CN104011250B - The structure high-strength steel plate of excellent in brittle-cracking propagation stopping characteristics and its manufacture method - Google Patents
The structure high-strength steel plate of excellent in brittle-cracking propagation stopping characteristics and its manufacture method Download PDFInfo
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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
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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
- C21D8/0205—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips of ferrous alloys
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- 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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- 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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- 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
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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
- 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
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- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
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- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
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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
- C21D2201/00—Treatment for obtaining particular effects
- C21D2201/05—Grain orientation
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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
- C21D2211/00—Microstructure comprising significant phases
- C21D2211/005—Ferrite
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Abstract
The present invention provides a kind of structure high-strength steel plate of the excellent in brittle-cracking propagation stopping characteristics of more than the thickness of slab 50mm being applied to ship and its manufacture method.A kind of steel plate of excellent in brittle-cracking propagation stopping characteristics, it is characterized in that, there is special component composition, metal structure is based on ferrite, the texture that the aggregation degree I with RD//(110) face of thickness of slab skin section is more than 1.3, the aggregation degree I in the RD/ of thickness of slab central part/(110) face is more than 1.8, Charpy fracture transition temperature vTrs of skin section is less than 60 DEG C, and Charpy fracture transition temperature vTrs of thickness of slab central part is less than 50 DEG C.
Description
Technical field
The present invention relates to the excellent structure of brittle-cracking propagation stopping characteristics (brittle crack arrestability)
With (for structural use) high-strength steel plate (high-strength thick steel plate) and its manufacturer
Method, particularly to the high-strength steel plate of more than the thickness of slab 50mm being suitable for ship.
Background technology
For the large structures such as ship, the accident that brittle fracture (brittle fracture) is brought is to economy
With environment produce impact very big, therefore, usually require that raising safety, for the steel being used it is desirable to use at a temperature of
Property (toughness) and brittle-cracking propagation stopping characteristics.
The thick-wall materials of high intensity are used for ship hull plate (outer in its structure by the ships such as container ship, bulk carrier
plate of ship's hull).Recently, with the maximization of hull, further development of high strength wall thickening.Generally,
The brittle-cracking propagation stopping characteristics of steel plate have high intensity or thick-wall materials get over the tendency being deteriorated, therefore, to crisp
The requirement of property crack propagation stop performance also improves further.
Method as making the brittle-cracking propagation stopping characteristics of steel improve, the side of known increase Ni content all the time
Method, in the storage tank of liquefied natural gas (Liquefied Natural Gas), uses 9%Ni steel with commercial size.
But, the increase of Ni amount has to make cost be substantially increased, accordingly, it is difficult to the purposes beyond being applied to LNG storage tank.
On the other hand, for be not reaching to the such extremely low temperature (ultra low temperature) of LNG, be used for ship
Oceangoing ship or pipeline, thickness of slab be less than the relatively thin steel of ratio of 50mm, so-called TMCP (Thermo-Mechanical can be passed through
Control Process, thermomechanically controls technique) method is realized grain refined and so that low temperature properties is improved, thus giving excellent crisp
Property crack propagation stop performance.
In addition, proposing in patent documentation 1 to make brittle-cracking propagation on the premise of so that cost of alloy is increased
Stop performance improves and the steel by the tissue micronization (ultra fine crystallization) of skin section.
The steel of the excellent in brittle-cracking propagation stopping characteristics that patent documentation 1 is recorded are characterised by, are conceived to fragility and split
The shear lip (plastic deformation area shear-lips) producing in steel skin section when stricture of vagina is propagated stops special to brittle-cracking propagation
Property raising effectively, make the crystal grain miniaturization of shearing lip portion, thus the propagation energy that the brittle crack absorbing propagation has.
As manufacture method, describe following method：Surface part is cooled to Ar by the control cooling after hot rolling3Phase
Height (transformation point) below, then, stops controlling cooling (controlled cooling), by skin section
Divide and heat (recuperate) again to more than transformation temperature, more than 1 time above-mentioned operation is repeated, during this period steel are implemented to roll
System, thus makes it repeated phase transformation or processing recrystallization, generates ultramicrofine ferritic structure (ferrite in surface part
) or bainite structure (bainite structure) structure.
In addition, having recorded following content in patent documentation 2：Shown using ferrite-pearlite (pearlite) as main body
In the steel of micro-assembly robot, in order that brittle-cracking propagation stopping characteristics improve, two surface elements of steel are by having more than 50% ferrum
The layer of ferritic tissue is constituted, and described ferritic structure has round equivalent grain size (circle-equivalent average grain
Size be) less than 5 μm, draw ratio (aspect ratio of the grains) be more than 2 ferrite crystal grain, and important
Be suppression ferrite particle diameter deviation, as suppression deviation method, by the maximum rolling rate of every 1 passage in finish rolling
(rolling reduction) is set as less than 12%, thus suppressing the recrystallization phenomenon of local.
But, the steel of the excellent in brittle-cracking propagation stopping characteristics described in patent documentation 1,2 are by only by steel
Skin section is heated after first cooling down again and implements processing in heating again and specifically organized, in actual production
Wayward under scale, especially for thickness of slab more than the thick-wall materials of 50mm for, be to rolling, cooling device load big
Technique.
On the other hand, recorded, in patent documentation 3, the miniaturization being not only conceived to ferrite crystal grain but also be conceived to and formed
Subgrain (subgrain) in ferrite crystal grain and make the TMCP elongation technology that brittle-cracking propagation stopping characteristics improve.
Specifically, when thickness of slab is 30～40mm, the cooling on steel plate top layer need not be carried out and heat etc. complicated again
Temperature control, makes brittle-cracking propagation stopping characteristics improve by following conditions：A () guarantees the rolling of fine ferrite crystal grain
More than the 5% partly middle generation rolling condition of fine ferrite structure in steel thickness of slab of condition, (b), (c) are in fine ferrum element
The dislocation (dislocation) making texture (texture) flourishing in body and being introduced by processing (rolling) using heat energy is again
Configuration and formed the rolling condition of subgrain, (d) suppression formed fine ferrite crystal grain and fine subgrain grain coarsening
Cooling condition.
In addition it is also known that rolling being applied to the ferrite after phase transformation in controlled rolling and making that texture is flourishing, it is crisp thus to make
Property crack propagation stop performance improve method.By producing breach along the direction parallel with plate face on the plane of disruption of steel
(separation) relax the stress of brittle crack front end to improve the resistance to brittle fracture.
For example, recorded following content in patent documentation 4：(110) face X-ray intensity ratio (X-ray is made by controlled rolling
Plane intensity ratio in the (110) plane showing a texture developing degree) be
More than 2 and make circle equivalent diameter (diameter equivalent to a circle in the crystal grains)
More than 20 μm of coarse grain is less than 10%, so that resistance to brittle fracture characteristic is improved.
Patent Document 5 discloses a kind of welding structure of the excellent in brittle-cracking propagation stopping characteristics as seam
With the steel plate of steel it is characterised in that the X-ray surface intensity in (100) face on rolling surface within thickness of slab is than for more than 1.5.
And describing by mechanical load direction produced by the prosperity of this texture and the angular deviation in crack propagation direction makes crisp
Property crack propagation stop performance is excellent.
Prior art literature
Patent documentation
Patent documentation 1：Japanese Patent Publication 7-100814 publication
Patent documentation 2：Japanese Unexamined Patent Publication 2002-256375 publication
Patent documentation 3：No. 3467767 publications of Japanese Patent No.
Patent documentation 4：No. 3548349 publications of Japanese Patent No.
Patent documentation 5：No. 2659661 publications of Japanese Patent No.
Content of the invention
Problems to be solved by the invention
Recently, big more than 6000TEU (Twenty-foot Equivalent Unit, twenty-foot equivalent unit)
In type container ship, using the steel plate more than 50mm for the thickness of slab.Well is first-class：The big fragility I of thick handss shipbuilding To お け Ru splits
Broadcast (the brittle-cracking propagation characteristic of growing up that heavy wall makes hull steel), Japanese ship ocean engineering can give a lecture collection of thesis the 3rd
Number, 2006, in pp359-362, the brittle-cracking propagation stopping characteristics of the steel plate of thickness of slab 65mm are evaluated, and are reported
Stop the result that in test, brittle crack does not stop in the large-scale brittle-cracking propagation of mother metal.
In addition, in standard ESSO test (ESSO test compliant with WES3003) of material to be tested, showing
The value (below, being also recited as Kca (- 10 DEG C)) being shown in the Kca at a temperature of -10 DEG C of use is less than 3000N/mm3/2Knot
Really, in the case of the application Ship Structure more than the steel plate of 50mm for the thickness of slab, suggest and guarantee that safety becomes problem.
From the point of view of manufacturing condition, disclosed experimental data, the brittle-cracking propagation described in above-mentioned patent documentation 1～5 stops
Only the steel plate of characteristic good is with the thickness of slab of about 50mm as main object, in the case of being applied to more than the thick-wall materials of 50mm,
Do not know the characteristic that can obtain specifying, the characteristic with regard to the crack propagation in the thickness of slab direction needed for Ship Structure does not obtain completely
To checking.
Therefore, it is an object of the invention to, provide can by optimize rolling condition and control the texture on thickness of slab direction
The high-strength steel plate of excellent in brittle-cracking propagation stopping characteristics stably to manufacture of industrial extremely easy technique and
Its manufacture method.
Method for solve problem
The present inventor has been repeated in-depth study to realize above-mentioned problem, even also have excellent with regard to steel plate
The high-strength steel plate of good crack propagation stop performance obtains following opinion.
1., for thickness of slab more than 50mm steel plate, the fracture of detailed examination standard ESSO test is as a result, becoming as Fig. 1
B, in the case of the fracture morphology shown in (), the width with brittle crack reduces, and the stress magnification factor of crackle leading section subtracts
Little, the crack arrest characteristic of result steel plate improves.Fig. 1 (a) (b) schematically illustrate standard ESSO test film 1 from breach 2 enter
Crackle 3 stops propagating with front end geometry 4 in mother metal 5.
2., in order to obtain fracture morphology as above, need to improve the crack arrest characteristic of skin section and thickness of slab central part.Make
The method improving for the crack arrest characteristic making skin section and thickness of slab central part, so that the property of skin section and thickness of slab central part is improved is to have
Effect.But, as thickness of slab is more than in steel plate 50mm, rate of cooling and rolling rate etc. is existed and limits, thus right
There is also gauge in the property improving thickness of slab central part.
3., as the method also making crack arrest characteristic improve in addition to improving toughness, the texture controlling thickness of slab central part is that have
Effect.(110) face is abreast made to gather especially with respect to rolling direction, so that develop on rolling direction or plate width direction splits
It is effective that the mode that stricture of vagina obliquely deviates from rolling direction or plate width direction respectively carries out texture controlling.
4. in addition, passing through to make the accumulation rolling rate in the state of thickness of slab central part is in austenite recrystallization temperature scope
For more than 20%, and make the average rolling rate of every 1 passage be less than 5%, realize the miniaturization of the tissue of skin section.So
Afterwards, by make accumulation rolling rate in the state of thickness of slab central part is in austenite non-recrystallization temperature range be 40% with
On, and make the average rolling rate of every 1 passage be more than 7%, the property of thickness of slab central part and texture can be made flourishing, thus
It is capable of above-mentioned tissue.
The present invention is to be studied further on the basis of obtained opinion and is completed.That is, the present invention is：
1. a kind of structure high-strength steel plate of excellent in brittle-cracking propagation stopping characteristics is it is characterised in that metal group
Knit based on ferrite, the aggregation degree I with RD//(110) face of thickness of slab skin section is more than 1.3, thickness of slab central part
The aggregation degree I in RD//(110) face is more than 1.8 texture, Charpy fracture transition temperature vTrs≤- 60 DEG C of skin section, and
Charpy fracture transition temperature vTrs≤- 50 DEG C of thickness of slab central part.
2. the structure high-strength steel plate of the excellent in brittle-cracking propagation stopping characteristics as described in 1 is it is characterised in that table
The aggregation degree I in the Charpy toughness value of layer portion and thickness of slab central part and RD//(110) face meets following (1) formula,
vTrs(top layer)+1.9×vTrs(1/2t)-6×IRD//(110) [top layer]-84×IRD//(110)[1/2t]≤-350···(1)
vTrs(top layer)：The fracture transition temperature (DEG C) of skin section,
vTrs(1/2t)：The fracture transition temperature (DEG C) of thickness of slab central part,
IRD//(110) [top layer]：The aggregation degree in the RD/ of skin section/(110) face,
IRD//(110)[1/2t]：The aggregation degree in the RD/ of thickness of slab central part/(110) face.
3. the structure high-strength steel plate of the excellent in brittle-cracking propagation stopping characteristics as described in 1 or 2, its feature exists
In steel composition contains C in terms of quality %：0.03～0.20%, Si：0.03～0.5%, Mn：0.5～2.2%, Al：0.005～
0.08%th, P：Less than 0.03%, S：Less than 0.01%, N：Less than 0.0050%, Ti：0.005～0.03%, surplus is by Fe and not
Evitable impurity is constituted.
4. the structure high-strength steel plate of the excellent in brittle-cracking propagation stopping characteristics as described in 3 is it is characterised in that steel
Composition contains Nb in terms of quality % further：0.005～0.05%, Cu：0.01～0.5%, Ni：0.01～1.0%, Cr：
0.01～0.5%, Mo：0.01～0.5%, V：0.001～0.10%, B：Less than 0.0030%, Ca：Less than 0.0050%,
REM：One or more of less than 0.010%.
5. the manufacture method of the structure high-strength steel plate of a kind of excellent in brittle-cracking propagation stopping characteristics, its feature exists
In the steel former material (slab) of the composition having described in 3 or 4 being heated to 900～1150 DEG C of temperature, is implemented in austenite and ties again
Accumulation rolling rate in brilliant temperature range and austenite non-recrystallization temperature range adds up to more than 65%, at thickness of slab central part
Accumulation rolling rate in the state of austenite recrystallization temperature scope is the average rolling of more than 20% and every 1 passage
Rate is less than 5.0% rolling, then, carries out in the state of thickness of slab central part is in austenite non-recrystallization temperature range
Accumulation rolling rate be more than 40% and the average rolling rate of every 1 passage be more than 7.0% rolling, then, with 4.0 DEG C/
The rate of cooling of more than s accelerates to be cooled to less than 600 DEG C.
6. the manufacture method of the structure high-strength steel plate of the excellent in brittle-cracking propagation stopping characteristics as described in 5, its
In, after accelerating to be cooled to below 600 DEG C, have further and be tempered to AC1The operation of the following temperature of point.
Invention effect
According to the present invention, obtain texture on thickness of slab direction and obtain suitable control, excellent in brittle-cracking propagation stopping characteristics
The high-strength steel plate of more than thickness of slab 50mm and its manufacture method, be applied to preferred thickness of slab more than 50mm, more preferably thickness of slab
The steel plate of more than 55mm is effective.In addition, in shipbuilding field, in the strength deck portion of large-scale container ship, bulk carrier
In structure, by being applied to hatch side coaming, deck member, it is favorably improved the safety of ship, therefore, industrially extremely
Useful.
Brief description
Fig. 1 is the figure of the fracture morphology showing schematically thickness of slab more than the standard ESSO test of the steel plate of 50mm, and (a) is
The figure of top view test film, (b) is the figure of the fracture representing test film.
Specific embodiment
It is stipulated that the property of 1. skin section and thickness of slab central part and texture, 2. metal structure in the present invention.
1. property and texture
In the present invention, for develop along the horizontal direction (direction in the face of steel plate) such as rolling direction or rolling vertical direction
For crackle, in order to obtain the fracture morphology of the Fig. 1 that can improve crack propagation stop performance, suitably regulation is in thickness of slab skin section
And the property of central part and the aggregation degree I in RD//(100) face.
Firstly, since mother metal is well the premise of the development for suppressing crackle, therefore, for the steel of the present invention
Plate, Charpy fracture transition temperature vTrs of skin section is defined as less than -60 DEG C, and by the Charpy fracture in thickness of slab central part
Transition temperature vTrs is defined as less than -50 DEG C.Charpy fracture transition temperature vTrs in thickness of slab central part be preferably -60 DEG C with
Under.
In addition, by making the texture in RD//(100) face flourishing, making cleavage surface (cleavage plane) with respect to crackle master
Direction is obliquely gathered, by producing the effect that the stress of the brittle crack front end that small crackle branch causes relaxes, fragility
Crack propagation Stopping Ability improves.By the nearest thickness of slab for ship hull plates such as container ship and bulk carriers more than 50mm
Thick-wall materials, obtain Kca (- 10 DEG C) >=6000N/mm as target at the aspect guaranteeing safety of structure3/2Brittle crack
In the case of propagating Stopping Ability, the aggregation degree I needing to make RD//(110) face of thickness of slab skin section is more than 1.3, preferably 1.6
More than, and make the aggregation degree I in RD//(110) face of thickness of slab central part be more than 1.8, preferably more than 2.0.
Here, the aggregation degree I in the RD/ of thickness of slab skin section or thickness of slab central part/(110) face refer to as follows.First, from plate
Thick skin section or the sample of thickness of slab central part collection thickness of slab 1mm, carry out mechanical lapping (mechanical to the face parallel with plate face
Polishing)/electrolytic polishing (electrolytic polishing), thus, prepares the test film of X-ray diffraction.Need
Illustrate, in the case of thickness of slab skin section, the face near with most surface is ground.Using this test film, using Mo ray
Source, implements X-ray diffraction measure (X-ray diffraction measurement), obtains (200), (110) and (211)
Pole figure (pole figures).Calculated by obtained pole figure by Bunge method and try to achieve three-dimensional crystals orientation density function
(three dimensional orientation distribution function).Then, by obtained three-dimensional crystals
Orientation density function, is recorded by Bunge, in ψ2=0 °～90 ° are added up in the sectional view of 19 with 5 ° of intervals, accumulate (110)
Face reaches the value of the three-dimensional crystals orientation density function of parallel orientation with respect to rolling direction, obtains accumulated value
(integrated value).Value obtained from the number of the orientation divided by above-mentioned accumulation for this accumulated value is referred to as RD//(110)
The aggregation degree I in face.
In addition to the regulation of above-mentioned mother metal and texture, the Charpy of preferably skin section and thickness of slab central part
The aggregation degree I in value and RD//(110) face meets following (1) formula.
vTrs(top layer)+1.9×vTrs(1/2t)-6×IRD//(110) [top layer]-84×IRD//(110)[1/2t]≤-350···(1)
vTrs(top layer)：The fracture transition temperature (DEG C) of skin section
vTrs(1/2t)：The fracture transition temperature (DEG C) of thickness of slab central part
IRD//(110) [top layer]：The aggregation degree in the RD/ of skin section/(110) face
IRD//(110)[1/2t]：The aggregation degree in the RD/ of thickness of slab central part/(110) face
By meeting above-mentioned (1) formula, more excellent brittle-cracking propagation Stopping Ability can be obtained.
2. metal structure
In the present invention, metal structure is based on ferrite.Here, in the present invention, metal structure is based on ferrite
The area percentage referring to ferritic phase is overall more than 60%.Bainite in surplus, martensite (inclusion island-like martensite),
Total area percentage of pearlite etc. is less than 40%.
In tissue based on ferrite, obtained according to the rolling condition in the rolling of common austenitic range with ferrum
Ferritic be main body metal structure in the case of although obtaining the property as target, but after rolling from austenite to ferrum element
When body phase becomes, transformation time fully exists, and therefore, obtained texture becomes unordered it is impossible to realize in the thickness of slab table as target
In layer portion the aggregation degree I in RD//(110) face be more than 1.3, preferably more than 1.6, the gathering of RD//(110) face of thickness of slab central part
Degree I is more than 1.8, preferably more than 2.0.Therefore, as described later, by designing rolling condition, even based on ferrite
Tissue it is also possible to the aggregation degree I obtaining RD/ in thickness of slab skin section/(110) face be more than 1.3, preferably more than 1.6, in thickness of slab
The aggregation degree I in the RD/ in centre portion/(110) face is more than 1.8, preferably more than 2.0.
3. chemical composition
Hereinafter, the preferred chemical composition in the present invention is illustrated.In explanation, % is quality %.
C：0.03～0.20%
C is the element improving hardness of steel, in the present invention, in order to ensure desired intensity, needs containing more than 0.03%, but
During more than 0.20%, not only weldability is deteriorated, and also has harmful effect to property.Therefore, C be preferably defined as 0.03～
0.20% scope.More preferably 0.05～0.15%.
Si：0.03～0.5%
Si is effective as deoxidant element and as the intensified element of steel, but when content is less than 0.03%, does not have it
Effect.When on the other hand, more than 0.5%, not only damage the surface texture of steel, and property becomes extreme difference.It is therefore preferable that making it
Addition is more than 0.03 and less than 0.50%.
Mn：0.5～2.2%
Mn adds as intensified element.During less than 0.5%, its effect is insufficient, and during more than 2.2%, weldability is deteriorated, steel
Material cost also rises, it is therefore preferable that being set to more than 0.5% and less than 2.2%.
Al：0.005～0.08%
Al works as deoxidizer, needs containing more than 0.005% for this, but containing when having more than 0.008%, can make
Property reduce, and so that the property in welding metal portion is reduced when welding.Therefore, Al is preferably defined as 0.005～0.008%
Scope.More preferably 0.02～0.04%.
N：Less than 0.0050%
N is combined with the Al in steel and forms AlN, thus, adjusts crystallization particle diameter during rolling processing and so that steel is strengthened, but super
When 0.0050%, property is deteriorated, it is therefore preferable that being set to less than 0.0050%.
P、S
P, S be steel in inevitable impurity, but P more than 0.03%, S more than 0.01% when, property be deteriorated, therefore,
It is preferably set to less than 0.03%, less than 0.01% respectively.It is more preferably less than 0.02%, less than 0.005% respectively.
Ti：0.005～0.03%
Ti by micro interpolation, forms nitride, carbide or carbonitride, and having makes crystal grain miniaturization and improve
The effect of mother metal.Its effect is obtained by more than 0.005% interpolation, but containing have more than 0.03% when, mother can be made
The property of material and welding heat affected zone reduces, and therefore, is set to 0.005～0.03%.
Be the preferred basis composition in the present invention above, but in order to make characteristic improve further, can contain Nb,
One or more of Cu, Ni, Cr, Mo, V, B, Ca, REM.
Nb：0.005～0.05%
Nb is separated out in ferrite transformation or when heating in the form of NbC again, contributes to high intensity.In addition, in Ovshinsky
In the rolling of body scope, there is the effect making non-recrystallization expanded range, contribute to ferritic grain refined, therefore, to property
Improvement also effective.This effect is played by more than 0.005% interpolation, but more than during 0.05% interpolation, thick NbC analyses
Go out, the reduction of instead resulting in property, therefore, its upper limit is preferably 0.05%.
Cu、Ni、Cr、Mo
Cu, Ni, Cr, Mo are the element of the quenching degree improving steel.Intensity after directly contributing to roll improves, and can
To add for functions such as raising property, elevated temperature strength or weatherabilities, their effect is by sending out containing more than 0.01%
Wave, therefore, in the case of containing, preferably more than 0.01%.But, excessively contain sometimes, can making property, weldability be deteriorated,
Therefore, in the case of containing, the upper limit preferably making Cu respectively is 0.5%, the upper limit of Ni is 1.0%, the upper limit of Cr is
0.5%th, the upper limit of Mo is 0.5%.
V：0.001～0.10%
V is the element making the intensity of steel improve by precipitation strength in the form of V (CN), in order to play this effect, can
With containing more than 0.001%.But, during containing having more than 0.10%, can making property reduce.Therefore, in the case of containing V, excellent
Choosing is set as containing in the range of 0.001～0.10%.
B：Less than 0.0030%
B can as improve steel quenching degree element micro add.But, during containing having more than 0.0030%, make weldering
The property of socket part reduces, and therefore, in the case of containing B, preferably comprises less than 0.0030%.
Ca：Less than 0.0050%, REM：Less than 0.010%
Ca, REM make the tissue miniaturization of welding heat affected zone improve toughness, even and if adding also without compromising on this
Bright effect, therefore, it can be added as needed on.But, excessively contain sometimes, thick field trash can be formed and make mother metal
Property be deteriorated, therefore, in the case of containing, the upper limit preferably making Ca is 0.0050%, the upper limit of REM be 0.010%.
4. manufacturing condition
Hereinafter, the preferred manufacturing condition in the present invention is illustrated.
As manufacturing condition, the preferably heating-up temperature of regulation steel former material, hot-rolled condition, cooling condition etc..Especially with regard to
Hot rolling, in addition to overall accumulation rolling rate, thickness of slab central part is in situation in the range of austenite recrystallization temperature and
It is in the average rolling of situation difference preferably regulation accumulation rolling rate and every 1 passage of austenite non-recrystallization temperature range
Rate.By these regulations, the gathering of the property in the skin section for steel plate and thickness of slab central part and RD//(110) face
Degree I and the intensity of thickness of slab 1/4, can obtain desired characteristic.
First, the molten steel of above-mentioned composition is passed through converter etc. and carry out melting, steel former material is made by continuous casting etc..Then, will
After steel former material is heated to 900～1150 DEG C of temperature, carry out hot rolling.
In order to obtain good property, reduce heating-up temperature, to reduce the crystallization particle diameter before rolling be effective, but heating temperature
It is impossible to fully guarantee to carry out the time of the rolling in the range of austenite recrystallization temperature when degree is less than 900 DEG C.In addition, exceeding
When 1150 DEG C, austenite grain becomes thick, and only resulting in property does not reduce, and oxidational losses is notable, and yield rate reduces, therefore, plus
Hot temperature is preferably 900～1150 DEG C.From the viewpoint of property, the scope of preferred heating-up temperature is 1000～1100
℃.
Generally, the feelings of the metal structure based on ferrite are being obtained by implementing common austenitic range rolling
Although obtaining the property as target under condition, but when austenite is to ferrite transformation, transformation time fully exists after rolling,
Therefore, obtained texture becomes unordered.Therefore, it is impossible to realize the RD/ of the thickness of slab skin section as target in the present invention/
(110) the aggregation degree I in face be more than 1.3, preferably more than 1.6, the aggregation degree I in RD//(110) face of thickness of slab central part be 1.8 with
Above, preferably more than 2.0.Therefore, in the present invention, it is preferably as follows described regulation hot-rolled condition.Thus, even based on ferrite
Body tissue it is also possible to obtain RD//(110) face of thickness of slab skin section aggregation degree I be more than 1.3, preferably more than 1.6, thickness of slab
The aggregation degree I in the RD/ of central part/(110) face is more than 1.8, preferably more than 2.0.
For hot rolling, preferably carry out thickness of slab central part first in the state of being in austenite recrystallization temperature scope
Accumulation rolling rate be more than 20% and rolling below 5.0% for the average rolling rate of every 1 passage.By making this accumulation
Rolling rate is more than 20%, austenite grain refined, the metal structure finally giving also grain refined, and property improves.On the other hand, lead to
The average rolling rate crossing every 1 passage making in this temperature range is less than 5.0%, can be near the particularly top layer of steel
Introduce strain, thus, it is possible to the aggregation degree I making RD//(110) face of thickness of slab skin section is more than 1.3, preferably more than 1.6, enter
And, skin section becomes grain refined, and the property obtaining skin section improves effect.
Then, preferably carry out tired in the state of the temperature of thickness of slab central part is in austenite non-recrystallization temperature range
The average rolling rate of long-pending rolling rate more than 40% and every 1 passage is more than 7.0% rolling.By making in this temperature range
Accumulation rolling rate be more than 40%, the texture of thickness of slab central part can be made fully flourishing.In addition, by making every 1 passage
Average rolling rate is more than 7.0%, and the aggregation degree I that can make RD//(110) face of thickness of slab central part is more than 1.8, preferably 2.0
More than.
In addition, as making above-mentioned austenite recrystallization temperature scope and austenite non-recrystallization temperature range altogether
Overall, accumulation rolling rate is preferably more than 65%.This is because, by making overall accumulation rolling rate be more than 65%, can
Guarantee that sufficient amount of rolling for tissue, property and intensity are capable of desired value.
Austenite recrystallization temperature scope and austenite non-recrystallization temperature range, can be by carrying out to having this
The steel that is grouped into is become to give the experiment of the preparation of heat/processing history making condition change to hold.
It should be noted that the end temp of hot rolling is not particularly limited, but from the viewpoint of rolling energy rate, preferably exist
It is made to terminate in austenite non-recrystallization temperature range.
Steel plate after terminating for rolling, is preferably cooled to less than 600 DEG C with the rate of cooling of 4.0 DEG C/more than s.Pass through
Make rate of cooling be 4.0 DEG C/more than s, sappy structure can be obtained without making tissue coarsening, can obtain as target
Excellent toughness.When rate of cooling is less than 4.0 DEG C/s, tissue coarsening is it is impossible to obtain the property as target.By making cooling
Stop temperature and be less than 600 DEG C, the carrying out recrystallizing can be avoided, by hot rolling and cooling afterwards, be able to maintain that gained
The desired texture arriving.When cooling down stopping temperature higher than 600 DEG C, even if recrystallize after cooling stops also carrying out it is impossible to obtain
To desired texture.It should be noted that above-mentioned rate of cooling and cooling stop the temperature that temperature is set to the thickness of slab central part of steel plate
Degree.The temperature of thickness of slab central part is calculated etc. by simulation and tried to achieve by thickness of slab, surface temperature and cooling condition etc..For example, lead to
Cross and use calculus of finite differences, calculate the Temperature Distribution in thickness of slab direction, obtain the temperature of the thickness of slab central part of steel plate.
Steel plate after terminating for cooling is processed it is also possible to implement tempering (temper).By implementing to be tempered, one can be entered
Step improves the property of steel plate.Temperature is set to A in terms of steel plate mean temperatureC1Point following implementing, thereby, it is possible to do not damage by
Desired tissue obtained by rolling, cooling.In the present invention, A is obtained by following formulaC1Point (DEG C).
AC1Point=751-26.6C+17.6Si-11.6Mn-169Al-23Cu-23Ni+24.1Cr+22.5Mo+23 3Nb-
39.7V-5.7Ti-895B
In formula, each element symbol is quality % content in steel, is set to 0 when not containing.
The mean temperature of steel plate is also same with the temperature of thickness of slab central part, by thickness of slab, surface temperature and cooling condition etc.
Calculated etc. by simulation and obtain.
Embodiment
The molten steel (steel mark A～O) of each composition shown in table 1 is carried out melting by converter, steel is made by continuous metal cast process
Former material (steel billet thickness 250mm), is hot-rolled down to thickness of slab 50～80mm, then, is cooled down, obtain No.1～29 supplies examination steel.For
A part, also implements tempering after the cooling period.Hot-rolled condition, cooling condition and tempered condition shown in table 2.
For obtained steel plate, 1/4 length direction with test film by thickness of slab is at a right angle with rolling direction
Mode cuts the JIS14A test film of Φ 14, carries out tension test, measures yield point (Yield Strength), tensile strength
(Tensile Strength).
In addition, by skin section and thickness of slab central part (hereinafter, also referred to as 1/2t portion) with the direction of the major axis of test film with
The parallel mode of rolling direction cuts JIS4 impact test piece, carries out Charpy-type test, obtains fracture transition temperature
(vTrs).Here, the impact test piece of skin section is the test making depth that the face nearest away from surface is away from surface of steel plate 1mm
Piece.
Then, in order to evaluate brittle-cracking propagation stopping characteristics, carry out the test of standard ESSO, the Kca value at obtaining -10 DEG C
(Kca(-10℃)).
In addition, obtaining the aggregation degree I in RD//(110) face of thickness of slab central part as follows.First, cut plate from thickness of slab central part
The sample of thick 1mm, by the face parallel with plate face is carried out with mechanical lapping/electrolytic polishing, prepares the test of X-ray diffraction
Piece.Using this test film, using Mo radiographic source, implement X-ray diffraction measure, obtain (200), (110) and (211) pole figure.
Calculated from obtained pole figure by Bunge method and obtain three-dimensional crystals orientation density function.Then, by obtained three-dimensional crystals
Orientation density function, is recorded by Bunge, in ψ2=0 °～90 ° are added up in the sectional view of 19 with 5 ° of intervals, accumulate (110)
Face reaches the value of the three-dimensional crystals orientation density function of parallel orientation with respect to rolling direction, obtains accumulated value.This is accumulated
Value is referred to as the aggregation degree I in RD//(110) face divided by value obtained from the number 19 of the orientation of above-mentioned accumulation.
These result of the tests shown in table 3.The property value of skin section and thickness of slab central part and texture are the present invention's
In the range of for examination steel plate (manufacture No.1～13,27～29) in the case of, (- 10 DEG C) of Kca is 6000N/mm3/2More than, display
Go out excellent brittle-cracking propagation Stopping Ability.In addition, the Charpy value of skin section and thickness of slab central part and RD//
(110) the aggregation degree I in face meet (1) formula for examination steel plate (manufacture numbering 1～13), be unsatisfactory for (1) formula for examination steel plate (system
Make numbering 27～29) compare, obtain high Kca (- 10 DEG C) value.
On the other hand, for manufacturing condition outside the scope of the present invention, the property of steel plate or texture be unsatisfactory for the present invention's
Specify supplies examination steel plate (manufacturing numbering 21～26), and the value of Kca (- 10 DEG C) is less than 6000N/mm3/2.One-tenth packet for steel plate
Supplying outside the preferred scope of the present invention is become to try steel plate (manufacturing numbering 14～20), the property of steel plate is unsatisfactory for the present application
Regulation, the value of Kca (- 10 DEG C) is not reaching to 6000N/mm3/2.
Label declaration
1 standard ESSO test film
2 breach
3 crackles
4 front end geometry
5 mother metals
Table 1
(quality %)
| Steel mark | C | Si | Mn | P | S | Al | Nb | Ti | V | Cu | Ni | Cr | Mo | N | B | Ca | REM | Ceq |
| A | 0.07 | 0.2 | 1.52 | 0.013 | 0.002 | 0.03 | - | 0.011 | - | - | - | 0.13 | - | 0.0033 | - | - | - | 0.35 |
| B | 0.09 | 0.16 | 1.45 | 0.007 | 0.001 | 0.03 | - | 0.016 | - | 0.11 | - | - | - | 0.0024 | - | - | 0.005 | 0.34 |
| C | 0.13 | 0.36 | 1.32 | 0.011 | 0.003 | 0.05 | - | 0.024 | - | - | - | - | - | 0.0041 | 0.0012 | - | - | 0.35 |
| D | 0.08 | 0.27 | 1.34 | 0.006 | 0.002 | 0.04 | - | 0.013 | - | - | 0.33 | - | - | 0.0022 | - | - | - | 0.33 |
| E | 0.08 | 0.23 | 1.62 | 0.013 | 0.003 | 0.06 | - | 0.015 | - | - | - | - | - | 0.0043 | - | - | - | 0.35 |
| F | 0.08 | 0.33 | 1.46 | 0.021 | 0.001 | 0.06 | - | 0.022 | 0.05 | - | - | - | - | 0.0041 | - | - | - | 0.33 |
| G | 0.11 | 0.15 | 1.34 | 0.009 | 0.005 | 0.04 | - | 0.009 | - | - | - | - | 0.05 | 0.0046 | - | - | - | 0.34 |
| H | 0.04 | 0.14 | 1.78 | 0.014 | 0.002 | 0.05 | - | 0.022 | - | - | - | - | - | 0.0023 | - | -0.0030 | - | 0.34 |
| I | 0.07 | 0.24 | 1.51 | 0.014 | 0.004 | 0.03 | - | 0.045 | - | - | - | 0.05 | - | 0.0034 | - | - | - | 0.33 |
| J | 0.09 | 0.3 | 1.48 | 0.006 | 0.003 | 0.02 | 0.009 | 0.006 | - | - | - | - | - | 0.0074 | - | - | - | 0.34 |
| K | 0.06 | 0.22 | 1.52 | 0.013 | 0.004 | 0.03 | - | 0.015 | 0.06 | - | - | - | - | 0.0027 | - | - | 0.052 | 0.33 |
| L | 0.11 | 0.16 | 1.44 | 0.043 | 0.002 | 0.02 | - | 0.012 | - | 0.06 | - | - | - | 0.0033 | - | - | - | 0.35 |
| M | 0.05 | 0.2 | 1.32 | 0.015 | 0.003 | 0.03 | - | 0.013 | - | - | - | 0.64 | - | 0.0041 | - | - | - | 0.40 |
| N | 0.07 | 0.17 | 1.38 | 0.008 | 0.027 | 0.04 | - | 0.021 | - | - | 0.25 | - | 0.05 | 0.0023 | - | - | - | 0.33 |
| O | 0.07 | 0.65 | 1.61 | 0.012 | 0.003 | 0.04 | - | 0.007 | - | - | - | - | - | 0.0046 | - | - | - | 0.34 |
Note 1：(symbol of element represents quality % of each composition to Ceq=C+Mn/6+Cu/15+Ni/15+Cr/5+Mo/5+V/5
Content, is set to 0 in the case of not containing.)
Table 2
Note 1：" recrystallization γ scope accumulation rolling rate " refers to that thickness of slab central part is being in austenite recrystallization temperature scope
Accumulation rolling rate in the state of interior.
Note 2：" recrystallization γ scope averagely rolling rate " refers to that thickness of slab central part is being in austenite recrystallization temperature scope
The average rolling rate of every 1 passage in the state of interior.
Note 3：" non-recrystallization γ scope accumulation rolling rate " refers to that thickness of slab central part is being in austenite non-recrystallization temperature
In the range of in the state of accumulation rolling rate.
Note 4：" non-recrystallization γ scope averagely rolling rate " refers to that thickness of slab central part is being in austenite non-recrystallization temperature
In the range of in the state of every 1 passage average rolling rate.
Table 3
Note 1：Underscore represents outside the scope of the invention.
Note 2：(1) formula vTrs(top layer)+1.9×vTrs(1/2t)-6×IRD//(110) [top layer]-84×IRD//(110)[1/2t]≤-350
Note 3：1/2t portion represents thickness of slab central part.
Claims (7)
1. a kind of excellent in brittle-cracking propagation stopping characteristics structure high-strength steel plate it is characterised in that metal structure with
Ferrite is main body, the aggregation degree I with RD//(110) face of thickness of slab skin section is more than 1.3, the RD/ of thickness of slab central part/
(110) the aggregation degree I in face is more than 1.8 texture, and Charpy fracture transition temperature vTrs of skin section is less than -60 DEG C, and
Charpy fracture transition temperature vTrs of thickness of slab central part is less than -50 DEG C, and, steel composition contains C in terms of quality %：0.03～
0.20%th, Si：0.03～0.5%, Mn：0.5～2.2%, Al：0.005～0.08%, P：Less than 0.03%, S：0.01% with
Under, N：Less than 0.0050%, Ti：0.005～0.03%, surplus is made up of Fe and inevitable impurity,
Here, the aggregation degree I in the RD/ of described thickness of slab skin section or thickness of slab central part/(110) face refer to as follows：
First, gather the sample of thickness of slab 1mm from thickness of slab skin section or thickness of slab central part, mechanical grinding is carried out to the face parallel with plate face
Mill or electrolytic polishing, thus, prepare the test film of X-ray diffraction, it should be noted that in the case of thickness of slab skin section, right
The face near with most surface is ground,
Using this test film, using Mo radiographic source, implement X-ray diffraction measure, obtain (200), (110) and (211) pole figure,
Calculated by obtained pole figure by Bunge method and try to achieve three-dimensional crystals orientation density function,
Then, by obtained three-dimensional crystals orientation density function, recorded by Bunge, in ψ2=0 °～90 ° are closed with 5 ° of intervals
In the sectional view of meter 19, accumulation (110) face reaches the three-dimensional crystals orientation density letter of parallel orientation with respect to rolling direction
The value of number, obtains accumulated value,
Value obtained from the number of the orientation divided by above-mentioned accumulation for this accumulated value is referred to as the aggregation degree I in RD//(110) face.
2. the structure high-strength steel plate of excellent in brittle-cracking propagation stopping characteristics as claimed in claim 1, its feature exists
In, the aggregation degree I in the Charpy fracture transition temperature of skin section and thickness of slab central part and RD//(110) face meets following (1) formula,
vTrs(top layer)+1.9×vTrs(1/2t)-6×IRD//(110) [top layer]-84×IRD//(110)[1/2t]≤-350…(1)
vTrs(top layer)：The fracture transition temperature (DEG C) of skin section,
vTrs(1/2t)：The fracture transition temperature (DEG C) of thickness of slab central part,
IRD//(110) [top layer]：The aggregation degree in the RD/ of skin section/(110) face,
IRD//(110)[1/2t]：The aggregation degree in the RD/ of thickness of slab central part/(110) face.
3. the structure high-strength steel plate of excellent in brittle-cracking propagation stopping characteristics as claimed in claim 1 or 2, its feature
It is, steel composition contains Nb in terms of quality % further：0.005～0.05%, Cu：0.01～0.5%, Ni：0.01～
1.0%th, Cr：0.01～0.5%, Mo：0.01～0.5%, V：0.001～0.10%, B：Less than 0.0030%, Ca：
Less than 0.0050%, REM：One or more of less than 0.010%.
4. a kind of structure high-strength steel plate of excellent in brittle-cracking propagation stopping characteristics manufacture method it is characterised in that
The steel former material of the composition having described in claim 1 is heated to 900～1150 DEG C of temperature, is implemented in austenite recrystallization temperature
Accumulation rolling rate in degree scope and austenite non-recrystallization temperature range adds up to more than 65%, is in Austria in thickness of slab central part
Accumulation rolling rate in the state of family name's body recrystallization temperature scope is more than 20% and the average rolling rate of every 1 passage is
Less than 5.0% rolling, then, carries out the accumulation in the state of thickness of slab central part is in austenite non-recrystallization temperature range
Rolling rate be more than 40% and the average rolling rate of every 1 passage be more than 7.0% rolling, then, with 4.0 DEG C/s with
On rate of cooling accelerate be cooled to less than 600 DEG C.
5. the manufacturer of the structure high-strength steel plate of excellent in brittle-cracking propagation stopping characteristics as claimed in claim 4
Method, wherein, after accelerating to be cooled to below 600 DEG C, has further and is tempered to AC1The operation of the following temperature of point.
6. a kind of structure high-strength steel plate of excellent in brittle-cracking propagation stopping characteristics manufacture method it is characterised in that
The steel former material of the composition having described in claim 3 is heated to 900～1150 DEG C of temperature, is implemented in austenite recrystallization temperature
Accumulation rolling rate in degree scope and austenite non-recrystallization temperature range adds up to more than 65%, is in Austria in thickness of slab central part
Accumulation rolling rate in the state of family name's body recrystallization temperature scope is more than 20% and the average rolling rate of every 1 passage is
Less than 5.0% rolling, then, carries out the accumulation in the state of thickness of slab central part is in austenite non-recrystallization temperature range
Rolling rate be more than 40% and the average rolling rate of every 1 passage be more than 7.0% rolling, then, with 4.0 DEG C/s with
On rate of cooling accelerate be cooled to less than 600 DEG C.
7. the manufacturer of the structure high-strength steel plate of excellent in brittle-cracking propagation stopping characteristics as claimed in claim 6
Method, wherein, after accelerating to be cooled to below 600 DEG C, has further and is tempered to AC1The operation of the following temperature of point.
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| JP2012-111157 | 2012-05-15 | ||
| PCT/JP2012/063410 WO2013099319A1 (en) | 2011-12-27 | 2012-05-18 | High-strength thick steel plate for construction having excellent characteristics for preventing diffusion of brittle cracks, and production method therefor |
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| CN110878404B (en) * | 2015-09-18 | 2022-03-04 | 杰富意钢铁株式会社 | High-strength thick steel plate for structure |
| WO2017145651A1 (en) * | 2016-02-24 | 2017-08-31 | Ｊｆｅスチール株式会社 | High strength ultra-thick steel plate having excellent brittle crack propagation stopping characteristics and manufaturing method of same |
| RU2630086C1 (en) * | 2016-06-14 | 2017-09-05 | Федеральное государственное бюджетное образовательное учреждение высшего образования "Калининградский государственный технический университет" | Low silica shipbuilding steel |
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2012
- 2012-05-15 JP JP2012111157A patent/JP5304924B2/en active Active
- 2012-05-18 CN CN201280065235.8A patent/CN104011250B/en active Active
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| EP1956100A1 (en) * | 2005-11-21 | 2008-08-13 | National Institute for Materials Science | Steel for warm working, method of warm working of the steel, and steel material and steel part obtained by the same |
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Also Published As
| Publication number | Publication date |
|---|---|
| CN104011250A (en) | 2014-08-27 |
| BR112014015795A2 (en) | 2017-06-13 |
| JP5304924B2 (en) | 2013-10-02 |
| KR101588261B1 (en) | 2016-01-25 |
| EP2799585B1 (en) | 2017-01-18 |
| EP2799585A1 (en) | 2014-11-05 |
| BR112014015795B1 (en) | 2019-02-12 |
| JP2013151731A (en) | 2013-08-08 |
| WO2013099319A1 (en) | 2013-07-04 |
| BR112014015795A8 (en) | 2017-07-04 |
| EP2799585A4 (en) | 2015-01-14 |
| KR20140094022A (en) | 2014-07-29 |
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