawasaki Steel Corp | High tensile strength steel excellent in hic resistance and its production |
| JP2004003015A (en) * | 2002-04-26 | 2004-01-08 | Jfe Steel Kk | High-strength steel sheet for line pipe superior in hic resistance, and manufacturing method therefor |
| CN1894434A (en) * | 2003-12-19 | 2007-01-10 | 新日本制铁株式会社 | Steel plates for ultra-high-strength linepipes and ultra-high-strength linepipes having excellent low-temperature toughness and manufacturing methods 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 |
| CN102317491A (en) * | 2009-02-12 | 2012-01-11 | 新日本制铁株式会社 | High-strength steel sheet and high-strength steel pipe having excellent hydrogen-induced cracking resistance for use in line pipe |
Cited By (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN108456834A (en) * | 2018-03-05 | 2018-08-28 | 石英楠 | A kind of high-strength line-pipe steel and preparation method thereof with the precipitate containing Ti |
| CN108456834B (en) * | 2018-03-05 | 2020-04-24 | 白婷婷 | High-strength pipeline steel containing Ti precipitates and preparation method thereof |
| CN113025902A (en) * | 2021-03-04 | 2021-06-25 | 东北大学 | Hot-rolled seamless steel tube with excellent toughness and manufacturing method thereof |
Also Published As
| Publication number | Publication date |
|---|---|
| CN102317491A (en) | 2012-01-11 |
| JP2010209460A (en) | 2010-09-24 |
| KR20130105941A (en) | 2013-09-26 |
| KR20110104111A (en) | 2011-09-21 |
| BRPI1008563A2 (en) | 2016-03-15 |
| JP5423323B2 (en) | 2014-02-19 |
| KR101524397B1 (en) | 2015-06-04 |
| WO2010093057A1 (en) | 2010-08-19 |
Similar Documents
| Publication | Publication Date | Title |
|---|---|---|
| CN105838992A (en) | High-strength steel sheet and high-strength steel pipe having excellent hydrogen-induced cracking resistance for use in line pipe | |
| KR101615842B1 (en) | 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 | |
| JP6542249B2 (en) | Ferritic stainless steel sheet, steel pipe and method for manufacturing the same | |
| KR101312901B1 (en) | High-strength steel sheet and high-strength steel pipe having excellent hydrogen-induced cracking resistance for use in line pipe | |
| EP3026138B1 (en) | High-strength steel material for oil well use, and oil well pipe | |
| JP5679114B2 (en) | Low yield ratio high strength hot rolled steel sheet with excellent low temperature toughness and method for producing the same | |
| RU2694393C2 (en) | High-strength steel material for oil well and pipes used in oil industry | |
| US10988819B2 (en) | High-strength steel material and production method therefor | |
| JP2009174006A (en) | Hot rolled steel sheet as stock for steel tube for hydroforming, steel tube for hydroforming, and their manufacturing methods | |
| JP4462452B1 (en) | Manufacturing method of high alloy pipe | |
| EP3006585B1 (en) | Seamless steel pipe for line pipe used in sour environment | |
| JP2012031509A (en) | High strength low yield ratio steel with highly uniform elongation characteristic, method of producing the same and high strength low yield ratio welded steel pipe | |
| JP2016191150A (en) | Stainless steel sheet excellent in toughness and production method thereof | |
| EP3018229B1 (en) | Seamless steel tube for line pipe used in acidic environment and method for its manufacture | |
| JP2008088547A (en) | Fire-resistant steel having excellent high-temperature strength, toughness and reheat embrittlement resistance and process for production of the same | |
| JP7127753B2 (en) | Steel plate and its manufacturing method | |
| JP4093177B2 (en) | Steel material for hydrofoam, electric sewing tube for hydrofoam, and manufacturing method thereof | |
| JP7155703B2 (en) | Thick steel plate for line pipe and manufacturing method thereof | |
| JP6213683B2 (en) | Steel and pipe for oil expansion | |
| WO2014024234A1 (en) | Steel plate for high strength steel pipe and high strength steel pipe | |
| JP7348553B2 (en) | oil country tubing | |
| JP2022089302A (en) | Austenitic stainless steel sheet and steel pipe and method for producing the same |
Legal Events
| Date | Code | Title | Description |
|---|---|---|---|
| C06 | Publication | ||
| PB01 | Publication | ||
| C10 | Entry into substantive examination | ||
| SE01 | Entry into force of request for substantive examination | ||
| CB02 | Change of applicant information | ||
| CB02 | Change of applicant information |
Address after: Tokyo, Japan, Japan Applicant after: Nippon Iron & Steel Corporation Address before: Tokyo, Japan, Japan Applicant before: Nippon Steel Corporation |
|
| RJ01 | Rejection of invention patent application after publication | ||
| RJ01 | Rejection of invention patent application after publication |
Application publication date: 20160810 |