CN109023137A - A kind of high-strength steel sheet that brittle crack crack arrest characteristic is excellent and its manufacturing method - Google Patents
A kind of high-strength steel sheet that brittle crack crack arrest characteristic is excellent and its manufacturing method Download PDFInfo
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- CN109023137A CN109023137A CN201811029084.6A CN201811029084A CN109023137A CN 109023137 A CN109023137 A CN 109023137A CN 201811029084 A CN201811029084 A CN 201811029084A CN 109023137 A CN109023137 A CN 109023137A
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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
- 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
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22C—ALLOYS
- C22C38/00—Ferrous alloys, e.g. steel alloys
- C22C38/002—Ferrous alloys, e.g. steel alloys containing In, Mg, or other elements not provided for in one single group C22C38/001 - C22C38/60
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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
- C22C38/06—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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
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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
- C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
- C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
- C22C38/48—Ferrous alloys, e.g. steel alloys containing chromium with nickel with niobium or tantalum
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- 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
- C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
-
- 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
- C21D2211/002—Bainite
-
- 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
-
- 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
- C21D2211/009—Pearlite
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- Crystallography & Structural Chemistry (AREA)
- Heat Treatment Of Steel (AREA)
Abstract
The invention discloses a kind of high-strength steel sheet that brittle crack crack arrest characteristic is excellent and its manufacturing methods, the high-strength steel sheet includes the component of following mass percent: C:0.04~0.1%, Mn:0.90~1.50%, Ni:0.40~1.20%, Nb:0.005~0.1%, Ti:0.005~0.10%, Al:0.005~0.06%, Cr:0.01~0.40%, Cu:0.10~0.60%, Si:0.10~0.40%, P:0.01% or less, S:0.004% are hereinafter, surplus is other inevitable impurity of Fe.The manufacturing method comprise the steps of: by slab 1080~1180 DEG C heat, then 880~1180 DEG C at a temperature of carry out roughing, in Ar3~Ar3+ 120 DEG C of temperature carries out finish rolling to the slab Jing Guo roughing, 100~600 DEG C is cooled to, to obtain steel plate.The present invention can obtain the excellent yield strength 390MPa grade high-strength steel plate of brittle crack crack arrest characteristic.
Description
Technical field
The present invention relates to a kind of steel plate and its manufacturing method, specially a kind of high intensity that brittle crack crack arrest characteristic is excellent
Steel plate and its manufacturing method.
Background technique
With putting into effect for super-container vessel, the requirement of the stability of lightweight and structure to Ship Structure
It is more more and more urgent.Using high strength steel, lightweight is carried out to planform, benefit economically can not only be obtained
Benefit, and the thickness of steel plate can be made thinning, it is ensured that the convenience of processing and weld job.
The Ship Structure cleavage event once occurred promotes people to study the brittle crack crack arrest of Ship Structure energetically.It is right
In the steel plate for being applied to container ship hatch coaming and upper deck, it is desirable that it is with excellent brittle crack crack arrest characteristic, to ensure
The safety of Ship Structure.
Application No. is the patents of " 201280057711.1 " to disclose a kind of high-strength steel plate, to slab heating temperature
Low, rolling load is big, and requires 2 DEG C/s or more for plate thickness center cooling velocity, and special heavy plate is difficult to reach.Application number
A kind of thick steel plate, the manufacturing method of thick steel plate are disclosed and to the biography of long brittle crack for the patent of " 201280007816.6 "
The evaluation method and evaluating apparatus for broadcasting Stopping Ability, using two-phase section roll control texture technology, production difficulty is big, and efficiency is aobvious
Writing reduces, unsuitable business application.Application No. is the patents of " 201580070867.7 " to disclose a kind of resistance to brittle crack expansion
The excellent high strength steel of malleability and its manufacturing method, using the precious metal Ni of high-content come toughening matrix, production cost is big
Amplitude improves.
For high strength steel extra-thick plate, due to the limitation of thickness of strand, total reduction is small, deforms not at center
Sufficiently, the low-temperature impact toughness of the organizational coarseness at final finished steel plate center, steel plate centre declines, and will appear at center
Brittle crack crack arrest characteristic becomes very low phenomenon.Therefore, the brittle crack crack arrest characteristic right and wrong of high strength ultra-thick steel plates are improved
Often difficult.
Summary of the invention
Goal of the invention: in order to overcome the deficiencies in the prior art, it is an object of the present invention to provide a kind of brittle cracks to stop
The high-strength steel sheet haveing excellent performance is split, it is a further object of the present invention to provide a kind of high intensity that brittle crack crack arrest characteristic is excellent
The manufacturing method of steel plate.
Technical solution: a kind of high-strength steel sheet that brittle crack crack arrest characteristic is excellent of the present invention includes following matter
Measure percentage component: C:0.04~0.1%, Mn:0.90~1.50%, Ni:0.40~1.20%, Nb:0.005~0.1%,
Ti:0.005~0.10%, Al:0.005~0.06%, Cr:0.01~0.40%, Cu:0.10~0.60%, Si:0.10~
0.40%, P:0.01% or less, S:0.004% are hereinafter, surplus is Fe and other inevitable impurity.
Preferably include the component of following mass percent: C:0.05~0.09%, Mn:0.95~1.45%, Ni:0.45
~1.10%, Nb:0.012~0.060%, Ti:0.009~0.030%, Al:0.01~0.05%, Cr:0.05~0.35%,
Cu:0.12~0.51%, Si:0.12~0.35%, P:0.008% or less, S:0.002% hereinafter, surplus be Fe other can not
The impurity avoided.
Cr, Cu, Ni have also played the toughening effect to matrix while improving harden ability, and the mass ratio of Cr, Cu, Ni are
(Cr+Cu)/Ni≤0.8, preferably (Cr+Cu)/Ni < 0.6.
It include following complex tissue at 1/2 thickness of steel plate: ferrite, bainite and pearlite, the Line Integral of pearlite
Number is for 10% hereinafter, preferably 10~20%, and ferrite area fraction is 10~20%, remaining as bainite, with the Mn
And the increase of Ni content, the percentage of acicular ferrite and bainite will increase, thus intensity also will increase.High-strength steel sheet
With a thickness of 50~100mm, preferably 80~100mm.
A method of preparing above-mentioned high-strength steel sheet comprising the steps of: heat slab at 1080~1180 DEG C, so
Afterwards 880~1180 DEG C at a temperature of carry out roughing, in Ar3~Ar3+ 120 DEG C of temperature carries out essence to the slab Jing Guo roughing
It rolls, is cooled to 100~600 DEG C, to obtain steel plate, when cooling termination temperature is more than 600 DEG C, can not be properly formed fine
A possibility that organizing, therefore becoming 390MPa or less there are yield strength.
Temperature difference of the slab at the mid-depth of thick incoming slab between outer surface is 100~400 DEG C, utilizes the temperature difference
It causes surface strength to be higher than at center, rolling deformation is penetrated into center, refines original austenite grains at center.
The reduction ratio of the last a time of roughing is 15~25%, total reduction ratio of accumulating is 40~59%, is help to obtain
Original austenite grains uniformly tiny at the heart.
It is 1.5~3.2 that the pressure of finish rolling overall process, which is compared, pressure than for the slab thickness after roughing and the steel plate after finish rolling it is thick
The ratio between degree.
According to heat transfer condition analytical Calculation, cooling velocity is 0.5~8 DEG C/s at the center of slab, is conducive to appropriate landform
At microstructure, so that yield strength reaches 390MPa or more.
The average cooling rate of slab is 3~40 DEG C/s, at plate thickness center there is the region of 30% plate thickness can obtain
Uniformly tiny ferrite, bainite and pearlite heterogeneous structure.
The utility model has the advantages that compared to the prior art the present invention, has the characteristics that following conspicuousness: brittle crack crack arrest can be obtained
The yield strength 390MPa grade high-strength steel plate haveing excellent performance；By the raising of the intensity of solution strengthening optimize Mn, Ni, Cr,
Cu and Si content；Optimize carbon content and Mn, Ni, Cr and Cu content by improving harden ability to improve intensity, slow
It can also ensure that the microstructure until at the center of the thick steel plate of 50mm or more in cooling velocity；The tissue of steel plate is carried out thin
Change, especially to organize to refine at the center of steel plate, maximizes the generation of crackle and extension energy consumption, raising brittle crack stops
Fragility energy；Controlling pressure condition in roughing, and ensuring the temperature gradient at center between surface, ensure that until
Microstructure at the center of steel plate.Simultaneously centered on 1/2 part of steel plate thickness, 30% range with steel plate thickness
In thickness, the X-ray diffracted intensity ratio of 113 > texture structure of { 332 } < is more than 2.
Detailed description of the invention
Fig. 1 is microstructure microphoto at steel plate center of the invention.
Specific embodiment
Embodiment 1
The manufacturing method of yield strength 390MPa grade high-strength steel plate, comprising the following steps:
(1) the slab each component mass percent selected are as follows: C:0.04%, Mn:0.90%, Ni:0.40%, Nb:
0.005%, Ti:0.005%, Al:0.005%, Cr:0.01%, Cu:0.10%, Si:0.10%, P:0.001%, S:
0.0004%, surplus is other inevitable impurity of Fe；
(2) slab is heated with 1080 DEG C, then 880 DEG C at a temperature of carry out roughing, the slab before rolling
Temperature difference at center between surface is 100 DEG C, when there are being rolled in the state of temperature difference, low table opposite with temperature
Face is compared, and more deformations is generated at the relatively high center of temperature, therefore crystal grain becomes more to miniaturize at center, and last one
Secondary reduction ratio is 15%, and total reduction ratio of accumulating is 40%；
(3) temperature at 805 DEG C carries out finish rolling to the slab Jing Guo roughing, and pressure is than being 3.1, to obtain with a thickness of 50
Steel plate；
(4) steel plate is cooled to 100 DEG C, at the center of slab cooling velocity be 8 DEG C/s, average cooling rate be 40 DEG C/
s。
Embodiment 2
The manufacturing method of yield strength 390MPa grade high-strength steel plate, comprising the following steps:
(1) select slab each component mass percent are as follows: C:0.1%, Mn:1.50%, Ni:1.20%, Nb:0.1%,
Ti:0.10%, Al:0.06%, Cr:0.40%, Cu:0.60%, Si:0.40%, P:0.01%, S:0.004%, surplus Fe
Other inevitable impurity；
(2) slab is heated with 1180 DEG C, then 1180 DEG C at a temperature of carry out roughing, the slab before rolling
Temperature difference at center between surface is 400 DEG C, when there are being rolled in the state of temperature difference, low table opposite with temperature
Face is compared, and more deformations is generated at the relatively high center of temperature, therefore crystal grain becomes more to miniaturize at center, and last one
Secondary reduction ratio is 20%, and total reduction ratio of accumulating is 41%；
(3) 795 DEG C temperature to Jing Guo roughing slab carry out finish rolling, pressure than be 1.9, thus obtain with a thickness of
The steel plate of 100mm；
(4) steel plate is cooled to 600 DEG C, cooling velocity is 0.5 DEG C/s or more at the center of slab, and average cooling rate is
3℃/s。
Fig. 1 is optical microstructure's photo at 100mm special heavy plate center obtained by the present embodiment, ferrite area fraction
It is 19%, bainite area percent is 78%, and pearlite area percent is 3%.
Embodiment 3
The manufacturing method of yield strength 390MPa grade high-strength steel plate, comprising the following steps:
(1) the slab each component mass percent selected are as follows: C:0.05%, Mn:0.95%, Ni:0.45%, Nb:
0.012%, Ti:0.009%, A1:0.01%, Cr:0.05%, Cu:0.12%, Si:0.120%, P:0.007%, S:
0.001%, surplus is other inevitable impurity of Fe；
(2) slab is heated with 1100 DEG C, then 980 DEG C at a temperature of carry out roughing, the slab before rolling
Temperature difference at center between surface is 150 DEG C, when there are being rolled in the state of temperature difference, low table opposite with temperature
Face is compared, and more deformations is generated at the relatively high center of temperature, therefore crystal grain becomes more to miniaturize at center, and last one
Secondary reduction ratio is 18%, and total reduction ratio of accumulating is 45%；
(3) 801 DEG C temperature to Jing Guo roughing slab carry out finish rolling, pressure than be 2.2, thus obtain with a thickness of
The steel plate of 80mm；
(4) steel plate is cooled to 300 DEG C, at the center of slab cooling velocity be 1.2 DEG C/s, average cooling rate be 7 DEG C/
s。
Embodiment 4
The manufacturing method of yield strength 390MPa grade high-strength steel plate, comprising the following steps:
(1) the slab each component mass percent selected are as follows: C:0.09%, Mn:1.45%, Ni:1.10%, Nb:
0.06%, Ti:0.03%, Al:0.05%, Cr:0.35%, Cu:0.51%, Si:0.35%, P:0.009%, S:0.003%,
Surplus is other inevitable impurity of Fe；
(2) slab is heated with 1100 DEG C, then 1160 DEG C at a temperature of carry out roughing, the slab before rolling
Temperature difference at center between surface is 300 DEG C, when there are being rolled in the state of temperature difference, low table opposite with temperature
Face is compared, and more deformations is generated at the relatively high center of temperature, therefore crystal grain becomes more to miniaturize at center, and last one
Secondary reduction ratio is 25%, and total reduction ratio of accumulating is 58%；
(3) 770 DEG C temperature to Jing Guo roughing slab carry out finish rolling, pressure than be 1.5, thus obtain with a thickness of
The steel plate of 90mm；
(4) steel plate is cooled to 450 DEG C, at the center of slab cooling velocity be 1.0 DEG C/s, average cooling rate be 6 DEG C/
s。
Embodiment 5
The manufacturing method of yield strength 390MPa grade high-strength steel plate, comprising the following steps:
(1) the slab each component mass percent selected are as follows: C:0.07%, Mn:1.20%, Ni:0.80%, Nb:
0.055%, Ti:0.055%, Al:0.032%, Cr:0.20%, Cu:0.35%, Si:0.25%, P:0.005%, S:
0.002%, surplus is other inevitable impurity of Fe；
(2) slab is heated with 1130 DEG C, then 1030 DEG C at a temperature of carry out roughing, the slab before rolling
Temperature difference at center between surface is 225 DEG C, when there are being rolled in the state of temperature difference, low table opposite with temperature
Face is compared, and more deformations is generated at the relatively high center of temperature, therefore crystal grain becomes more to miniaturize at center, and last one
Secondary reduction ratio is 19%, and total reduction ratio of accumulating is 50%；
(3) 780 DEG C temperature to Jing Guo roughing slab carry out finish rolling, pressure than be 1.7, thus obtain with a thickness of
The steel plate of 75mm；
(4) steel plate is cooled to 350 DEG C, cooling velocity is 1.5 DEG C/s or more at the center of slab, and average cooling rate is
11℃/s。
The steel plate of Examples 1 to 5 is measured by EBSD method, the grain at the center with 20 degree or more of high angle crystal boundary
Degree for 30 μm hereinafter, to by strengthen crystal grain improve intensity, while make crackle generation and extension minimum, it is crisp to improve
Property crackle crack arrest characteristic.Centered on 1/2 part of above-mentioned steel plate thickness, in the thickness of 30% range with steel plate thickness,
{ 332 } the X-ray diffracted intensity ratio of<113>texture structure is more than 2.
Comparative example
The molten steel of 1 different chemical composition of table
By chemical component each in table 1 form molten steel (number A~J), according to embodiment 5 preparation process use converter into
Row melting is made slab by continuous metal cast process with a thickness of the slab of 320mm, is cooled down after hot rolling, obtain corresponding A shown in table 2
The trial-production steel plate of~J.Wherein, A-E is steel of the present invention, and F-J is compared steel.
As shown in table 2, compare central part when steel F is the roughing proposed in the present invention to be controlled with average surface temperature difference
The case where for less than 100 DEG C, it can be seen that do not assign adequately deformation, central part crystal grain to central part when due to roughing
Having a size of 37 μm, { 332 }<113>texture group in the thickness of 30% range centered on 1/2 part of thickness with plate thickness
The X-ray diffracted intensity ratio knitted is 1.2l, therefore, -10 DEG C at a temperature of the Kca value that measures lower than generally making needed for ship steel
6000N/mm1.5。
The performance of 2 different chemical composition steel plate of table
The C content for comparing steel G has value more higher than the upper limit of C content of the invention, even if passing through cooling pair when roughing
The granularity of central part austenite is refined, and is also created and is easy to happen brittle upper bainite, therefore final microstructure
Granularity be 32 μm, centered on 1/2 part of thickness with plate thickness 30% range thickness in { 332 }<113>texture
The X-ray diffracted intensity ratio of tissue is 1.63, also, content of pearlite in alloy has been more than 10%, the Kca value measured at a temperature of -10 DEG C
Also below 6000N/mm1.5。
The Ni content for comparing steel H has value more higher than the upper limit of Ni content of the invention, due to high harden ability, base material
Microstructure be the granular bainite containing a large amount of islands MA, even if when roughing by the cooling granularity to central part austenite into
Row miniaturization, the granularity of final microstructure also are indicated as 22 μm, and the Kca value measured at a temperature of -10 DEG C is also below 6000N/
mm1.5。
P, S content for comparing steel I have value more higher than the upper limit of P, S content of the invention, even if other conditions are full
Foot condition proposed by the invention, but brittleness occurs because of P, S of high-content, the Kca value measured at a temperature of -10 DEG C also below
6000N/mm1.5。
Compare (Cr+Cu)/Ni=0.9 of steel J, (Cr+Cu)/Ni≤0.8 of steel A~E of the invention, even if leading to when roughing
Supercooling miniaturize the granularity of central part austenite, also creates a part in central part and is easy to happen brittle upper shellfish
Family name's body, Kca value at a temperature of -10 DEG C is also below 6000N/mm1.5。
In contrast, it can be seen that meet difficult to understand by cooling miniaturization central part when composition range of the invention and roughing
Invention steel A~E of the granularity of family name's body, meets that yield strength is 390Mpa or more, central part granularity is 30 μm hereinafter, and having
The complex tissue of ferrite, bainite and pearlitic structrure.Also, with plate thickness centered on 1/2 part of thickness
The X-ray diffracted intensity ratio of { 332 }<113>texture structure is more than 2.0 in the thickness of 30% range, is measured at a temperature of -10 DEG C
Kca value is also above 6000N/mm1.5。
Claims (10)
1. a kind of high-strength steel sheet that brittle crack crack arrest characteristic is excellent, it is characterised in that the group comprising following mass percent
Point: C:0.04~0.1%, Mn:0.90~1.50%, Ni:0.40~1.20%, Nb:0.005~0.1%, Ti:0.005~
0.10%, Al:0.005~0.06%, Cr:0.01~0.40%, Cu:0.10~0.60%, Si:0.10~0.40%, P:
0.01% or less, S:0.004% is hereinafter, surplus is Fe and other inevitable impurity.
2. a kind of high-strength steel sheet that brittle crack crack arrest characteristic is excellent according to claim 1, it is characterised in that: described
The mass ratio of Cr, Cu, Ni are (Cr+Cu)/Ni≤0.8.
3. a kind of high-strength steel sheet that brittle crack crack arrest characteristic is excellent according to claim 1, it is characterised in that described
Include following complex tissue at 1/2 thickness of steel plate: ferrite, bainite and pearlite, the area fraction of pearlite are 10%
Below.
4. a kind of high-strength steel sheet that brittle crack crack arrest characteristic is excellent according to claim 1, it is characterised in that: described
High-strength steel sheet with a thickness of 50~100mm.
5. a kind of preparation method for the high-strength steel sheet that brittle crack crack arrest characteristic is excellent, it is characterised in that comprise the steps of:
By slab 1080~1180 DEG C heat, then 880~1180 DEG C at a temperature of carry out roughing, in Ar3~Ar3+ 120 DEG C
Temperature carries out finish rolling to the slab Jing Guo roughing, 100~600 DEG C is cooled to, to obtain steel plate.
6. a kind of preparation method of high-strength steel sheet that brittle crack crack arrest characteristic is excellent according to claim 5, special
Sign is: temperature difference of the slab at the mid-depth of thick incoming slab between outer surface is 100~400 DEG C.
7. a kind of preparation method of high-strength steel sheet that brittle crack crack arrest characteristic is excellent according to claim 5, special
Sign is: the reduction ratio of described last a time of roughing is 15~25%, and total reduction ratio of accumulating is 40~59%.
8. a kind of preparation method of high-strength steel sheet that brittle crack crack arrest characteristic is excellent according to claim 5, special
Sign is: it is 1.5~3.2 that the pressure of the finish rolling, which is compared, and the pressure is than the slab thickness after being roughing and the steel plate after finish rolling
The ratio between thickness.
9. a kind of preparation method of high-strength steel sheet that brittle crack crack arrest characteristic is excellent according to claim 5, special
Sign is: cooling velocity is 0.5~8 DEG C/s at the center of the slab.
10. a kind of preparation method of high-strength steel sheet that brittle crack crack arrest characteristic is excellent according to claim 5, special
Sign is: the average cooling rate of the slab is 3~40 DEG C/s.
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Application publication date: 20181218 |