CN105899696A - High-strength steel sheet with small in-plane anisotropy of elongation and manufacturing method therefor - Google Patents
High-strength steel sheet with small in-plane anisotropy of elongation and manufacturing method therefor Download PDFInfo
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- CN105899696A CN105899696A CN201480058323.4A CN201480058323A CN105899696A CN 105899696 A CN105899696 A CN 105899696A CN 201480058323 A CN201480058323 A CN 201480058323A CN 105899696 A CN105899696 A CN 105899696A
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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
- 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
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
- C21D8/0426—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
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/0421—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the working steps
- C21D8/0436—Cold 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
- C21D8/04—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing
- C21D8/0447—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of plates or strips to produce plates or strips for deep-drawing characterised by the heat treatment
- C21D8/0473—Final recrystallisation annealing
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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
- C21D9/00—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor
- C21D9/46—Heat treatment, e.g. annealing, hardening, quenching or tempering, adapted for particular articles; Furnaces therefor for sheet metals
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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
- C22C38/002—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
- C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
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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
- C22C38/06—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
- C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
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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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- C—CHEMISTRY; METALLURGY
- C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
- C22F—CHANGING THE PHYSICAL STRUCTURE OF NON-FERROUS METALS AND NON-FERROUS ALLOYS
- C22F1/00—Changing the physical structure of non-ferrous metals or alloys by heat treatment or by hot or cold working
- C22F1/004—Heat treatment in fluid bed
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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
- C21D2211/003—Cementite
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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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- 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
Abstract
The purpose of the present invention is to provide a high-strength cold-rolled steel sheet and a manufacturing method therefor, wherein said steel sheet is ideal for car parts and electrical machine parts, is high-strength with a yield point (YP) of 400 MPa or more, and has excellent press-formability as a result of reducing the in-plane anisotropy of elongation. A high-strength steel sheet with small in-plane anisotropy of elongation contains, in mass%, C: 0.060-0.099%, Si: 0.09% or less, Mn: 1.0-1.49%, P: 0.050% or less, S: 0.03% or less, sol. Al: 0.01-0.09%, N: 0.005% or less, Nb: 0.035-0.080%, the remainder being obtained from Fe and unavoidable impurities, and does not contain martensite phases or retained austenite phases. In the texture of the plate surface at the sheet thickness position of the steel sheet, the mean crystal orientation density (I alpha) in the phi = 25-35 degree range of alpha-fibers represented by the ODF (crystal orientation distribution function) (phi1 = 0degree, phi2 = 45degree, and phi = 0-55degree) is 2.0 to 4.0 and the mean crystal orientation density (Igamma) of gamma-fibers (phi1 = 0-60degree, phi2 = 45degree, and phi = 55degree) is 2.0 to 10.0.
Description
Technical field
The present invention relates to little high-strength of intra-face anisotropy useful, percentage elongation in the purposes such as automobile use, motor use
Degree steel plate and manufacture method thereof.
Background technology
In recent years, from the viewpoint of environment of preserving our planet, in order to suppress CO2Discharge capacity, it is desirable to improve the combustion of automobile
Material efficiency.In addition, in order to ensure the safety of passenger during collision, also require to improve centered by the collision characteristic of body of a motor car
Safety.Therefore, lightweight and the strengthening of body of a motor car are being actively pushed forward.In order to meet the lightweight of body of a motor car simultaneously
And strengthening, parts raw material is carried out high intensity, and in the unquestioned scope of rigidity, thickness of slab is carried out thin-walled property
It is effective, and the most energetically high-strength steel sheet is applied to automotive part.Additionally, in machine field, go out
In time suppressing product carrying, the purpose of unexpected deformation when falling, the demand improving strength of parts is higher, such as, it is intended to make
It is the steel plate of more than 300MPa by yield strength (YP).
On the other hand, become by punch process using steel plate as raw-material automobile component, motor parts great majority
Shape, therefore steel plate must have excellent press formability.But, high-strength steel sheet, compared with common mild steel plate, strikes out
Shape, ductility deteriorate significantly, therefore it is required that carry out the improvement of this respect.
As high-strength steel sheet, such as, for yield strength (YP) is 440MPa level, just like lower steel plate: in formability
So that the fixing amount of solid solution C, solid solution N adds Ti, Nb in excellent ultra-low carbon steel plate, and with IFization (gap-free atom,
Interstitial free) steel based on, be added to the solution strengthening element such as Si, Mn, P.
Additionally, when yield strength (YP) is more than 500MPa, complex tissue steel plate obtains actually used, including having ferrum
The DP steel plate of the duplex structure of ferritic and martensite, it is effectively utilized the TRIP steel plate of retained austenite.The former is because of martensite week
The overstrain enclosed, and there is low yield strength and process the feature that hardening can be high.The latter is because of plasticity strain induced martensite phase transformation
And there is the feature that uniform elongation uprises.
It is said that in general, the mechanical property of high-strength steel sheet is to be come by the tensile properties of the specific directions such as rolling right angle orientation
Evaluate.But, analyze actual stamping time, it is also expressly that shape components, such as at stretch forming, Sven-Gan Eriksson
In AEG-process can forming height, by the biggest impact of the intra-face anisotropy of percentage elongation.Therefore, by reducing percentage elongation
Intra-face anisotropy, the improvement of press formability can be expected.
For the steel plate that intra-face anisotropy is little, such as in patent documentation 1, disclose a kind of sinter-hardened property excellent,
And cold-rolled steel sheet that intra-face anisotropy is little and manufacture method thereof.This technology is specified with rolling rate time cold rolling by C amount
Δ r, can realize intra-face anisotropy and dent resistance simultaneously.Additionally, its needs begin to cool down within 2 seconds after hot rolling, and
Cool down with the rate of cooling of more than 70 DEG C/sec through the temperature ranges of more than 100 DEG C.But, in the most so-called respectively to
The opposite sex is Δ r, may not be consistent with the intra-face anisotropy of percentage elongation.
For the steel plate relevant to the intra-face anisotropy of percentage elongation, such as in patent documentation 2, disclose a kind of elongation
High-strength steel sheet that the intra-face anisotropy of rate is little and manufacture method thereof.This steel plate is characterised by, it is in terms of area occupation ratio
Make ferritic phase be more than 85% and less than 99% and in terms of area containing more than 1% and less than 13% martensite compound
Organization steel, and at the alpha fibers (φ 1 represented by the ODF (crystalline orientation distribution function) in the plate face of 1/4 thickness of slab position of steel plate
=0 °, φ 2=45 °, Φ=0 °～55 °) in average crystallite orientation density I in the range of Φ=25 °～35 ° be more than 2.0
And less than 4.0.But, for the complex tissue steel containing martensite, due to yield strength (YP) step-down, therefore there are
During product carrying, the problem of unexpected deformation inhibition reduction when falling.Even if containing martensite, if passing through high-alloying
And improving hot strength (TS), then yield strength (YP) also uprises.But, at this moment there are and cause what manufacturing cost rose to ask
Topic.
Additionally, as the anisotropic technology of reduction high-strength steel sheet, such as, think in patent documentation 3: in hot rolling
After end, preferably within 0.4 second, it is cooled to 720 DEG C with the rate of cooling of more than 400 DEG C/sec, thus can reduce the face of r value
Interior anisotropy.But, the most so-called intra-face anisotropy is Δ r, may not be consistent with the intra-face anisotropy of percentage elongation.And
And, cool down with the rate of cooling of more than 400 DEG C/sec thickness of slab as 2mm more than hot rolled steel plate time, steel plate top layer and internal temperature
Degree difference is relatively big, there is also and has caused uneven microstructure, produces the problem that material is uneven.Additionally, in order to more than 400 DEG C/sec
Rate of cooling cooling thickness of slab is the hot rolled steel plate of more than 2mm, needs large-scale equipment, causes cost increase.
Additionally, as utilizing remaining γ to organize and improve the technology of intra-face anisotropy, such as, disclose patent documentation 4.
But, all many and relatively costly because of alloying component.Additionally, the significant high intensity being calculated as more than 590MPa with TS, therefore become
Load required for shape is high, needs large-scale stamping machine to cause high cost.
Prior art literature
Patent documentation
Patent documentation 1: Japanese Unexamined Patent Publication 2004-197155 publication
Patent documentation 2: Japanese Unexamined Patent Publication 2009-132981 publication
Patent documentation 3: Japanese Unexamined Patent Publication 2011-144414 publication
Patent documentation 4: Japanese Unexamined Patent Publication 2012-21225 publication
Summary of the invention
Invent problem to be solved
Present invention advantageously solves the problems referred to above, its object is to provide one to be suitable for automobile component, motor portion
Part, there is high intensity that yield strength (YP) is more than 400MPa and reduce the intra-face anisotropy of percentage elongation, punching press
The high strength cold rolled steel plate having excellent moldability and manufacture method thereof.
For the method solving problem
It is said that in general, in the rolling texture of cold-rolled steel sheet,<100>are oriented parallel to rolling direction (Rolling
Direction) gamma fiber that alpha fibers and<111>are oriented parallel to normal direction (Normal Direction) is flourishing.So
And, if recrystallization is carried out in annealing operation, alpha fibers dies down, and gamma fiber becomes strong.Owing to alpha fibers makes relative to rolling direction
Being the percentage elongation reduction in 45 ° of directions, therefore for the cold-rolled steel sheet manufactured with usual operation, it relative to rolling direction is
The percentage elongation in 45 ° of directions is low, and the anisotropy of percentage elongation becomes strong.
The present inventors has been repeated further investigation to solve the problems referred to above, found that in order to improve relative to
Rolling direction is that the percentage elongation in 45 ° of directions is to reduce anisotropy, it is important that the knitting of plate face of 1/4 thickness of slab position of steel plate
In structure, Φ in the alpha fibers (φ 1=0 °, φ 2=45 °, Φ=0 °～55 °) represented by ODF (crystalline orientation distribution function)=
Average crystallite orientation density I in the range of 25 °～35 °αIt is more than 2.0 and less than 4.0, gamma fiber (φ 1=0 °～60 °, φ
2=45 °, Φ=55 °) average crystallite orientation density IγIt is more than 2.0 and less than 10.0.It is moreover found that in order to obtain
State texture, it is important that the control that one-tenth is grouped into, the control of particularly Nb content, and the control to manufacturing condition.
The present invention completes based on above-mentioned opinion, and its main points are as described below.
[1] high-strength steel sheet that the intra-face anisotropy of a kind of percentage elongation is little, in terms of quality % containing C:0.060～
0.099%, below Si:0.09%, Mn:1.0～1.49%, below P:0.050%, below S:0.03%, sol.Al:0.01～
0.09%, below N:0.005%, Nb:0.035～0.080%, surplus is made up of Fe and inevitable impurity, described steel plate
Without martensitic phase and retained austenite phase, in the texture in the plate face of 1/4 thickness of slab position of steel plate, (crystalline orientation is distributed ODF
Function) represented by alpha fibers (φ 1=0 °, φ 2=45 °, Φ=0 °～55 °) in average in the range of Φ=25 °～35 °
Crystalline orientation density IαIt is more than 2.0 and less than 4.0, gamma fiber (φ 1=0 °～60 °, φ 2=45 °, Φ=55 °) average
Crystalline orientation density IγIt is more than 2.0 and less than 10.0.
[2] according to the high-strength steel sheet that the intra-face anisotropy of the percentage elongation described in [1] is little, wherein, in terms of quality % also
Containing Ti:0.010～0.050%.
[3] according to the high-strength steel sheet that the intra-face anisotropy of the percentage elongation described in [1] or [2] is little, wherein, by following
(1) the Δ El represented by formula is-2%～2%,
Δ El=(El0-2El45+El90)/2···(1)
Wherein, El0、El45And El90It is to measure relative on the direction that the rolling direction of steel plate is 0 °, 45 ° and 90 °
The value of elongation at break.
[4] according to the high-strength steel sheet that the intra-face anisotropy of the percentage elongation according to any one of [1]～[3] is little, wherein,
Yield strength YP is more than 400MPa, and yield ratio YR (YR=YP/TS) as yield strength YP with the ratio of hot strength TS is
More than 0.79.
[5] according to the high-strength steel sheet that the intra-face anisotropy of percentage elongation according to any one of [1]～[4] is little, its
Surface has zinc-plated system tunicle.
[6] manufacture method of the high-strength steel sheet that the intra-face anisotropy of a kind of percentage elongation is little, prepares have [1] or [2]
The steel billet that described one-tenth is grouped into, heats described steel billet, keeps 60 in the temperature range of slab heating temperature more than 1150 DEG C
After more than minute, carry out roughing, then the final passes rate that final rolling temperature is 820～920 DEG C and finish rolling be 15～
Carry out finish rolling under conditions of 25%, after finish rolling, within 2 seconds, start water-cooled cool down, after manufacturing hot rolled steel plate, to described heat
Rolled steel plate implements pickling and cold rolling, then when carrying out continuous annealing, and holding 10～250 within the scope of the temperature more than 830 DEG C
Second.
[7] manufacture method of the high-strength steel sheet that the intra-face anisotropy of basis percentage elongation described in [6] is little, wherein,
Make finish rolling entrance side temperature be less than 1050 DEG C by water-cooled after described roughing, then carry out described finish rolling.
[8] manufacture method of the high-strength steel sheet that the intra-face anisotropy of basis percentage elongation described in [6] or [7] is little, its
In, the steel plate after annealing is implemented zinc-plated process.
It should be noted that so-called high intensity refers to that yield strength YP is more than 400MPa in the present invention.
Invention effect
According to the present invention it is possible to the high-strength steel sheet that the intra-face anisotropy obtaining percentage elongation is little, press formability is excellent.
Therefore during product carrying additionally, due to yield strength (YP) is high, unexpected deformation when falling is inhibited.The present invention's is high-strength
Degree steel plate goes for automotive part, motor parts, exceedingly useful.
Accompanying drawing explanation
Fig. 1 is to represent Φ=25 ° in alpha fibers～average crystallite orientation density I when 35 °α, in gamma fiber during Φ=55 °
Average crystallite orientation density IγFigure with the relation of Δ El.
Detailed description of the invention
Hereinafter, the present invention is specifically described.
First, to becoming the reason being grouped into illustrate.It should be noted that the unit of each constituent content, as long as no
Special instruction, then be quality %.
C:0.060～0.099%
C is the essential elements for making crystallization grain refined, high intensity.Additionally, it is by forming the precipitation with aftermentioned Nb
Thing and there is the effect that particularly improves yield strength (YP).When C amount less than 0.060% time, due to grain refined brought strong
On degree, ascending effect is low, it is therefore necessary to containing more than 0.060%.On the other hand, if C measures more than 0.099%, the is the most easily formed
2 phases, percentage elongation reduces.Therefore, C amount is set as the scope of 0.060～0.099%.It is preferably 0.060～the model of 0.090%
Enclose.
Below Si:0.09%
Si has and improves the effect of surface quality with trace to postpone the generation of oxide skin in hot rolling.In addition,
Also there is the effect etc. of the processing hardening energy improving ferritic phase.From this point of view, more than about 0.01% is preferably comprised.
But, if Si measures more than 0.09%, then easily form remaining γ phase.Therefore, Si amount is set as less than 0.09%.Preferably set
It is set to less than 0.049%.
Mn:1.0～1.49%
Mn is the element useful for improving armor plate strength by solution strengthening, the grain refined effect of crystallization.When Mn measures
During less than 1.0%, owing to solution strengthening, grain refined effect are low, it is therefore necessary to containing more than 1.0%.On the other hand, if Mn measures
More than 1.49%, the most easily forming martensitic phase, yield strength (YP) reduces.Therefore, Mn amount is set as 1.0～1.49%
Scope.
Below P:0.050%
If P measures more than 0.050%, then deterioration that weldability can occur, the surface defect caused because of segregation.Therefore,
P amount is set as less than 0.050%.It is preferably less than 0.040%.
Below S:0.03%
The effect that S has the once oxidation skin fissility improving steel plate, improves exterior quality.But, if S amount increases,
The MnS then separated out in steel becomes many.Therefore, make the ductility such as the percentage elongation of steel plate, stretch flangeability decline, make press formability
Decline.Additionally, high-temperature ductility when also making to carry out slab hot rolling declines, become easily to produce surface defect.From this viewpoint
Set out, S amount is set as less than 0.03%.Preferably less than 0.01%, more preferably less than 0.005%, more preferably
Less than 0.002%.
Sol.Al:0.01～0.09%
Sol.Al in addition to useful as the deoxidant element of steel, also there is the fixing solid solution N existed as impurity thus
Improve the effect of formability.Therefore, sol.Al amount is set as more than 0.01%.On the other hand, if sol.Al amount exceedes
0.09%, then cause cost to improve, and surface defect can be induced.Therefore, sol.Al amount is set as 0.01～0.09%
Scope.It is preferably 0.02～0.07%.
Below N:0.005%
If the amount of N is too much, then cause formability to be deteriorated, substantial amounts of Al must be added in order to fix solid solution N simultaneously.Cause
This, reduce the most as far as possible.From this point of view, N amount is set as less than 0.005%.
Nb:0.035～0.080%
Nb is the essential elements for making crystallization grain refined, high intensity.Additionally, it becomes precipitate to have with aforementioned C-shaped
There is the effect particularly improving yield strength (YP).And, also have and make Nb precipitate micro-in the finishing rolling step of hot rolling technology
Thin precipitation and partly suppress the recrystallization of steel, improve the effect of the alpha fibers after cold rolling and annealing, therefore Nb be the present invention
Important element.In order to obtain this effect, it is necessary to the Nb containing more than 0.035% measures.On the other hand, if it exceeds 0.080%,
Then can fully suppress the recrystallization in the finishing rolling step of hot rolling technology, excessively improve cold rolling and annealing after alpha fibers, thus
The anisotropy of percentage elongation is deteriorated, and hot rolling load uprises simultaneously.Therefore, Nb amount is set as the model of 0.035～less than 0.080%
Enclose.It is preferably less than 0.060%.
In the present invention, in addition to mentioned component, it is also possible to containing following element.
Ti:0.010～0.050%
Ti has formation precipitate and improves the effect of yield strength (YP).It is therefore preferable that containing more than 0.010%.Separately
On the one hand, using Nb as in the present invention of essential component, excessively hot rolling load can be made to uprise containing Ti.Therefore, it is set as
Less than 0.050%.Therefore, Ti amount is set as the scope of 0.010～less than 0.050%.It is preferably less than 0.029%.
In the present invention, in addition to mentioned component, it is also possible to containing following element.But, following element is particularly quenched
The element of property formation martensitic phase higher, easy thoroughly.It is therefore preferable that be following ranges.
Below Cr:0.05%
Cr Yu Mn is similarly the element easily forming martensitic phase, and if generating martensitic phase, then yield strength (YP)
Decline.Therefore, Cr amount is set as less than 0.05%.It is preferably less than 0.02%, more preferably less than 0.01%.Due to excessively
Reduction cause cost increase, be the most preferably 0.001% by its lower limit set.
Below Mo:0.05%
Mo Yu Mn is similarly the element easily forming martensitic phase, and if generating martensitic phase, then yield strength (YP)
Decline.Therefore, Mo amount is set as less than 0.05%.It is preferably less than 0.02%, more preferably less than 0.01%.Due to excessively
Reduction cause cost increase, be the most preferably 0.001% by its lower limit set.
In the steel plate of the present invention, composition other than the above is Fe and inevitable impurity.But, as long as will not damage
The scope of evil effect of the present invention, does not the most repel containing composition other than the above.
Then, the structure of steel of steel plate of the present invention, the restriction reason of texture are illustrated.
Structure of steel: without martensitic phase and retained austenite phase
Generating martensitic phase and retained austenite phase time, yield strength (YP) declines, during product carrying, unexpected when falling
Deformation inhibition reduce.Therefore, it is necessary to without martensitic phase and retained austenite phase.It should be noted that the present invention
The microscopic structure of steel plate is to comprise ferrite+pearlite or comprise the tissue of cementite further, and the what is called in the present invention is not
Refer to that martensitic phase and retained austenite are calculated as less than 1% with percentage by volume containing martensitic phase mutually with retained austenite.This
Outward, without martensitic phase and the situation of retained austenite phase, can be controlled by manufacturing condition described later.
Texture: the α in the texture in the plate face of 1/4 thickness of slab position of steel plate, represented by ODF (crystalline orientation distribution function)
Average crystallite orientation density I in the range of Φ=25 °～35 ° in fiber (φ 1=0 °, φ 2=45 °, Φ=0 °～55 °)α
It is more than 2.0 and less than 4.0, average crystallite orientation density I of gamma fiber (φ 1=0 °～60 °, φ 2=45 °, Φ=55 °)γ
It is more than 2.0 and less than 10.0
In the past, the analysis of texture used pole figure based on X-ray diffraction (XRD).Multiple crystalline substance is related to owing to pole figure shows
The statistics crystalline orientation distribution of grain, the method being therefore suitable for determining preferred orientation.But, the texture of polycrystalline material is not only
For single preferred orientation, in most cases show multiple preferred orientation.Such as, as the orientation rotated around certain crystallographic axis
In the fibrous textures such as the alpha fibers of group, gamma fiber, it is difficult to correctly evaluated the existence ratio of each orientation by pole figure.Therefore, based on pole
Figure information makes three-dimensional crystals orientation distribution function, evaluates the existence ratio of each orientation.Carrying out above-mentioned three-dimensional crystals orientation point
During the evaluation of cloth function, by the incomplete pole figure of (200), (211), (110) obtained by bounce technique, use Series Expansion Method
Obtain.Outcome research is understood, in the structure of steel without martensitic phase and retained austenite phase as above, and alpha fibers (φ
1=0 °, φ 2=45 °, Φ=0 °～55 °) in average crystallite orientation density I in the range of Φ=25 °～35 °αBe 2.0 with
Upper and less than 4.0, and average crystallite orientation density I of gamma fiber (φ 1=0 °～60 °, φ 2=45 °, Φ=55 °)γFor
When more than 2.0 and less than 10.0, the intra-face anisotropy of percentage elongation diminishes.When to make texture be above-mentioned scope each in the face of percentage elongation
The reason that anisotropy diminishes is the clearest and the most definite.As reason, it is believed that be following caused, i.e. improve rolling direction, relative to rolling
Direction is the existence ratio of the gamma fiber of the percentage elongation in 90 ° of directions and improves relative to the percentage elongation that rolling direction is 45 ° of directions
Alpha fibers (φ 1=0 °, φ 2=45 °, Φ=0 °～55 °) in Φ=25 °～the balance of the existence ratio of 35 ° good.
Then, the present inventors carries out hot rolling to the steel billet with present component composition, makes hot rolled steel plate, in pickling
After carry out cold rolling, make cold-rolled steel sheet, be then carried out annealing, make cold rolled annealed steel plate, and implement temper rolling further.System
Make by the crystalline orientation calculated by the plate face X-ray diffraction result of 1/4 thickness of slab position of so obtained each cold rolled annealed steel plate
Distribution function (hereinafter referred to as ODF:Orientation Distribution Function), by this ODF, pays close attention to and is considered outstanding
It affects the texture being referred to as alpha fibers of the processabilities such as percentage elongation, is studied the relation of this alpha fibers with formability.Knot
Fruit specify that as in alpha fibers orientation Φ=0 ° of group～55 °, particularly the average crystallite in the range of Φ=25 °～35 °
Orientation density IαIt is orientated density I with the average crystallite of gamma fiberγStrong with the dependency of Δ El.In the present invention, when the value of Δ El
During for-2%～2%, the intra-face anisotropy being considered as percentage elongation is little, it is judged that good for press formability.It addition, Δ El can be by
Following formula (1) is obtained.
Δ El=(El0-2El45+El90)/2……(1)
Wherein, El0、El45And El90Be from cold rolled annealed steel plate be 0 ° (L direction), 45 ° of (D sides relative to rolling direction
To) and 90 ° of direction (C direction) directions on cut JIS5 test film and according to the regulation of JIS Z 2241 with crosshead speed
The value of the elongation at break carrying out stretching test measurement in 10mm/ minute.
The average crystallite of such gained is orientated density IαAnd IγWith the absolute value of Δ El (following, be the most also only called | Δ
El |) relation be shown in Fig. 1.As shown in Figure 1, it is orientated density I when average crystalliteαBe more than 2.0 and less than 4.0, average crystallite takes
To density IγThe good result that value is less than 2.0% of | Δ El | when being more than 2.0 and less than 10.0, can be obtained.Namely
Saying and specify that, have in the range of Φ=25 ° in alpha fibers (φ 1=0 °, φ 2=45 °, Φ=0 °～55 °)～35 ° is average
Crystalline orientation density IαIt is more than 2.0 and less than 4.0, gamma fiber (φ 1=0 °～60 °, φ 2=45 °, Φ=55 °) average
Crystalline orientation density IγThe intra-face anisotropy being the percentage elongation of the high-strength steel sheet of the texture of more than 2.0 and less than 10.0 is little.
Therefore, the steel plate of the present invention is preferably more than-2% by the Δ El represented by following (1) formula and less than 2%.
Δ El=(El0-2El45+El90)/2···(1)
Wherein, El0、El45And El90It is to measure relative on the direction that the rolling direction of steel plate is 0 °, 45 ° and 90 °
The value of elongation at break.
In the present invention, can further yield strength, yield ratio be carried out defined below.
Yield strength YP is more than 400MPa, yield ratio YR (YR=as yield strength YP with the ratio of hot strength TS
YP/TS) it is more than 0.79
By improving yield strength, during product carrying, unexpected deformation when falling is inhibited.In order to obtain this effect,
Yield strength YP is preferably more than 400MPa.On the other hand, if excessively improved, then resilience becomes big, it is difficult to maintaining member shape,
Therefore below 550MPa it is preferably.Additionally, yield ratio YR is preferably more than 0.79.If it should be noted that hot strength phase
Uprise for yield strength, then punching press load is necessary to be improved with Shangdi, it is necessary to import large-scale stamping machine.Therefore, hot strength TS
It is preferably below 580MPa.
Then, the manufacture method of the present invention is illustrated.
First, in order to prevent the gross segregation of composition, the steel billet of use preferably employs continuous metal cast process manufacture.Alternatively, it is also possible to
Manufactured by ingot casting method, thin stock casting.Additionally, after manufacturing slab, except being temporarily cooled to room temperature, the most again heat
Outside previous methods, it is also possible to be suitable for without any problems and do not carry out cooling down and being directly loaded in heating furnace by temperature sheet and carry out hot rolling
Direct sending rolling or carry out the energy saving technique such as Direct Rolling of hot rolling after being somewhat incubated immediately.
Then, the condition of hot-rolled process is illustrated.
Slab heating temperature: keep more than 60 minutes in the temperature range more than 1150 DEG C
When heating of plate blank, in order to be completely dissolved Nb precipitate, and Nb is made to separate out in the finishing rolling step of hot rolling technology
The fine precipitation of thing, thus partly suppress the recrystallization of steel, improves the alpha fibers after cold rolling and annealing, and preferably heating-up temperature height is also
And the retention time is long.From this point of view, the present invention keeps in the temperature range of slab heating temperature more than 1150 DEG C
More than 60 minutes.On the other hand, when slab heating temperature is too high or the retention time is long, due to along with the increasing of oxidative weight
Adding, scale loss increases, and the most preferably heating-up temperature is set as less than 1300 DEG C, and the retention time is preferably 500 points
Below clock.
The steel billet heated under these conditions is implemented the hot rolling being made up of roughing and finish rolling.Herein, steel billet passes through roughing
Be formed as sheet billet.It should be noted that the condition of roughing need not special provision, conventional method is used to carry out.Additionally,
In order to prevent fault during hot rolling, improve the non-uniform temperature of width, utilize the so-called sheet billet of combustion thin plate base to heat
Device, strip edge heater are effective.
In order to make Nb precipitate separate out imperceptibly in finishing rolling step, it is applicable for carrying out finish rolling at low temperatures, and essence
Roll entrance side temperature and be preferably less than 1050 DEG C.In the present invention, owing to heating slab under the high temperature more than 1150 DEG C, therefore it is
It is cooled to 1050 DEG C at finish rolling entrance side, preferably before finish rolling, sheet billet is carried out water-cooled.On the other hand, due to excessive low
Temperatureization causes load during hot rolling to uprise, the most preferably more than 930 DEG C.
Final rolling temperature: 820～920 DEG C
Then, sheet billet is carried out finish rolling, makes hot rolled steel plate.At this moment, by final rolling temperature i.e. finish rolling outlet side temperature
(FT) 820～920 DEG C it are set as.This is preferred in order to obtain the intra-face anisotropy of percentage elongation after cold rolling and recrystallization annealing
Texture.When FT is less than 820 DEG C, not only load during hot rolling uprises, and for fractions system, becomes at ferrite
The rolling in district, texture produces and significantly changes.On the other hand, if FT is more than 920 DEG C, the most not only organizes coarsening, and rolled
Austenite grain recrystallization after system is complete, it is impossible to roll with austenite for partial, re-crystallization state, the most cold rolled annealed after
The intra-face anisotropy of percentage elongation becomes big.Therefore, final rolling temperature is set as 820～920 DEG C, more preferably 820～890 DEG C.
The final passes rate of finish rolling: 15～25%
The texture utilizing in austenitic area rolling in finish rolling is formed, and makes the alpha fibers after cold rolling and annealing improve.This effect is subject to
The impact of the final passage of finish rolling is the strongest.When the final passes rate of finish rolling is less than 15%, utilizes in austenitic area and roll
Texture formed insufficient, cold rolling and annealing after alpha fibers cannot become strong, therefore set it to more than 15%.On the other hand,
When more than 25%, owing to load during rolling uprises, therefore it is set as less than 25%.
The time started to water-cooled after finish rolling: within 2 seconds
Needing after finish rolling to make austenite with the direct phase transformation of partial, re-crystallization state, therefore the holding in austenitic area is not
Preferably.Therefore, within 2 seconds, water-cooled is started after finish rolling.More preferably within 0.5 second.
The rate of cooling batched to coiled material after finish rolling, does not has special provision.It should be noted that in order to suppress cooling in
The recrystallization of austenitic area, preferably more than 20 DEG C/sec.Additionally, direction in excessive cooling easily generation thickness of slab direction, face
Non-uniform temperature, the most preferably less than 200 DEG C/sec.More preferably less than 99 DEG C/sec, more preferably 40 DEG C/sec with
Under.
Coiled material coiling temperature (CT) does not has special provision.It should be noted that be preferably set to more than 400 DEG C and 720 DEG C
Below.Particularly, if CT is more than 720 DEG C, then coarse grains, intensity may be caused to decline.
Then, by carrying out pickling, cold rolling, annealing, the high-strength steel sheet of the present invention can be obtained.
Pickling does not has special provision, is carried out by conventional method.For inhibited oxidation skin defect, it is also possible to before pickling
Implement shot-peening, leveling.
Cold rolling do not have special provision.It should be noted that rolling rate is preferably set to 30～80%.When rolling rate is less than
When 30%, recrystallization when there is annealing becomes unstable and causes the probability of the reduction of percentage elongation.If additionally, rolling rate
More than 80%, then load when rolling uprises.
Annealing: by holding 10～250 seconds within the scope of continuous annealing temperature more than 830 DEG C
Recrystallization is slow because of a large amount of interpolation Nb for the steel plate of the present invention, and when annealing at low temperatures, non-recrystallization tissue is residual
Staying, therefore percentage elongation reduces.In order to avoid this problem, till needing to be heated to austenite one phase district when annealing.Accordingly, it would be desirable to
Heating-up temperature is made to be more than 830 DEG C and heat more than 10 seconds.In the case of being heated to more than necessity, there is the grain of austenitic area
Growth and the dissolving of precipitate, therefore intensity reduces.Therefore, annealing time is set as less than 250 seconds.More preferably 60 seconds with
Under.Further, since need such short time heat treatment, it is therefore desirable to carried out by continuous annealing process.Additionally, in annealing
After fast cooling in the case of, easily generate martensitic phase, the most preferably carry out cold with the average cooling rate of less than 50 DEG C/sec
But.
Above, the basic working procedure of manufacture method of the present invention is illustrated.It should be noted that can also add following
Operation.
After above-mentioned cold-rolled steel sheet annealing operation, add and implement what the surface such as electroplating processes or hot dip process processed
Operation, can form coating on surface of steel plate.It should be noted that coating is not limited to pure zinc coating, Zn based alloy coating, also
The various coating that Al coating, Al system alloy layer etc. are applied on conventional surface of steel plate can be formed.Additionally, in order in plating
Corrosion resistance, anti-finger printing is improved, it is also possible to coating chemical conversion processing tunicle after covering.
Further, for cold rolled annealed plate fabricated as described above or coated steel sheet, thick in order to carry out shape correction, surface
Rugosity etc. adjust, it is also possible to implement temper rolling or leveling processing.The elongation percentage of temper rolling or leveling processing adds up to and preferably exists
In the range of 0.2～15%.When less than 0.2%, it is impossible to realize shape correction, the desired purpose of roughness adjustment.More
It is preferably more than 1.3%.On the other hand, if it exceeds 15%, then have and cause the significantly reduced tendency of ductility, the most excellent
Choosing.
Embodiment 1
Hereinafter, the present invention is described in further detail by embodiment.
The molten steel being formed into the various compositions shown in table 1 carries out melting in converter, and makes steel billet by continuous metal cast process.
Under the conditions shown in Table 2 these steel billets are implemented hot rolling, make the thick hot rolled steel plate of 3.2mm.These hot rolled steel plates are carried out
After pickling, the thick as roll material of 1.6mm is made in cold rolling by 50% rolling rate.Then, on continuous annealing production line,
Under the conditions shown in Table 2 these as roll materials are implemented continuous annealing.Further, real to the cold rolled annealed steel plate obtained
Execute the temper rolling that percentage elongation is 1.3%.Additionally, for a part of as roll material, in Continuous Hot Dip Galvanizing Line,
Implementing galvanizing after annealing under conditions of shown in table 2, implementing elongation percentage is the temper rolling of 1.3%.
For cold rolled annealed plate, the hot-dip galvanizing sheet steel of such gained, research tensile properties, structure of steel and texture.
(1) tensile properties
It is 0 ° (L direction), 45 ° (D directions) and 90 ° of (C sides from the rolling direction of each cold rolled annealed steel plate relative to gained
To) direction on cut JIS5 tension test sheet, and enter with crosshead speed 10mm/ minute according to the regulation of JIS Z 2241
Row tension test, obtains yield strength (YP), hot strength (TS), percentage elongation (El).Herein, yield strength (YP), stretching are by force
Degree (TS), percentage elongation (El), the representative value of yield ratio (YP/TS) are set to the value of the test film cut from 0 ° of direction.Will surrender
It is qualified more than intensity 400MPa to be set to.
Additionally, the index of the intra-face anisotropy as percentage elongation, use Δ El.This Δ El is each in representing the face of percentage elongation
Anisotropy, it is calculated by following formula (1).
Δ El=(El0-2El45+El90)/2···(1)
Wherein, El0、El45And El90Expression cuts from the direction in 0 ° (L direction), 45 ° (D directions) and 90 ° (C directions)
The elongation at break of test film.
If Δ El is-2%～2%, then it may be said that the intra-face anisotropy of percentage elongation is excellent.
(2) structure of steel, texture
The percentage by volume of (a) phase
About the percentage by volume of each phase, it is to measure each phase by a counting method (according to ASTM E562-83 (1988))
Area occupation ratio, and using this area occupation ratio as percentage by volume.About the area occupation ratio of each phase, cut out from each cold rolled annealed plate of gained
Take test film, for the vertical cross-section (L cross section) parallel with rolling direction, use nital to carry out corruption after grinding
Erosion, uses scanning electron microscope (SEM) to carry out observing the kind identifying phase with the multiplying power of 4000 times, and obtains martensite
The area occupation ratio (martensite percentage rate) of phase.It should be noted that in macrograph, using the particle with white contrast as horse
Family name's body.Additionally, the existence rate of retained austenite phase (remaining γ percentage rate), it is to be spread out by the plate face X-ray carrying out thickness of slab 1/4
Penetrate, measure (211), the integrated intensity of γ phase (220) of α phase (ferritic phase), and be standardized and obtain.
(b) three-dimensional crystals orientation distribution function
Carry out the plate face X-ray diffraction of the thickness of slab 1/4 of each cold rolled annealed plate of gained, and by being obtained by bounce technique
(200), (211), the incomplete pole figure of (110), use Series Expansion Method to obtain three-dimensional crystals orientation distribution function, and obtain
Alpha fibers (Φ=0 °～55 °) in average crystallite orientation density I in the range of Φ=25 °～35 °α,
With gamma fiber (Φ=55 °) average crystallite orientation density Iγ, it is evaluated.IαBe 2.0 with
Upper and less than 4.0, IγBeing the steel plate of more than 2.0 and less than 10.0, the intra-face anisotropy of its percentage elongation is little.
Show the result in table 3.
It is clear that by table 3, the height that steel grade D, E, F, H, I, N are YP >=400MPa, YR >=0.79 of the scope of the present invention
Intensity and high yield ratio steel plate.And, do not contain martensitic phase, remaining γ phase, and have and comprise ferrite+pearlite+carburizing
The tissue of body, owing to meeting IαIt is more than 2.0 and less than 4.0, IγIt is more than 2.0 and less than 10.0, therefore, it is known that △ El is-
2%～2%, the intra-face anisotropy of percentage elongation is little.Additionally, in the present invention, if steel grade D and E is compared, then understand
Sheet billet is carried out water-cooled, makes the steel grade that hot fine rolling entrance side temperature is less than 1050 DEG C and final rolling temperature is less than 890 DEG C
E, the intra-face anisotropy of its percentage elongation is less.Additionally, in the present invention, if to steel grade I and N mill model comparison, then understand to the greatest extent
Pipe is identical component, but steel grade N is low-intensity and low ductility.Thinking that its reason is that the rate of cooling of hot rolling is high, tissue becomes
Obtain uneven.
On the other hand, the YP of steel grade A, O of composition or the annealing time deviation present invention is less than 400MPa, for low-intensity.
Additionally, the texture balance of steel grade G, P, Q of the composition range of the deviation present invention is destroyed, anisotropy becomes big.Especially as
Containing martensitic phase, the steel grade G of the steel plate of retained austenite phase, not only anisotropy is big, and YR reduces.
Additionally, meet the heating of plate blank condition of steel grade B, C, J, L, M of the composition range of the present invention, annealing temperature, cooling
Time started, the final passes rate etc. of finish rolling are unsatisfactory for the scope of the present invention, and therefore texture balance is destroyed, anisotropy
Become big.
Claims (8)
1. the high-strength steel sheet that the intra-face anisotropy of percentage elongation is little, in terms of quality % containing C:0.060～0.099%,
Below Si:0.09%, Mn:1.0～1.49%, below P:0.050%, below S:0.03%, sol.Al:0.01～0.09%,
Below N:0.005%, Nb:0.035～0.080%, surplus is made up of Fe and inevitable impurity,
Described steel plate does not contains martensitic phase and retained austenite phase, in the texture in the plate face of 1/4 thickness of slab position of steel plate, ODF
Φ=25 °～35 ° in alpha fibers (φ 1=0 °, φ 2=45 °, Φ=0 °～55 °) represented by (crystalline orientation distribution function)
In the range of average crystallite orientation density IαIt is more than 2.0 and less than 4.0, gamma fiber (φ 1=0 °～60 °, φ 2=45 °, Φ
=55 °) average crystallite orientation density IγIt is more than 2.0 and less than 10.0.
The high-strength steel sheet that the intra-face anisotropy of percentage elongation the most according to claim 1 is little, wherein, in terms of quality % also
Containing Ti:0.010～0.050%.
The high-strength steel sheet that the intra-face anisotropy of percentage elongation the most according to claim 1 and 2 is little, wherein, by following (1)
Δ El represented by formula is-2%～2%,
Δ El=(El0-2El45+El90)/2···(1)
Wherein, El0、El45And El90It is relative to the fracture measured on the direction that the rolling direction of steel plate is 0 °, 45 ° and 90 °
The value of percentage elongation.
4. according to the high-strength steel sheet that the intra-face anisotropy of the percentage elongation according to any one of claims 1 to 3 is little, wherein,
Yield strength YP is more than 400MPa, and yield ratio YR (YR=YP/TS) as yield strength YP with the ratio of hot strength TS is
More than 0.79.
5., according to the high-strength steel sheet that the intra-face anisotropy of the percentage elongation according to any one of Claims 1 to 4 is little, it is at table
Mask has zinc-plated system tunicle.
6. a manufacture method for the high-strength steel sheet that the intra-face anisotropy of percentage elongation is little, prepares have claim 1 or 2 institute
The steel billet that the one-tenth stated is grouped into, heats described steel billet, keeps 60 points in the temperature range of slab heating temperature more than 1150 DEG C
After more than clock, carry out roughing, be then 15～25% in the final passes rate that final rolling temperature is 820～920 DEG C and finish rolling
Under conditions of carry out finish rolling, after finish rolling, within 2 seconds, start water-cooled cool down, manufacture after hot rolled steel plate, to described hot-rolled steel
Pickling and cold rolling implemented by plate, then when carrying out continuous annealing, and holding 10～250 seconds within the scope of the temperature more than 830 DEG C.
The manufacture method of the high-strength steel sheet that the intra-face anisotropy of percentage elongation the most according to claim 6 is little, wherein,
Make finish rolling entrance side temperature be less than 1050 DEG C by water-cooled after described roughing, then carry out described finish rolling.
8. according to the manufacture method of the little high-strength steel sheet of the intra-face anisotropy of the percentage elongation described in claim 6 or 7, its
In, the steel plate after annealing is implemented zinc-plated process.
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| JP2013218833A JP5817805B2 (en) | 2013-10-22 | 2013-10-22 | High strength steel sheet with small in-plane anisotropy of elongation and method for producing the same |
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| PCT/JP2014/005228 WO2015059903A1 (en) | 2013-10-22 | 2014-10-15 | High-strength steel sheet with small in-plane anisotropy of elongation and manufacturing method therefor |
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| CN109355583A (en) * | 2018-11-09 | 2019-02-19 | 唐山钢铁集团有限责任公司 | A kind of cold rolled annealed steel band of less anisotropy low-alloy high-strength and its production method |
| CN111621712A (en) * | 2020-05-22 | 2020-09-04 | 武汉钢铁有限公司 | Production method of low-alloy electro-galvanized steel plate with yield strength of more than or equal to 420MPa for automobile |
| CN113574190A (en) * | 2019-03-29 | 2021-10-29 | 日本制铁株式会社 | High carbon steel sheet and method for producing same |
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| CN105063484B (en) * | 2015-08-28 | 2017-10-31 | 宝山钢铁股份有限公司 | 500MPa grades of high-elongation hot-dip aluminizing zincs of yield strength and color coated steel sheet and its manufacture method |
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| CN101305110A (en) * | 2005-11-09 | 2008-11-12 | 新日本制铁株式会社 | High-tensile-strength steel sheet having reduced acoustical anisotropy, excellent weldability, yield stress of 450 MPa or larger and tensile strength of 570 MPa or larger and its production method |
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| JP2011144414A (en) * | 2010-01-13 | 2011-07-28 | Sumitomo Metal Ind Ltd | Cold rolled steel sheet and method for producing the same |
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| CN109355583A (en) * | 2018-11-09 | 2019-02-19 | 唐山钢铁集团有限责任公司 | A kind of cold rolled annealed steel band of less anisotropy low-alloy high-strength and its production method |
| CN113574190A (en) * | 2019-03-29 | 2021-10-29 | 日本制铁株式会社 | High carbon steel sheet and method for producing same |
| CN111621712A (en) * | 2020-05-22 | 2020-09-04 | 武汉钢铁有限公司 | Production method of low-alloy electro-galvanized steel plate with yield strength of more than or equal to 420MPa for automobile |
Also Published As
| Publication number | Publication date |
|---|---|
| KR101813914B1 (en) | 2018-01-02 |
| MX2016005137A (en) | 2016-07-18 |
| JP5817805B2 (en) | 2015-11-18 |
| KR20160074623A (en) | 2016-06-28 |
| JP2015081360A (en) | 2015-04-27 |
| WO2015059903A1 (en) | 2015-04-30 |
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