CN108779525A - The high intensity pole steel plate and its manufacturing method of excellent in brittle-cracking propagation stopping characteristics - Google Patents
The high intensity pole steel plate and its manufacturing method of excellent in brittle-cracking propagation stopping characteristics Download PDFInfo
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- CN108779525A CN108779525A CN201780013041.6A CN201780013041A CN108779525A CN 108779525 A CN108779525 A CN 108779525A CN 201780013041 A CN201780013041 A CN 201780013041A CN 108779525 A CN108779525 A CN 108779525A
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- 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
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- 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
-
- 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
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- 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
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- 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
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- 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
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- 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
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- 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
- C22C38/18—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
Abstract
The purpose of the present invention is to provide high intensity pole steel plates and its manufacturing method that plate thickness is 70mm or more and excellent in brittle-cracking propagation stopping characteristics.A kind of high intensity pole steel plate of the excellent in brittle-cracking propagation stopping characteristics of plate thickness 70mm or more has and contains C in terms of quality %：0.03~0.20%, Si：0.03~0.5%, Mn：0.5~2.2%, P：0.01% or less, S：0.005% or less, Ti：0.005~0.03%, Al：0.005~0.080% and N：0.0050% or less, the Ceq defined by following formula (1) be 0.36 or more and 0.40 or less and surplus by Fe and inevitable impurity constitute at being grouped as, and the texture that (200) face aggregation degree in the rolling surface that (211) face aggregation degree in the rolling surface with plate thickness center is 1.2 or more, surface of steel plate is 1.7 or more, Charpy fracture transition temperature vTrs at 1/4 position of plate thickness is -40 DEG C hereinafter, the Charpy fracture transition temperature vTrs at surface of steel plate is -80 DEG C or less.
Description
Technical field
The present invention relates to make in the large structures such as ship, marine structure, low-temperature storage tank, building/civil structure object
, plate thickness 70mm or more excellent in brittle-cracking propagation stopping characteristics high intensity pole steel plate and its manufacturing method.
Background technology
For the large structures such as ship, marine structure, low-temperature storage tank, building/civil structure object, companion occurs
With brittle fracture generate accident when, be affected to what social economy, environment etc. were brought.Therefore, above-mentioned large structure warp
The raising of safety is often required, for the steel plate of the former material as large structure, at use temperature crisp is required with high level
Property crack propagation stop performance.
The ships such as container ship, bulk carrier use the steel plate of high intensity as ship hull plate in its structure.Recently,
Along with the enlargement of hull, it is desirable that further high intensity is promoting the wall thickening of the steel plate as former material.
In general, what the brittle-cracking propagation stopping characteristics of steel plate were then more deteriorated with high intensity or heavy wall
Tendency.Therefore, for the steel plate used in large structure, the requirement to brittle-cracking propagation stopping characteristics also further carries
It is high.
Here, as the means for making the brittle-cracking propagation stopping characteristics of steel plate improve, it has been known that there is increase steel back and forth
In Ni contents method.For example, for the holding vessel of liquefied natural gas (LNG), 9%Ni is used under commercial size
Steel.
But the increase of Ni contents forces manufacturing cost to be sharply increased in steel.Therefore, 9%Ni steel is dfficult to apply to LNG storages
Deposit the purposes other than tank.
On the other hand, small for plate thickness that extremely low temperature as LNG is not achieved, being used in such as ship or line pipe
In the relatively thin steel plate of 50mm, grain refined is realized by TMCP methods, low-temperature flexibility is made to improve, it is excellent crisp thereby, it is possible to realize
Property crack propagation stop performance.
In addition, in order to which cost of alloy is raised to improve brittle-cracking propagation stopping characteristics in the case that not making, in patent text
Offer steel plate obtained from the tissue micronization proposed in 1 by surface section.
The steel plate of excellent in brittle-cracking propagation stopping characteristics described in patent document 1 is when being conceived to brittle-cracking propagation
The raising of brittle-cracking propagation stopping characteristics is effectively completed in the shear lip (plastic deformation area) that steel plate surface section generates
, which is characterized in that by making the crystal grain miniaturization of shearing lip portion propagate energy possessed by the brittle crack of propagation to absorb
Amount.In addition, describing in patent document 1：It is cooled down by the control after hot rolling and surface section is cooled to Ar3Transformation temperature hereinafter,
Then, stop control cooling, by surface section re-heat to Ar3More than transformation temperature, above-mentioned operation is repeated more than primary, herein
Period depresses steel plate, it is thus made to repeated phase transformation or processing recrystallization, is generated as a result, in surface part ultra tiny
Ferritic structure or bainite structure.
It describes in patent document 2：For the steel plate of the microscopic structure based on ferrite-pearlite, it is
Raising brittle-cracking propagation stopping characteristics, it is important that make two surface elements of steel plate by be 50% or more with area occupation ratio tool
There is round equivalent grain size：5 μm or less and draw ratio：The ferritic structure of 2 or more ferrite crystal grain is constituted, and inhibits iron plain
The unevenness of body crystallization particle diameter；As the method for inhibiting the unevenness, the maximum depression rate of every a time in finish rolling is set as
Thus 12% hereinafter, inhibit the recrystallization phenomenon of part.
The technology in terms of a kind of extension of TMCP is described in patent document 3, is not only conceived to ferrite crystal grain
Miniaturization, and it is conceived to the subgrain formed in ferrite crystal grain, thus brittle-cracking propagation stopping characteristics is made to improve.Specifically
For, describe following technology：For plate thickness is the steel plate of 30~40mm, the cooling on steel plate surface layer need not be carried out and answered
The temperature of the complexity such as heat controls, and so that brittle-cracking propagation stopping characteristics is improved by following conditions, the condition is：(a) ensure
Rolling condition, (b) of fine ferrite crystal grain generate rolling for fine ferrite structure in 5% or more part of steel plate plate thickness
Condition processed, (c) make texture flourishing in fine ferrite and will be by dislocation progress that processing (rolling) introduces using thermal energy
It is reconfigured and forms the rolling condition of subgrain and (d) inhibit to be formed by the thick of fine ferrite crystal grain and fine subgrain
The cooling condition changed greatly.
In addition, it is also known that following method：In controlled rolling, pressure is implemented to the ferrite after phase transformation and texture is made to send out
It reaches, thus brittle-cracking propagation stopping characteristics is made to improve.In this method, along the side parallel with plate face on the plane of disruption of steel
To separation is generated, so that the stress of brittle crack front end is mitigated, thus improve the resistance to brittle fracture.
For example, describing in patent document 4：By controlled rolling make (110) face X-ray intensity ratio be 2 or more and
The area occupation ratio of the coarse grain of round 20 μm of equivalent diameter or more is set to be 10% hereinafter, thus making resistance to brittle fracture characteristic raising.
In patent document 5, the steel for welded structures as the excellent in brittle-cracking propagation stopping characteristics of connector portions, it is open
A kind of X-ray surface intensity in (100) face in rolling surface being characterized in that in plate thickness is recorded than the steel plate for 1.5 or more
By the angle in caused by texture prosperity mechanical load direction and crack propagation direction it is inconsistent by make brittle crack
Propagation halt characteristic is excellent.
In addition, describing a kind of excellent steel for welded structures of brittle-cracking propagation stopping characteristics in patent document 6
The manufacturing method of plate, wherein in each portion's (plate thickness in plate thickness direction by being provided to the average reduction ratio in controlled rolling
1/4 position, plate thickness central portion etc.) keep texture flourishing.
In addition, recently be more than 6000TEU Large Container Ship in, use plate thickness for 70mm or more steel plate.?
In non-patent literature 1, the brittle-cracking propagation stopping characteristics for the steel plate that plate thickness is 65mm are evaluated, and reports in mother
The large-scale brittle-cracking propagation of material stops the result that brittle crack will not stop in experiment.
Existing technical literature
Patent document
Patent document 1：Japanese Patent Publication 7-100814 bulletins
Patent document 2：Japanese Unexamined Patent Publication 2002-256375 bulletins
Patent document 3：No. 3467767 bulletins of Japanese Patent No.
Patent document 4：No. 3548349 bulletins of Japanese Patent No.
Patent document 5：No. 2659661 bulletins of Japanese Patent No.
Patent document 6：No. 5733425 bulletins of Japanese Patent No.
Non-patent literature
Non-patent literature 1：Thick hand shipbuilding splits Den with the big brittleness I of Steel To お け Ru Long and broadcasts Behavior Move (heavy wall makes the length of hull steel
Big brittle-cracking propagation behavior), Japanese ship ocean engineering joint performance say the 3rd phase of collection of thesis, 2006, pp359-362
Invention content
Problem to be solved by the invention
In technology described in patent document 1,2, by only will steel plate surface section it is temporarily cooling after make its re-heat and
Implement processing in re-heat and is specifically organized.Therefore, it is difficult to control under actual production scale, especially for plate thickness
In manufacture for the thick-wall materials of 70mm or more, it is to rolling equipment, cools down the big technique of the load of equipment.
In addition, for the steel plate described in Patent Documents 1 to 6, from the point of view of manufacturing condition, disclosed experimental data,
With plate thickness：The steel plate of about 50mm~about 70mm is main object, for the application in the thick-wall materials of 70mm or more, it is unclear that
Scheduled characteristic can be obtained, for the crack propagation characteristic in the plate thickness direction needed for large structure, is not tested completely
Card.
In addition, in non-patent literature 1, the ESSO experiments of material to be tested show the value of the Kca at -10 DEG C of temperature in use
Less than 3000N/mm1.5As a result, implying that：It is being more than the steel of 50mm using plate thickness for the technology of non-patent literature 1
In the case of the large structure of plate, it is sufficient that can not say that safety ensures.
The present invention is 70mm or more and brittle-cracking propagation stopping characteristics its purpose is to provide plate thickness in view of the foregoing
Excellent high intensity pole steel plate and its manufacturing method.
The method for solving problem
To solve the above-mentioned problems, the present inventor couple has excellent brittle-cracking propagation plate thickness is 70mm or more
Research has been repeated in the high intensity pole steel plate of stop performance and the manufacturing method for stably obtaining the steel plate.As a result, it has been found that
(211) face aggregation degree in rolling surface with plate thickness center is 1.2 or more and surface of steel plate (being only called sometimes on " surface ")
It is texture that (200) face aggregation degree in rolling surface is 1.7 or more, disconnected as the Charpy at 1/4 position of plate thickness of the index of toughness
It with the Charpy fracture transition temperature vTrs at surface of steel plate is -80 DEG C of extremely thickness below that mouthful transition temperature vTrs, which be -40 DEG C or less,
Steel plate has extremely excellent brittle-cracking propagation stopping characteristics.
The present invention further studies above-mentioned opinion and completes.The purport of the present invention constitutes as described below.
[1] a kind of high intensity pole steel plate of the excellent in brittle-cracking propagation stopping characteristics of plate thickness 70mm or more has such as
It is lower at being grouped as：Contain C in terms of quality %：0.03~0.20%, Si：0.03~0.5%, Mn：0.5~2.2%, P：0.01%
Below, S：0.005% or less, Ti：0.005~0.03%, Al：0.005~0.080% and N：0.0050% hereinafter, by following
The Ceq that formula (1) defines is 0.36 or more and 0.40 hereinafter, surplus is made of Fe and inevitable impurity,
And in the rolling surface that (211) face aggregation degree in the rolling surface with plate thickness center is 1.2 or more, surface of steel plate
(200) face aggregation degree be 1.7 or more texture,
Charpy fracture transition temperature vTrs at 1/4 position of plate thickness be -40 DEG C hereinafter,
Charpy fracture transition temperature vTrs at surface of steel plate is -80 DEG C or less.
Ceq=C+Mn/6+Cu/15+Ni/15+Cr/5+Mo/5+V/5 ... (1)
Here, C, Mn, Cu, Ni, Cr, Mo and V in formula (1) indicate the content (quality %) of each element, without containing when set
It is 0.
[2] the high intensity pole steel plate of the excellent in brittle-cracking propagation stopping characteristics as described in [1], wherein mentioned component
Composition also contains Nb in terms of quality %：0.005~0.05%, Cu：0.05~1.0%, Ni：0.05~1.5% and Cr：0.01~
One or more of 0.5%.
[3] the high intensity pole steel plate of the excellent in brittle-cracking propagation stopping characteristics as described in [1] or [2], wherein above-mentioned
Also contain Mo in terms of quality % at being grouped as：0.01~0.5%, V：0.001~0.10%, B：0.0030% or less, Ca：
0.0050% or less, REM：One or more of 0.0100% or less.
[4] a kind of manufacturer of the high intensity pole steel plate of the excellent in brittle-cracking propagation stopping characteristics of plate thickness 70mm or more
Method will have the temperature that 1000~1200 DEG C are heated at the steel former material being grouped as described in any one of [1]~[3], then,
Temperature accumulating within the scope of the austenite recrystallization temperature temperature that reduction ratio is 10% or more, plate thickness center in plate thickness center
Accumulation reduction ratio within the scope of austenite non-recrystallization temperature is 50% or more, plate thickness surface temperature in Ar3Below transformation temperature
And the temperature in plate thickness center is in Ar3Accumulation reduction ratio when more than transformation temperature temperature range carries out heat under conditions of being more than 20%
It rolls, then, 500 DEG C of cooling stopping temperature below is cooled to the cooling velocity of 0.5 DEG C/s or more.
[5] manufacturing method of the high intensity pole steel plate of the excellent in brittle-cracking propagation stopping characteristics as described in [4],
In, after being cooled to 500 DEG C of cooling stopping temperature below, the temperature in plate thickness center is less than Ac1The temperature of transformation temperature is returned
Fire.
Invention effect
According to the present invention, the texture in plate thickness direction obtains suitable control, therefore, even the extremely thick steel of plate thickness 70mm or more
Plate, brittle-cracking propagation stopping characteristics are also excellent, and toughness is also excellent and is high intensity.In addition, according to the present invention, by right
Rolling condition optimizes, can be industrially to manufacture to extremely easy process stabilizing high intensity pole steel plate.For example, incite somebody to action this
The high intensity pole steel plate of invention is applied to be engaged in the strength deck portion structure of the container ship in shipbuilding field, bulk carrier
The deck component of hatch gusset plate, thereby assisting in ship, the safety is improved, industrially exceedingly useful.
Specific implementation mode
Hereinafter, embodiments of the present invention will be described.It should be noted that the present invention is not limited to embodiment party below
Formula.
< is at being grouped as >
Hereinafter, being illustrated to each ingredient.It should be noted that " % " of the content of expression composition refers to " quality % ".
C：0.03~0.20%
C is the element for the intensity for improving steel.In the present invention, in order to ensure desired intensity, C content is set as
0.03% or more.In addition, when C content is more than 0.20%, not only weldability deteriorates, and can also generate harmful effect to toughness.Therefore,
C content is set as 0.03~0.20% range.It should be noted that lower limit is preferably 0.05% or more.The upper limit is preferably
0.15% or less.
Si：0.03~0.5%
Intensified elements of the Si as deoxidant element and as steel is effective.When Si contents are less than 0.03%, it cannot get these
Effect.On the other hand, when Si contents are more than 0.5%, the surface texture of steel can be not only damaged, but also toughness extremely deteriorates.Therefore,
Si contents are set as 0.03~0.5% range.
Mn：0.5~2.2%
Mn as intensified element and by containing.When Mn contents are less than 0.5%, effect is insufficient.On the other hand, it is more than
When 2.2%, weldability deterioration, steel plate cost also increases.Therefore, Mn contents are set as 0.5~2.2% range.
P：0.01% or less, S：0.005% or less
P, S is the inevitable impurity in steel.When their content increases, toughness deterioration.For plate thickness 70mm or more
Steel plate for, in order to ensure good toughness, by P content be suppressed to 0.01% hereinafter, by S contents be suppressed to 0.005% with
Under.It should be noted that it is preferred range that P content, which is 0.006% or less, S contents are 0.003% or less.
Ti：0.005~0.03%
Ti forms nitride, carbide or carbonitride by micro by containing, and having makes crystal grain miniaturization and improve
The effect of base metal tenacity.Its effect is by making Ti contents be obtained for 0.005% or more.On the other hand, Ti contents are more than
When 0.03%, the toughness of base material and welding heat affected zone reduces.Therefore, Ti contents are set as 0.005~0.03% range.
Al：0.005~0.080%
Al plays a role as deoxidier.In order to use Al as deoxidier, need Al content being set as 0.005%
More than.In addition, when Al content is more than 0.080%, toughness reduces, and the toughness in welding metal portion reduces when being welded.Cause
This, Al content is set as 0.005~0.080% range.It should be noted that lower limit is preferably 0.020% or more.The upper limit is excellent
It is selected as 0.060% or less.
N：0.0050% or less
N and the Al in steel in conjunction with and crystallization particle diameter when adjusting rolling processing, so that steel is strengthened.The effect in order to obtain, it is excellent
N content is set as 0.0010% or more by choosing.On the other hand, when N content is more than 0.0050%, toughness deterioration.In the present invention,
N content is set as 0.0050% range below.
It is the basis composition of the present invention above, surplus is Fe and inevitable impurity.
In the present invention, in order to further increase characteristic, can contain on the basis of mentioned component forms Nb, Cu, Ni,
One or more of Cr.
Nb：0.005~0.05%
Nb is precipitated in the form of NbC in ferrite transformation or when reheating, and contributes to high intensity.In addition, Nb has
Make the widened effect in non-recrystallization region in the rolling of austenitic area, contributes to ferritic grain refined.Therefore, Nb contains
It is also effective for the improvement of toughness.Its effect is by making Nb contents be played for 0.005% or more.Nb contents are more than 0.05%
When, coarse NbC is precipitated, sometimes results in the reduction of toughness.Therefore, containing Nb, preferably Nb contents are set
It is 0.005~0.05%.
Cu：0.05~1.0%
Cu is the element for the quenching degree for improving steel.The element can in order to directly contribute to rolling after intensity improve and
It improves the functions such as toughness, elevated temperature strength or weatherability and contains.These effects are by making Cu contents be played for 0.05% or more.
On the other hand, excessive Cu, which contains, can make toughness, weldability deterioration.It is sufficient as ensuring in the steel plate more than plate thickness 70mm
Intensity and do not make toughness, the range of weldability deterioration, Cu contents are preferably set to 0.05~1.0%.
Ni：0.05~1.5%
Ni is the element for the quenching degree for improving steel.Ni can be improved and be improved to directly contribute to the intensity after rolling
The functions such as toughness, elevated temperature strength or weatherability and contain.These effects are by making Ni contents be played for 0.05% or more.It is another
Aspect, excessive Ni, which contains, can make toughness, weldability deterioration.As ensuring sufficient intensity in the steel plate more than plate thickness 70mm
And toughness, the range of weldability deterioration are not made, Ni contents are preferably set to 0.05~1.5%.
Cr：0.01~0.5%
Cr is the element for the quenching degree for improving steel.The element can in order to directly contribute to rolling after intensity improve and
It improves the functions such as toughness, elevated temperature strength or weatherability and contains.These effects are by making Cr contents be played for 0.01% or more.
On the other hand, excessive containing toughness, weldability deterioration can be made.Even if being filled as being also ensured that in the steel plate more than plate thickness 70mm
The intensity divided and the range for not making toughness, weldability deteriorate, Cr contents are preferably set to 0.01~0.5%.
In the present invention, in order to further increase characteristic, can contain on the basis of mentioned component forms Mo, V, B,
One or more of Ca, REM.
Mo：0.01~0.5%
Mo is the element for the quenching degree for improving steel.The element can improve simultaneously to directly contribute to the intensity after rolling
And it improves the functions such as toughness, elevated temperature strength or weatherability and contains.These effects are by making Mo contents be sent out for 0.01% or more
It waves.On the other hand, excessive containing toughness, weldability deterioration can be made.Even if being that 70mm or more is also ensured that adequately as plate thickness
Intensity and do not make toughness, the range of weldability deterioration, Mo contents are preferably set to 0.01~0.5%.
V：0.001~0.10%
V is the element for making the intensity of steel improve by the precipitation strength of precipitation in the form of V (CN).The effect is by making
V content plays for 0.001% or more.But V content, when being more than 0.10%, toughness reduces sometimes.Therefore, in the feelings containing V
Under condition, V content is preferably set as to 0.001~0.10% range.
B：0.0030% or less
B is the element for the quenching degree for improving steel, is obtained even if B content is 0.0030% or less such micro lower
To said effect.In addition, when B content is more than 0.0030%, the toughness of weld part reduces.Therefore, excellent containing B
B content is set as 0.0030% or less by choosing.It should be noted that from the viewpoint of obtaining said effect, the lower limit of B content
It is preferably set to 0.0006%.
Ca：0.0050% or less, REM：0.0100% or less
Ca, REM make the tissue miniaturization of welding heat affected zone and improve toughness.It will not be damaged containing these ingredients
Therefore the effect of the present invention can contain as needed.But excessively coarse field trash is formed sometimes and is made containing sometimes
The toughness of base material deteriorates.Therefore, containing these ingredients, the upper limit of content is preferably set as Ca：0.0050%,
REM：0.0100%.
Ceq：0.36 or more and 0.40 or less
The present invention high intensity pole steel plate in, in addition to it is each at being grouped as in the range of above-mentioned content other than, will be under
The Ceq for stating formula (1) expression is adjusted to 0.36 or more and 0.40 or less.When Ceq is less than 0.36, it is difficult to improve the rolling in plate thickness center
(211) face aggregation degree in face.In addition, in order to ensure weldability, Ceq is set as 0.40 or less.
Ceq=C+Mn/6+Cu/15+Ni/15+Cr/5+Mo/5+V/5 ... (1)
C, Mn, Cu, Ni, Cr, Mo and V in formula (1) indicate the content (quality %) of each element, without containing when be set as 0.
< texture >
The high intensity pole steel plate of the present invention have (211) face aggregation degree satisfaction 1.2 in the rolling surface in plate thickness center with
(200) face aggregation degree in upper, surface (from the range of 1mm under surface most surface) rolling surface meets 1.7 or more texture.
It, can be with by using above-mentioned at being grouped as and be controlled such that texture meets above range using aftermentioned manufacturing condition
Obtain the high intensity pole steel plate of excellent in brittle-cracking propagation stopping characteristics.
As described above, in the present invention, by the control being grouped as with texture, even if plate thickness is 70mm or more, this hair
Bright high intensity pole steel plate also has effect as intensity, toughness and excellent in brittle-cracking propagation stopping characteristics.
< manufacturing methods >
The molten steel of mentioned component composition is subjected to melting using converter etc., steel former material (steel is made by continuously casting etc.
Base), after being heated to 1000~1200 DEG C, carry out hot rolling.
When heating temperature is less than 1000 DEG C, be unable to fully to ensure to carry out the rolling within the scope of austenite recrystallization temperature when
Between.On the other hand, when heating temperature is more than 1200 DEG C, austenite grain coarsening leads to the reduction of toughness, moreover, oxygen
Changing loss becomes notable, and yield rate reduces.Therefore, the heating temperature of steel former material is set as 1000~1200 DEG C of range.From carrying
From the viewpoint of the toughness of high steel plate, the lower limit of the range of preferred heating temperature is 1000 DEG C or more, the upper limit be 1150 DEG C with
Under.It should be noted that the temperature of steel former material refers to the temperature in the plate thickness center of steel plate.
In hot rolling, carrying out accumulation reduction ratio of the temperature in plate thickness center within the scope of austenite recrystallization temperature first is
10% or more rolling.By the way that the accumulation reduction ratio in the temperature range is set as 10% or more, plate thickness 1/4 can be realized
The Charpy fracture transition temperature (vTrs) for setting place is -40 DEG C or less.When accumulating reduction ratio less than 10%, the grain refined of austenite is not
Fully, toughness will not improve, and cannot achieve the Charpy fracture transition temperature at 1/4 position of plate thickness is -40 DEG C or less.Above-mentioned accumulation
The upper limit of reduction ratio is not particularly limited, but since the improvement effect of grain refined becomes smaller, and above-mentioned accumulation reduction ratio is preferably
45% or less.It should be noted that in the case where the present invention is at being grouped as, above-mentioned condition preferably includes in above-mentioned hot rolling
Accumulation reduction ratio within the scope of temperature in 1100~950 DEG C is 10% or more.
In turn, carry out accumulation reduction ratio of the temperature in plate thickness center within the scope of austenite non-recrystallization temperature for 50% with
On rolling.By the way that the accumulation reduction ratio in the temperature range is set as 50% or more, the rolling in plate thickness center can be obtained
The texture that (211) face aggregation degree in face is 1.2 or more.Conversely, when the accumulation reduction ratio in the temperature range is less than 50%, obtain
Less than the texture that (211) face aggregation degree in the rolling surface in plate thickness center is 1.2 or more.The upper limit of above-mentioned accumulation reduction ratio does not have
It is particularly limited to, but in order not to hinder rolling efficiency, preferably 75% or less.It should be noted that in the present invention at being grouped as
In the case of, it is 50% that above-mentioned condition is preferably included in the accumulation reduction ratio within the scope of the temperature in 950~700 DEG C in hot rolling
More than.
In turn, in the present invention, in hot rolling, plate thickness surface temperature is in Ar3Below transformation temperature and the temperature in plate thickness center
In Ar3Accumulation reduction ratio when more than transformation temperature temperature range is more than 20%.Be important condition in the present invention, by
Hot rolling is carried out under this condition, and (200) face aggregation degree in the rolling surface of surface of steel plate can be made flourishing.Moreover, by this
Hot rolling is carried out under part, it is at 1.7 or more, surface of steel plate that can obtain (200) face aggregation degree in the rolling surface of surface of steel plate
Charpy fracture transition temperature (vTrs) is -80 DEG C or less.If plate thickness surface accumulated in the temperature range reduction ratio be 20% with
Under, then it cannot get desired texture and vTrs.Here, Ar3Transformation temperature is expressed from the next.
Ar3=910-310C-80Mn-20Cu-15Cr-55Ni-80Mo
The symbol of element in above-mentioned formula indicates the content (quality %) of each element, without containing when be set as 0.
It should be noted that the temperature on surface is in Ar3Be suitable in range below transformation temperature rolling temperature range be
Ar3Transformation temperature~(Ar3Transformation temperature -80) DEG C.In addition, the temperature in plate thickness center is in Ar3It is suitable for rolling in range more than transformation temperature
The temperature range of system is (Ar3Transformation temperature+80) DEG C~Ar3Transformation temperature.
In addition, in hot rolling in the present invention, be not intended to limit it is above-mentioned as defined in rolling outside temperature range, at least in above-mentioned rule
The pressure of accumulation reduction ratio as defined in being carried out within the scope of fixed temperature.
It will terminate the steel plate after rolling and 500 DEG C of cooling stopping temperature below are cooled to the cooling velocity of 0.5 DEG C/s or more
Degree.When cooling velocity is less than 0.5 DEG C/s, (211) face aggregation degree being unable to ensure in the rolling surface of plate thickness central position is 1.2
More than.In addition, when cooling stopping temperature being unsatisfactory for 500 DEG C or less, it is unable to get desired intensity and texture.
In turn, it in the case where carrying out temper after being cooled to 500 DEG C of cooling stopping temperature below, needs in plate thickness
The temperature in center is less than Ac1It is carried out at a temperature of transformation temperature.This is because temper is Ac1When more than transformation temperature, rolling
When so that flourishing texture is disappeared.Here, Ac1Transformation temperature is expressed from the next.
Ac1=751-26.6C+17.6Si-11.6Mn-169Al-23Cu-23Ni+24.1Cr+22.5Mo+23 3Nb-
39.7V-5.7Ti-895B
The symbol of element in formula indicates the content (quality %) of each element, without containing when be set as 0.
It should be noted that in the above description, the temperature in plate thickness center is according to the steel measured using radiation thermometer
Plate surface temperature is found out by Calculation of Heat Transfer.In addition, rolling after cooling condition in temperature condition be set as plate thickness center
Temperature, cooling velocity also refers to the average cooling rate that the temperature based on plate thickness center calculates.
Embodiment
Then, the embodiment of the present invention is illustrated.
Melting respectively will be carried out using converter at the molten steel being grouped as shown in table 1, steel former material is made by continuous casting process.
It after plate thickness is hot-rolled down to 70~100mm, is cooled down, is obtained shown in table 2 for trying steel.Heating condition, hot rolling item are shown in table 2
Part, cooling condition.In addition, for being tempered after cooling for trying steel, it is also shown that temperature.
For obtained steel plate, the JIS 14A test films of Φ 14mm are cut from 1/4 position of plate thickness, carry out stretching examination
It tests, measures yield strength (YS), tensile strength (TS).The situation that YS is 390MPa or more, TS is 510MPa or more is evaluated as
Well.
From 1/4 position of plate thickness and surface of steel plate, in a manner of keeping the lengthwise direction of test film parallel with rolling direction
No. 4 impact test pieces of JIS are cut, Charpy-type test is carried out, finds out Charpy fracture transition temperature (vTrs).By plate thickness 1/4
It is good that the situation that the vTrs set is -40 DEG C or less, the vTrs of surface of steel plate is -80 DEG C or less is evaluated as toughness.
In addition, in order to which the texture to steel plate is evaluated, (211) face measured respectively in the rolling surface in plate thickness center is gathered
(200) face aggregation degree in the rolling surface of degree and surface of steel plate (surface of steel plate refers to from the range of 1mm under surface most surface).
About face aggregation degree, using X-ray diffraction device (Rigaku Denki Co., Ltd's manufacture), using Mo radiographic sources come into
Row measures.
Then, in order to evaluate brittle-cracking propagation stopping characteristics, progress temperature-gradient type ESSO experiments, find out-
Kca values at 10 DEG C (are also denoted as Kca (- 10 DEG C) N/mm below1.5).By Kca, (- 10 DEG C) are 6000N/mm1.5Above situation
As good.
These test results are shown in table 3.
According to shown in table 3 as a result, example of the present invention have plate thickness center rolling surface in (211) face aggregation degree be 1.2
The texture that (200) face aggregation degree above and in the rolling surface of surface of steel plate is 1.7 or more, the Charpy at 1/4 position of plate thickness are disconnected
It with the Charpy fracture transition temperature vTrs at surface of steel plate is -80 DEG C or less and toughness that mouthful transition temperature vTrs, which be -40 DEG C or less,
It is excellent, and it is 6000N/mm to have obtained (- 10 DEG C) of Kca1.5Above such excellent brittle-cracking propagation stopping characteristics.
On the other hand, deviate a certain item that comparative example of the invention is unsatisfactory in YS, TS, texture, vTrs.In addition, obtaining
The value of Kca (- 10 DEG C) all ungratified result.
Claims (5)
1. a kind of high intensity pole steel plate of the excellent in brittle-cracking propagation stopping characteristics of plate thickness 70mm or more,
With as follows at being grouped as：Contain C in terms of quality %：0.03~0.20%, Si：0.03~0.5%, Mn：0.5~
2.2%, P：0.01% or less, S：0.005% or less, Ti：0.005~0.03%, Al：0.005~0.080% and N：
0.0050% hereinafter, the Ceq defined by following formula (1) is 0.36 or more and 0.40 hereinafter, surplus is by Fe and inevitably miscellaneous
Texture at,
And in the rolling surface that (211) face aggregation degree in the rolling surface with plate thickness center is 1.2 or more, surface of steel plate
(200) texture that face aggregation degree is 1.7 or more,
Charpy fracture transition temperature vTrs at 1/4 position of plate thickness be -40 DEG C hereinafter,
Charpy fracture transition temperature vTrs at surface of steel plate be -80 DEG C hereinafter,
Ceq=C+Mn/6+Cu/15+Ni/15+Cr/5+Mo/5+V/5 ... (1)
Here, C, Mn, Cu, Ni, Cr, Mo and V in formula (1) indicate the quality % contents of each element, without containing when be set as 0.
2. the high intensity pole steel plate of excellent in brittle-cracking propagation stopping characteristics as described in claim 1, wherein the ingredient
Composition also contains Nb in terms of quality %：0.005~0.05%, Cu：0.05~1.0%, Ni：0.05~1.5% and Cr：0.01~
One or more of 0.5%.
3. the high intensity pole steel plate of excellent in brittle-cracking propagation stopping characteristics as claimed in claim 1 or 2, wherein described
Also contain Mo in terms of quality % at being grouped as：0.01~0.5%, V：0.001~0.10%, B：0.0030% or less, Ca：
0.0050% or less, REM：One or more of 0.0100% or less.
4. a kind of manufacturing method of the high intensity pole steel plate of the excellent in brittle-cracking propagation stopping characteristics of plate thickness 70mm or more,
By with the temperature according to any one of claims 1 to 3 for being heated at the steel former material being grouped as 1000~1200 DEG C,
Then,
Temperature in plate thickness center accumulates reduction ratio for 10% or more, plate thickness center within the scope of austenite recrystallization temperature
Accumulation reduction ratio of the temperature within the scope of austenite non-recrystallization temperature is 50% or more, plate thickness surface temperature in Ar3Transformation temperature
Below and the temperature in plate thickness center is in Ar3Accumulation reduction ratio when more than transformation temperature temperature range be more than 20% under conditions of into
Row hot rolling, then,
It is cooled to 500 DEG C of cooling stopping temperature below with the cooling velocity of 0.5 DEG C/s or more.
5. the manufacturing method of the high intensity pole steel plate of excellent in brittle-cracking propagation stopping characteristics as claimed in claim 4,
In, after being cooled to 500 DEG C of cooling stopping temperature below, the temperature in plate thickness center is less than Ac1The temperature of transformation temperature is returned
Fire.
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| CN109868412A (en) * | 2019-02-18 | 2019-06-11 | 山东钢铁股份有限公司 | Exempt to preheat 500MPa grades of high-strength steel of big thickness low-carbon-equivalent and its manufacturing method before a kind of weldering |
Citations (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2008169468A (en) * | 2006-12-14 | 2008-07-24 | Nippon Steel Corp | High-strength thick steel plate having excellent brittle crack propagation-stopping performance |
| JP2008214652A (en) * | 2007-02-28 | 2008-09-18 | Jfe Steel Kk | High strength thick steel plate for structural purpose having excellent brittle crack propagation arrest property, and method for producing the same |
| JP2011214116A (en) * | 2010-04-01 | 2011-10-27 | Nippon Steel Corp | Thick high strength steel plate having excellent brittle crack propagation arresting property, and method for producing the same |
| CN102753719A (en) * | 2009-12-28 | 2012-10-24 | Posco公司 | High strength steel sheet having excellent brittle crack resistance and method for manufacturing same |
| JP2013151743A (en) * | 2011-12-27 | 2013-08-08 | Jfe Steel Corp | High strength thick steel plate excellent in toughness of high heat input welding part and brittle crack propagation stopping property, and method for producing the same |
| CN104024462A (en) * | 2011-12-27 | 2014-09-03 | 杰富意钢铁株式会社 | High-strength thick steel plate for construction having excellent characteristics for preventing diffusion of brittle cracks, and production method therefor |
| CN104024456A (en) * | 2011-12-27 | 2014-09-03 | 杰富意钢铁株式会社 | High-strength thick steel plate for construction having excellent characteristics for preventing diffusion of brittle cracks, and production method therefor |
| CN105102650A (en) * | 2013-03-26 | 2015-11-25 | 杰富意钢铁株式会社 | High strength thick steel plate for high heat input welding with excellent brittle crack arrestability and manufacturing method therefor |
| CN105102651A (en) * | 2013-03-26 | 2015-11-25 | 杰富意钢铁株式会社 | High strength thick steel plate with superior brittle crack arrestability for high heat input welding and method for manufacturing same |
| CN107208238A (en) * | 2015-03-12 | 2017-09-26 | 杰富意钢铁株式会社 | High intensity pole steel plate and its manufacture method |
Family Cites Families (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS548349A (en) | 1977-06-22 | 1979-01-22 | Mitsubishi Electric Corp | Elevator door device |
| JPS54142842A (en) | 1978-04-27 | 1979-11-07 | Kiyoshi Tamura | Hollow structure in reinforced cement |
| JP2659661B2 (en) | 1993-01-06 | 1997-09-30 | 新日本製鐵株式会社 | Structural steel for welding with excellent brittle fracture propagation stopping performance at joints and method of manufacturing the same |
| JPH07100814A (en) | 1993-10-04 | 1995-04-18 | Sekisui Chem Co Ltd | Manufacture of cement molded item |
| JP3467767B2 (en) | 1998-03-13 | 2003-11-17 | Ｊｆｅスチール株式会社 | Steel with excellent brittle crack arrestability and method of manufacturing the same |
| JP4077167B2 (en) | 2001-02-28 | 2008-04-16 | 株式会社神戸製鋼所 | Steel plate with excellent arrest properties and its manufacturing method |
| CN108130479A (en) * | 2011-02-08 | 2018-06-08 | 杰富意钢铁株式会社 | The excellent plate thickness of long brittle-cracking propagation stopping characteristics is the steel plate and its manufacturing method of more than 50mm |
| JP5304924B2 (en) * | 2011-12-27 | 2013-10-02 | Ｊｆｅスチール株式会社 | Structural high-strength thick steel plate with excellent brittle crack propagation stopping characteristics and method for producing the same |
-
2017
- 2017-01-30 WO PCT/JP2017/003152 patent/WO2017145651A1/en active Application Filing
- 2017-01-30 KR KR1020187024221A patent/KR102192969B1/en active IP Right Grant
- 2017-01-30 CN CN202211251915.0A patent/CN115652197A/en active Pending
- 2017-01-30 JP JP2017533359A patent/JP6338022B2/en active Active
- 2017-01-30 CN CN201780013041.6A patent/CN108779525A/en active Pending
Patent Citations (10)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JP2008169468A (en) * | 2006-12-14 | 2008-07-24 | Nippon Steel Corp | High-strength thick steel plate having excellent brittle crack propagation-stopping performance |
| JP2008214652A (en) * | 2007-02-28 | 2008-09-18 | Jfe Steel Kk | High strength thick steel plate for structural purpose having excellent brittle crack propagation arrest property, and method for producing the same |
| CN102753719A (en) * | 2009-12-28 | 2012-10-24 | Posco公司 | High strength steel sheet having excellent brittle crack resistance and method for manufacturing same |
| JP2011214116A (en) * | 2010-04-01 | 2011-10-27 | Nippon Steel Corp | Thick high strength steel plate having excellent brittle crack propagation arresting property, and method for producing the same |
| JP2013151743A (en) * | 2011-12-27 | 2013-08-08 | Jfe Steel Corp | High strength thick steel plate excellent in toughness of high heat input welding part and brittle crack propagation stopping property, and method for producing the same |
| CN104024462A (en) * | 2011-12-27 | 2014-09-03 | 杰富意钢铁株式会社 | High-strength thick steel plate for construction having excellent characteristics for preventing diffusion of brittle cracks, and production method therefor |
| CN104024456A (en) * | 2011-12-27 | 2014-09-03 | 杰富意钢铁株式会社 | High-strength thick steel plate for construction having excellent characteristics for preventing diffusion of brittle cracks, and production method therefor |
| CN105102650A (en) * | 2013-03-26 | 2015-11-25 | 杰富意钢铁株式会社 | High strength thick steel plate for high heat input welding with excellent brittle crack arrestability and manufacturing method therefor |
| CN105102651A (en) * | 2013-03-26 | 2015-11-25 | 杰富意钢铁株式会社 | High strength thick steel plate with superior brittle crack arrestability for high heat input welding and method for manufacturing same |
| CN107208238A (en) * | 2015-03-12 | 2017-09-26 | 杰富意钢铁株式会社 | High intensity pole steel plate and its manufacture method |
Cited By (1)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| CN109868412A (en) * | 2019-02-18 | 2019-06-11 | 山东钢铁股份有限公司 | Exempt to preheat 500MPa grades of high-strength steel of big thickness low-carbon-equivalent and its manufacturing method before a kind of weldering |
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| JPWO2017145651A1 (en) | 2018-03-08 |
| KR20180104095A (en) | 2018-09-19 |
| WO2017145651A1 (en) | 2017-08-31 |
| CN115652197A (en) | 2023-01-31 |
| KR102192969B1 (en) | 2020-12-18 |
| JP6338022B2 (en) | 2018-06-06 |
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