U.S. patent application number 12/373570 was filed with the patent office on 2009-12-24 for high strength steel plate superior in stretch flange formability and fatigue characteristics.
Invention is credited to Hiroshi Harada, Kaoru Kawasaki, Wataru Ohashi, Katsuhiro Sasai, Kenichi Yamamoto.
Application Number | 20090317285 12/373570 |
Document ID | / |
Family ID | 38923047 |
Filed Date | 2009-12-24 |
United States Patent
Application |
20090317285 |
Kind Code |
A1 |
Sasai; Katsuhiro ; et
al. |
December 24, 2009 |
HIGH STRENGTH STEEL PLATE SUPERIOR IN STRETCH FLANGE FORMABILITY
AND FATIGUE CHARACTERISTICS
Abstract
The present invention provides high strength hot rolled steel
plate superior in stretch flange formability and fatigue
characteristics comprising steel plate containing C: 0.03 to 0.20%,
Si: 0.08 to 1.5%, Mn: 1.0 to 3.0%, P: 0.05% or less, S: 0.0005% or
more, N: 0.0005 to 0.01%, acid soluble Al: 0.01% or less, acid
soluble Ti: less than 0.008%, and a total of one or both of Ce or
La: 0.0005 to 0.04%, having a balance of iron and unavoidable
impurities and having a number ratio of stretched inclusions
present in the steel plate having a circle equivalent diameter of 1
.mu.m or more and a long axis/short axis of 5 or more of 20% or
less.
Inventors: |
Sasai; Katsuhiro; (Chiba,
JP) ; Ohashi; Wataru; (Chiba, JP) ; Yamamoto;
Kenichi; (Chiba, JP) ; Kawasaki; Kaoru;
(Hyogo, JP) ; Harada; Hiroshi; (Hyogo,
JP) |
Correspondence
Address: |
BIRCH STEWART KOLASCH & BIRCH
PO BOX 747
FALLS CHURCH
VA
22040-0747
US
|
Family ID: |
38923047 |
Appl. No.: |
12/373570 |
Filed: |
March 2, 2007 |
PCT Filed: |
March 2, 2007 |
PCT NO: |
PCT/JP2007/054614 |
371 Date: |
January 13, 2009 |
Current U.S.
Class: |
420/83 |
Current CPC
Class: |
C22C 38/005 20130101;
C21D 8/0426 20130101; C22C 38/02 20130101; C22C 38/04 20130101;
C21D 9/48 20130101; C21D 9/46 20130101; C21D 2211/002 20130101 |
Class at
Publication: |
420/83 |
International
Class: |
C22C 38/04 20060101
C22C038/04 |
Claims
1. A high strength steel plate superior in stretch flange
formability and fatigue characteristics characterized by comprising
steel plate containing, by mass %, C: 0.03 to 0.20%, Si: 0.08 to
1.5%, Mn: 1.0 to 3.0%, P: 0.05% or less, S: 0.0005% or more, N:
0.0005 to 0.01%, acid soluble Al: 0.01% or less, acid soluble Ti:
less than 0.008%, and a total of one or both of Ce or La: 0.0005 to
0.04%, having a balance of iron and unavoidable impurities, and
having a number ratio of stretched inclusions present in the steel
plate having a circle equivalent diameter of 1 .mu.m or more and a
long axis/short axis of 5 or more of 20% or less.
2. A high strength steel plate superior in stretch flange
formability and fatigue characteristics characterized by comprising
steel plate containing, by mass %, C: 0.03 to 0.20%, Si: 0.08 to
1.5%, Mn: 1.0 to 3.0%, P: 0.05% or less, S: 0.0005% or more, N:
0.0005 to 0.01%, acid soluble Al: 0.01% or less, acid soluble Ti:
less than 0.008%, and a total of one or both of Ce or La: 0.0005 to
0.04%, having a balance of iron and unavoidable impurities, and
having inclusions in the steel plate comprised of an oxide or
oxysulfide of one or both of Ce or La on which MnS is precipitated
in a number ratio of 10% or more.
3. A high strength steel plate superior in stretch flange
formability and fatigue characteristics characterized by comprising
steel plate containing, by mass %, C: 0.03 to 0.20%, Si: 0.08 to
1.5%, Mn: 1.0 to 3.0%, P: 0.05% or less, S: 0.0005% or more, N:
0.0005 to 0.01%, acid soluble Al: 0.01% or less, acid soluble Ti:
less than 0.008%, and a total of one or both of Ce or La: 0.0005 to
0.04%, having a balance of iron and unavoidable impurities, and
having a volume number ratio of stretched inclusions present in the
steel plate having a circle equivalent diameter of 1 .mu.m or more
and a long axis/short axis of 5 or more of
1.0.times.10.sup.4/mm.sup.3 or less.
4. A high strength steel plate superior in stretch flange
formability and fatigue characteristics characterized by comprising
steel plate containing, by mass %, C: 0.03 to 0.20%, Si: 0.08 to
1.5%, Mn: 1.0 to 3.0%, P: 0.05% or less, S: 0.0005% or more, N:
0.0005 to 0.01%, acid soluble Al: 0.01% or less, acid soluble Ti:
less than 0.008%, and a total of one or both of Ce or La: 0.0005 to
0.04%, having a balance of iron and unavoidable impurities, and
having a volume number density of inclusions in the steel plate
comprised of an oxide or oxysulfide of one or both of Ce or La on
which MnS is precipitated in a volume number density of
1.0.times.10.sup.3/mm.sup.3 or more.
5. A high strength steel plate superior in stretch flange
formability and fatigue characteristics characterized by comprising
steel plate containing, by mass %, C: 0.03 to 0.20%, Si: 0.08 to
1.5%, Mn: 1.0 to 3.0%, P: 0.05% or less, S: 0.0005% or more, N:
0.0005 to 0.01%, acid soluble Al: 0.01% or less, acid soluble Ti:
less than 0.008%, and a total of one or both of Ce or La: 0.0005 to
0.04%, having a balance of iron and unavoidable impurities, and
having an average circle equivalent diameter of stretched
inclusions present in the steel plate having a circle equivalent
diameter of 1 .mu.m or more and a long axis/short axis of 5 or more
of 10 .mu.m or less.
6. A high strength steel plate superior in stretch flange
formability and fatigue characteristics characterized by comprising
steel plate containing, by mass %, C: 0.03 to 0.20%, Si: 0.08 to
1.5%, Mn: 1.0 to 3.0%, P: 0.05% or less, S: 0.0005% or more, N:
0.0005 to 0.01%, acid soluble Al: 0.01% or less, acid soluble Ti:
less than 0.008%, and a total of one or both of Ce or La: 0.0005 to
0.04%, having a balance of iron and unavoidable impurities, having
inclusions present in the steel plate comprising an oxide or
oxysulfide of one or both of Ce or La on which MnS is precipitated,
and having the inclusions include, in average composition, a total
of one or both of Ce or La in 0.5 to 50 mass %.
7. A high strength steel plate superior in stretch flange
formability and fatigue characteristics characterized by comprising
steel plate containing, by mass %, C: 0.03 to 0.20%, Si: 0.08 to
1.5%, Mn: 1.0 to 3.0%, P: 0.05% or less, S: 0.0005% or more, N:
0.0005 to 0.01%, acid soluble Al: 0.01% or less, acid soluble Ti:
less than 0.008%, and a total of one or both of Ce or La: 0.0005 to
0.04%, having a balance of iron and unavoidable impurities, and
having a (Ce+La)/S ratio of 0.1 to 70.
8. A high strength steel plate superior in stretch flange
formability and fatigue characteristics as set forth in any one of
claims 1 to 7 characterized by comprising steel plate containing,
by mass %, one or more of any of Nb: 0.01 to 0.10%, V: 0.01 to
0.05%, Cr: 0.01 to 0.6%, Mo: 0.01 to 0.4%, and B: 0.0003 to 0.03%
and having a balance of iron and unavoidable impurities.
Description
TECHNICAL FIELD
[0001] The present invention relates to high strength hot rolled
steel plate superior in stretch flange formability and fatigue
characteristics suitable as a material for members of an automobile
chassis.
BACKGROUND ART
[0002] From the viewpoint of improvement of automobile safety and
improvement of the fuel economy leading in turn to environmental
protection, the demands for increasing the strength and reducing
the weight of the hot rolled steel plate used for automobiles have
been growing stronger. Among auto parts, in particular, the weight
of frames, arms, etc. called "chassis parts" accounts for a high
ratio of the weight of the vehicle as a whole, so the materials
used for such locations are being made higher in strength and
smaller in thickness to enable lighter weight. Further, the
materials used for such chassis parts are required to have high
fatigue characteristics from the viewpoint of durability with
respect to the vibration during driving.
[0003] However, along with the higher strength and fatigue
resistance, the hole expandability tends to drop in the same way as
the ductility. When using high strength steel plate for the
complicatedly shaped chassis parts etc. of automobiles, this hole
expandability becomes an important matter for study.
[0004] For this reason, several types of steel plates designed to
achieve both the mechanical strength characteristics and the
fatigue characteristics and hole expandability (workability) have
been proposed. For example, Japanese Patent Publication (A) No.
11-199973 proposes steel plate comprised of composite structure
steel plate of a ferrite phase and a martensite phase in which fine
Cu is precipitated or a solid solution is dispersed (in general
called "DP steel plate"). In the technology disclosed in this
Japanese Patent Publication (A) No. 11-199973, it was found that
the solid solution Cu or CU precipitates comprised of Cu alone and
having a particle size of 2 nm or less are extremely effective for
improving the fatigue characteristics and do not impair the
workability either. The ratios of compositions of the various
ingredients were limited based on this.
[0005] It is known that such DP steel plate is superior in the
balance of strength and ductility and in the fatigue
characteristics, but the stretch flange formability, evaluated by a
hole expansion test, remains inferior. One of the reasons is
believed to be that DP steel plate is a composite of a soft ferrite
phase and a hard martensite phase, so at the time of hole
expansion, the boundary parts of the two phases cannot keep up with
the deformation and easily become starting points for breakage.
[0006] As opposed to this, high strength hot rolled steel plate
satisfying not only the fatigue characteristics, but also the tough
demands for stretch flange formability for materials of recent
wheels or chassis parts has been proposed (for example, see
Japanese Patent Publication (A) No. 2001-200331). In the technology
disclosed in Japanese Patent Publication (A) No. 2001-200331, the C
is made as low as possible to make the main phase a bainite
structure and introduce a solution strengthened or precipitation
strengthened ferrite structure in a suitable volume ratio, reduce
the difference in hardness of the ferrite and bainite, and further
avoid formation of coarse carbides.
DISCLOSURE OF THE INVENTION
[0007] High strength hot rolled steel plate having a steel plate
structure of mainly a bainite phase and suppressing the formation
of coarse carbides such as disclosed in said Japanese Patent
Publication (A) No. 2001-200331 does indeed exhibit a superior
stretch flange formability, but cannot necessarily be said to be
superior in fatigue characteristics compared with DP steel plate
containing Cu. Further, with just suppressing the formation of
coarse carbides, it is not possible to prevent the occurrence of
cracks at the time of extreme hole expansion. According to the
research of the inventors, the cause is the presence of stretched
sulfide-based inclusions mainly comprised of MnS in the steel
plate. Upon repeated deformation, internal defects form near the
stretched coarse MnS-based inclusions present at the surface layer
or its vicinity and propagate as cracks to thereby cause
deterioration of the fatigue characteristics. Again, stretched
coarse MnS-based inclusions easily become starting points of
cracking at the time of hole expansion. For this reason, it is
preferable not to allow the MnS-based inclusions in the steel to
stretch as much as possible but to make them finely spherical.
[0008] However, Mn is an element effectively contributing to the
increase in strength of a material along with C and Si, but with
high strength steel plate, to secure strength, the general practice
has been to set the concentration of Mn high. Furthermore, if not
performing the overlapping treatment of desulfurization in the
secondary refining process, an S concentration of 50 ppm or more
ends up being included. For this reason, a cast slab usually
contains MnS. If the cast slab is hot rolled and cold rolled, the
MnS easily deforms, so becomes stretched MnS-based inclusions.
These become causes lowering the fatigue characteristics and
stretch flange formability (hole expandability). However, no
example has been found proposing hot rolled steel plate superior in
stretch flange formability and fatigue characteristics from the
viewpoint of control of the precipitation and deformation of
MnS.
[0009] Therefore, the present invention was proposed in
consideration of the above points and has as its object the
provision of high strength steel plate superior in stretch flange
formability and fatigue characteristics improving the stretch
flange formability and the fatigue characteristics by causing the
precipitation of fine MnS in the cast slab and making this disperse
as fine spherical inclusions not deformed and not easily becoming
starting points of cracking in the steel plate at the time of
rolling.
[0010] To solve the problems described above, the inventors engaged
in in-depth studies on the method of making fine MnS precipitate in
cast slabs and making this disperse as fine spherical inclusions
not deformed and not easily becoming starting points of cracking at
the time of rolling and to clarify the additive elements not
causing deterioration of the fatigue characteristics. As a result,
they learned that MnS precipitates on the fine, hard Ce oxides, La
oxides, cerium oxysulfides, and lanthanum oxysulfides formed due to
deoxidation due to addition of Ce and La, the thus precipitated MnS
is resistant to deformation at the time or rolling as well, so the
amount of stretched coarse MnS in the steel plate is remarkably
reduced and, at the time of repeated deformation or at the time of
hole expansion, these MnS-based inclusions do not easily become
starting points of cracking or routes for crack propagation and
that this leads to an improvement in the fatigue resistance
etc.
[0011] The high strength steel plate superior in stretch flange
formability and fatigue characteristics according to the present
invention has as its gist the following:
[0012] (1) A high strength steel plate superior in stretch flange
formability and fatigue characteristics characterized by comprising
steel plate containing, by mass %, C: 0.03 to 0.20%, Si: 0.08 to
1.5%, Mn: 1.0 to 3.0%, P: 0.05% or less, S: 0.0005% or more, N:
0.0005 to 0.01%, acid soluble Al: 0.01% or less, acid soluble Ti:
less than 0.008%, and a total of one or both of Ce or La: 0.0005 to
0.04%, having a balance of iron and unavoidable impurities, and
having a number ratio of stretched inclusions present in the steel
plate having a circle equivalent diameter of 1 .mu.m or more and a
long axis/short axis of 5 or more of 20% or less.
[0013] (2) A high strength steel plate superior in stretch flange
formability and fatigue characteristics characterized by comprising
steel plate containing, by mass %, C: 0.03 to 0.20%, Si: 0.08 to
1.5%, Mn: 1.0 to 3.0%, P: 0.05% or less, S: 0.0005% or more, N:
0.0005 to 0.01%, acid soluble Al: 0.01% or less, acid soluble Ti:
less than 0.008%, and a total of one or both of Ce or La: 0.0005 to
0.04%, having a balance of iron and unavoidable impurities, and
having inclusions in the steel plate comprised of an oxide or
oxysulfide of one or both of Ce or La on which MnS is precipitated
in a number ratio of 10% or more.
[0014] (3) A high strength steel plate superior in stretch flange
formability and fatigue characteristics characterized by comprising
steel plate containing, by mass %, C: 0.03 to 0.20%, Si: 0.08 to
1.5%, Mn: 1.0 to 3.0%, P: 0.05% or less, S: 0.0005% or more, N:
0.0005 to 0.01%, acid soluble Al: 0.01% or less, acid soluble Ti:
less than 0.008%, and a total of one or both of Ce or La: 0.0005 to
0.04%, having a balance of iron and unavoidable impurities, and
having a volume number ratio of stretched inclusions present in the
steel plate having a circle equivalent diameter of 1 .mu.m or more
and a long axis/short axis of 5 or more of
1.0.times.10.sup.4/mm.sup.3 or less.
[0015] (4) A high strength steel plate superior in stretch flange
formability and fatigue characteristics characterized by comprising
steel plate containing, by mass %, C: 0.03 to 0.20%, Si: 0.08 to
1.5%, Mn: 1.0 to 3.0%, P: 0.05% or less, S: 0.0005% or more, N:
0.0005 to 0.01%, acid soluble Al: 0.01% or less, acid soluble Ti:
less than 0.008%, and a total of one or both of Ce or La: 0.0005 to
0.04%, having a balance of iron and unavoidable impurities, and
having a volume number density of inclusions in the steel plate
comprised of an oxide or oxysulfide of one or both of Ce or La on
which MnS is precipitated in a volume number density of
1.0.times.10.sup.3/mm.sup.3 or more.
[0016] (5) A high strength steel plate superior in stretch flange
formability and fatigue characteristics characterized by comprising
steel plate containing, by mass %, C: 0.03 to 0.20%, Si: 0.08 to
1.5%, Mn: 1.0 to 3.0%, P: 0.05% or less, S: 0.0005% or more, N:
0.0005 to 0.01%, acid soluble Al: 0.01% or less, acid soluble Ti:
less than 0.008%, and a total of one or both of Ce or La: 0.0005 to
0.04%, having a balance of iron and unavoidable impurities, and
having an average circle equivalent diameter of stretched
inclusions present in the steel plate having a circle equivalent
diameter of 1 .mu.m or more and a long axis/short axis of 5 or more
of 10 .mu.m or less.
[0017] (6) A high strength steel plate superior in stretch flange
formability and fatigue characteristics characterized by comprising
steel plate containing, by mass %, C: 0.03 to 0.20%, Si: 0.08 to
1.5%, Mn: 1.0 to 3.0%, P: 0.05% or less, S: 0.0005% or more, N:
0.0005 to 0.01%, acid soluble Al: 0.01% or less, acid soluble Ti:
less than 0.008%, and a total of one or both of Ce or La: 0.0005 to
0.04%, having a balance of iron and unavoidable impurities, having
inclusions present in the steel plate comprising an oxide or
oxysulfide of one or both of Ce or La on which MnS is precipitated,
and having the inclusions include, in average composition, a total
of one or both of Ce or La in 0.5 to 50 mass %.
[0018] (7) A high strength steel plate superior in stretch flange
formability and fatigue characteristics characterized by comprising
steel plate containing, by mass %, C: 0.03 to 0.20%, Si: 0.08 to
1.5%, Mn: 1.0 to 3.0%, P: 0.05% or less, S: 0.0005% or more, N:
0.0005 to 0.01%, acid soluble Al: 0.01% or less, acid soluble Ti:
less than 0.008%, and a total of one or both of Ce or La: 0.0005 to
0.04%, having a balance of iron and unavoidable impurities, and
having a (Ce+La)/S ratio of 0.1 to 70.
[0019] (8) A high strength steel plate superior in stretch flange
formability and fatigue characteristics as set forth in any one of
(1) to (7) characterized by comprising steel plate containing, by
mass %, one or more of any of Nb: 0.01 to 0.10%, V: 0.01 to 0.05%,
Cr: 0.01 to 0.6%, Mo: 0.01 to 0.4%, and B: 0.0003 to 0.03% and
having a balance of iron and unavoidable impurities.
BRIEF DESCRIPTION OF THE DRAWINGS
[0020] FIG. 1 is a view showing the relationship of Ce+La (%) and S
(%).
BEST MODE FOR CARRYING OUT THE INVENTION
[0021] Below, as the best mode for carrying out the present
invention, high strength steel plate superior in stretch flange
formability and fatigue characteristics will be studied in detail.
Below, the "mass %" in the composition will be simply described as
"%".
[0022] First, the experiments leading to the completion of the
present invention will be explained.
[0023] The inventors deoxidized molten steel containing C, 0.07%,
Si: 0.2%, Mn: 1.2%, P: 0.01% or less, S: 0.005%, and N: 0.003% and
having a balance of Fe using various elements and produced steel
ingots. They hot rolled the obtained steel ingots to obtain 3 mm
hot rolled steel plate. They then used the thus produced hot rolled
steel plate for hole expansion tests and fatigue tests and
investigated the number density, form, and average composition of
the inclusions in the steel plate.
[0024] As a result, they learned that steel plate not deoxidized
much at all by Al, but given Si, then given at least Ce and La for
deoxidation was the most superior in stretch flange formability and
fatigue characteristics. The reason is that MnS precipitates on
fine, hard Ce oxides, La oxides, cerium oxysulfides, and lanthanum
oxysulfides formed due to deoxidation due to addition of Ce and La,
the precipitated MnS is resistant to deformation at the time of
rolling as well, and therefore the stretched coarse MnS remarkably
decreases in the steel plate. As a result, these MnS-based
inclusions do not easily become starting points of cracking or
routes of crack propagation at the time of repeated deformation or
at the time of hole expansion. This leads to improvement of the
fatigue resistance etc. as explained above.
[0025] Note that the reason why the Ce oxides, La oxides, cerium
oxysulfides, and lanthanum oxysulfides become finer is that the
SiO.sub.2-based inclusions first formed by Si deoxidation are
reduced and broken up by the later added Ce and La to form fine Ce
oxides, La oxides, cerium oxysulfides, and lanthanum oxysulfides
and, furthermore, the interfacial energy between the formed Ce
oxides, La oxides, cerium oxysulfides, and lanthanum oxysulfides
themselves and the molten steel is low, so clustering after
formation is also suppressed.
[0026] Based on the findings obtained from these experimental
studies, as explained below, the inventors studied the conditions
for the chemical ingredients of steel plate and completed the
present invention.
[0027] Below, the reasons for limiting the chemical ingredients in
the present invention will be explained.
[0028] C: 0.03 to 0.20%
[0029] C is the most basic element for controlling the
quenchability and strength of steel. It increases the hardness and
depth of the quenched hardened layer and effectively contributes to
the improvement of the fatigue strength. That is, this C is an
essential element for securing the strength of steel plate. To
obtain high strength steel plate, at least 0.03% is necessary.
However, if this C is excessively included, the C is fixed by the
formation of Ti carbides like in the past or even if using cooling
conditions, a cementite phase ends up being formed. This cementite
phase causes work hardening of the steel plate and is not
preferable for improvement of the stretch flange formability
characteristics. For this reason, in the present invention, from
the viewpoint of improving the workability, the concentration of C
is made 0.20% or less.
[0030] Si: 0.08 to 1.5%
[0031] Si becomes an important deoxidizing element in molten steel
to which Al or Ti are not added as much as possible like in the
present invention, so is extremely important in the present
invention. Further, Si has the function of increasing the
nucleation sites of austenite at the time of quenching heating and
suppressing the grain growth of the austenite and of making the
grain size of the quenched hardened layer finer. This Si suppresses
carbide formation and suppresses the drop in grain boundary
strength due to carbides. Furthermore, this Si is effective against
the formation of a bainite structure as well and plays an important
role in terms of securing the strength of the material as a whole.
To lower the concentration of solute oxygen in the molten steel and
cause the formation of SiO.sub.2-based inclusions once (to reduce
the SiO.sub.2-based inclusions by the later added Ce and La and
thereby make the inclusions finer), it is necessary to add Si in
0.08% or more. For this reason, in the present invention, the lower
limit of Si was made 0.08%. As opposed to this, if the Si
concentration is too high, the concentration of SiO.sub.2 in the
inclusions becomes higher and large inclusions become easier to
form or the toughness and ductility become extremely poor and the
surface decarburization and surface flaws increase, so the fatigue
characteristics conversely deteriorate. In addition to this, if
excessively adding Si, the weldability and the ductility are
detrimentally affected. For this reason, in the present invention,
the upper limit of the Si was made 1.5%.
[0032] Mn: 1.0 to 3.0%
[0033] Mn is an element useful for deoxidization in the steelmaking
stage. Along with C and Si, it is an element effective for raising
the strength of the steel plate. To obtain this effect, it is
necessary to include this Mn in 1.0% or more. However, if Mn is
included in an amount over 3.0%, the ductility drops due to the
segregation of Mn and solution strengthening. Further, the
weldability and matrix toughness also deteriorate, so the upper
limit of Mn is made 3.0%.
[0034] P: 0.05% or less
[0035] P is effective in the point of acting as a substitution type
solution strengthening element smaller than Fe atoms, but
segregates at the grain boundaries of the austenite and causes a
drop in the grain boundary strength, so causes a drop in the
torsional fatigue strength. Deterioration of the workability is a
concern, so the amount is made 0.05% or less. Further, if not
necessary for solution strengthening, P does not have to be added.
The lower limit value of P therefore includes 0%.
[0036] S: 0.0005% or more
[0037] S segregates as an impurity. S forms coarse stretched
inclusions of MnS and causes deterioration in the stretch flange
formability, so as low a concentration as possible is desirable. In
the past, to secure stretch flange formability, the concentration
of S had to be made an ultralow one of less than 0.0005%. However,
in the present invention, fine MnS is made to precipitate on the
hard Ce oxides, La oxides, cerium oxysulfides, and lanthanum
oxysulfides to make deformation at the time of rolling difficult
and prevent stretching of the inclusions, so the upper limit value
of the concentration of S is not particularly defined.
[0038] Further, to reduce the S concentration to a level equal to
the past of less than 0.0005%, it is necessary to considerably
strengthen the desulfurization in the secondary refining. The cost
of the desulfurization for achieving this concentration becomes too
high and the effect of controlling the shape of the MnS becomes
difficult to obtain, so the lower limit value of the S
concentration is made 0.0005%.
[0039] N: 0.0005 to 0.01%
[0040] N is an element which is unavoidably mixed in the steel
since nitrogen in the air is taken in during the melting process. N
forms nitrides together with Al, Ti, etc. to promote the increased
fineness of the matrix structure. However, if overly adding this N,
even with a fine amount of Al or a fine amount of Ti, coarse
precipitates are formed and the stretch flange formability is
degraded. For this reason, in the present invention, the upper
limit of the concentration of N was made 0.01%. On the other hand,
to make the concentration of N less than 0.0005%, the cost becomes
high, so 0.0005% is made the lower limit.
[0041] Acid soluble Al: 0.01% or less
[0042] With acid soluble Al, the oxides easily cluster and become
coarse, so this is preferably suppressed as much as possible to
prevent deterioration of the stretch flange formability and the
fatigue characteristics. However, use as a preliminary deoxidizing
material up to 0.01% is allowed. This is because if the acid
soluble Al concentration is over 0.01%, the Al.sub.2O.sub.3 content
in the inclusions exceeds 50% and the inclusions cluster. From the
viewpoint of preventing clustering, the lower the acid soluble Al
concentration the better. The lower limit value includes 0%.
Further, the "acid soluble Al concentration" measures the
concentration of Al dissolved in an acid, so is a method of
analysis utilizing the fact that solute Al dissolves in acid while
Al.sub.2O.sub.3 does not dissolve in acid. Here, the "acid" means,
for example, a mixed acid of a mixture of hydrochloric acid in 1
part, nitric acid in 1 part, and water in 2 parts (mass ratio).
Using such an acid, it is possible to separate acid soluble Al and
Al.sub.2O.sub.3 not dissolving in an acid and measure the acid
soluble Al concentration.
[0043] Acid soluble Ti: less than 0.008%
[0044] With acid soluble Ti as well, the oxides easily cluster and
become coarse. Further, this bonds with the N in the steel to form
coarse TiN inclusions. Therefore, the acid soluble Ti is made less
than 0.008%. The lower limit value includes 0%. Further, the "acid
soluble Ti concentration" measures the concentration of Ti
dissolved in an acid, so is a method of analysis utilizing the fact
that solute Ti dissolved in acid, while Ti oxide does not dissolve
in acid. Here, the "acid" means, for example, a mixed acid of a
mixture of hydrochloric acid in 1 part, nitric acid in 1 part, and
water in 2 parts (mass ratio). Using such an acid, it is possible
to separate acid soluble Ti and Ti oxides not dissolving in an acid
and measure the acid soluble Ti concentration.
[0045] Total of one or both of Ce or La: 0.0005 to 0.04%
[0046] Ce and La have the effect of reducing the SiO.sub.2 produced
by Si deoxidation and forming inclusions having Ce oxides (for
example, Ce.sub.2O.sub.3, CeO.sub.2), cerium oxysulfides (for
example, Ce.sub.2O.sub.2S), La oxides (for example,
La.sub.2O.sub.3, LaO.sub.2), lanthanum oxysulfides (for example,
La.sub.2O.sub.2S), Ce oxide-La oxides, or cerium
oxysulfide-lanthanum oxysulfides as main phases (50% or more as a
rule of thumb) which easily become Mn precipitating sites and are
hard, fine, and resistant to deformation at the time of
rolling.
[0047] Here, these inclusions sometimes also partially contain MnO,
SiO.sub.2, or Al.sub.2O.sub.3 depending on the deoxidizing
conditions, but if the main phase is such an oxide, they will
sufficiently function as MnS precipitating sites and the effect of
increasing the fineness and hardness of the inclusions will not be
impaired. To obtain such inclusions, the total concentration of the
one or both of Ce or La must be made 0.0005% to 0.04%. If the total
concentration of the one or both of Ce or La is less than 0.0005%,
the SiO.sub.2 inclusions cannot be reduced, while if over 0.04%,
large amounts of cerium oxysulfide and lanthanum oxysulfide are
produced and form coarse inclusions which degrade the stretch
flange formability and fatigue characteristics.
[0048] Nb: 0.01 to 0.10%
[0049] Nb forms carbides, nitrides, and carbonitrides with C or N
to promote the increased fineness of the matrix structure. To
obtain this effect, at least 0.01% is necessary. However, even if
included in a large amount over 0.10%, the effect is saturated and
the cost becomes high, so 0.10% is made the upper limit.
[0050] V: 0.01 to 0.05%
[0051] V forms carbides, nitrides, and carbonitrides with C or N to
promote the increased fineness of the matrix structure. To obtain
this effect, at least 0.01% is necessary. However, even if included
in a large amount over 0.05%, the effect is saturated and the cost
becomes high, so 0.05% is made the upper limit.
[0052] Cr: 0.01 to 0.6%
[0053] Cr may be included as necessary to improve the quenchability
of steel and secure strength of the steel plate. To obtain this
effect, at least 0.01% is necessary. However, inclusion of a large
amount conversely degrades the balance of strength and ductility.
Therefore, 0.6% is made the upper limit.
[0054] Mo: 0.01 to 0.4%
[0055] Mo may be included as necessary to improve the quenchability
of steel and secure strength of the steel plate. To obtain this
effect, at least 0.01% is necessary. However, inclusion of a large
amount conversely degrades the balance of strength and ductility.
Therefore, 0.4% is made the upper limit.
[0056] B: 0.0003 to 0.003%
[0057] B may be included as necessary to improve the quenchability
of steel, strengthen the grain boundaries, and improve the
workability. To obtain this effect, at least 0.0003% is necessary.
However, inclusion of a large amount conversely detracts from the
cleanliness of the steel and degrades the ductility. Therefore,
0.003% is made the upper limit.
[0058] Next, the conditions of presence of the inclusions in the
steel plate of the present invention will be explained. Further,
the "steel plate" means the plate after rolling obtained by hot
rolling or further cooling rolling.
[0059] To obtain the steel plate superior in stretch flange
formability and fatigue characteristics, it is important to reduce
as much as possible the stretched coarse MnS-based inclusions
easily becoming starting points of cracking and routes for crack
propagation in the steel plate. The inventors discovered through
experiments that MnS-based inclusions with a circle equivalent
diameter of less than 1 .mu.m are harmless as starting points of
cracking and do not cause deterioration of the stretch flange
formability or fatigue characteristics. Further, inclusions with a
circle equivalent diameter of 1 .mu.m or more are easily observed
by a scan type electron microscope (SEM) etc., so the inventors
investigated the shape and composition of inclusions in steel plate
with a circle equivalent diameter of 1 .mu.m or more and evaluated
the state of distribution of the MnS-based inclusions. Here, the
"circle equivalent diameter" is defined as the (long
axis.times.short axis).sup.0.5 found from the long axis and short
axis of inclusions observed in cross-section.
[0060] Note that the upper limit of the circle equivalent diameter
of the MnS-based inclusions is not particularly limited, but in
practice MnS-based inclusions of about 1 mm are observed.
[0061] The number ratio of the stretched inclusions is found by
analyzing the composition of a plurality of randomly selected
inclusions (for example 50 or so) with a circle equivalent diameter
of 1 .mu.m or more using an SEM and measuring the long axes and
short axes of the inclusions from the SEM image. Here, when
defining "stretched inclusions" as inclusions with a long
axis/short axis (stretch ratio) of 5 or more, the number ratio of
the stretched inclusions can be found by dividing the detected
number of stretched inclusions by the total number of inclusions
investigated (in the above example, 50 or so).
[0062] Note that the stretch ratio of the inclusions was made 5 or
more because the inclusions with a stretch ratio of 5 or more in
comparative steel plate not containing La are almost all MnS-based
inclusions. Further, the upper limit of the stretch ratio of the
MnS-based inclusions is not particularly limited, but in practice
MnS-based inclusions with a stretch ratio of 50 or so are sometimes
observed.
[0063] As a result, it was learned that with steel plate controlled
in form to a number ratio of stretched inclusions with a stretch
ratio of 5 or more of 20% or less, the stretch flange formability
and the fatigue characteristics are improved. That is, if the
number ratio of the stretched inclusions with a stretch ratio of 5
or more exceeds 20%, the number of MnS-based stretched inclusions
easily becoming starting points of cracking becomes too large and
the stretch flange formability and the fatigue characteristics
drop. In the present invention, the number ratio of stretched
inclusions with a stretch ratio of 5 or more is made 20% or less.
Further, the stretch flange formability and the fatigue
characteristics are better the small the number of stretched
MnS-based inclusions, so the lower limit value of the number ratio
of the stretched inclusions with a stretch ratio of 5 or more
includes 0%.
[0064] Here, the lower limit value of the number ratio of stretched
inclusions with a circle equivalent diameter of 1 .mu.m or more and
with a stretch ratio of 5 or more being 0% means when there are
inclusions with a circle equivalent diameter of 1 .mu.m or more,
but none with a stretch ratio of 5 or more or when there are
stretched inclusions with a stretch ratio of 5 or more, but all
have a circle equivalent diameter of less than 1 .mu.m.
[0065] Further, in steel plate controlled to a form with a number
ratio of the stretched inclusions with a stretch ratio of 5 or more
of 20% or less, in accordance with this, MnS precipitates on the
oxide or oxysulfide of one or both of Ce or La. The form of the
inclusions is not particularly limited so long as MnS precipitates
on an oxide or oxysulfide of one or both of Ce or La, but usually
is an oxide or oxysulfide of one or both of Ce or La as core around
which the MnS precipitates.
[0066] Further, inclusions comprised of an oxide or oxysulfide of
one or both of Ce or La on which MnS has precipitated are resistant
to deformation even at the time of rolling, so become unstretched
shapes even in the steel plate, that is, substantially spherical
inclusions.
[0067] Here, the spherical inclusions judged as not stretched are
not particularly limited, but may be inclusions in the steel plate
with a stretch ratio of 3 or less, preferably inclusions with a
ratio of 2 or less. This is because at the cast slab stage before
the rolling, the stretch ratio of the inclusions of a form of an
oxide or oxysulfide of one or both of Ce or La on which MnS is
precipitated was 3 or less. Further, if spherical inclusions judged
as not stretched are completely spherical, the stretch ratio would
become 1, so the lower limit of the stretch ratio is 1.
[0068] The number ratio of the inclusions was investigated by a
method similar to the investigation of the number ratio of the
stretched inclusions. As a result, it was learned that in steel
plate controlled in precipitation to have a number ratio of
inclusions of a form of an oxide or oxysulfide of one or both of Ce
or La on which MnS is precipitated of 10% or more, the stretch
flange formability and the fatigue characteristics are improved. If
the number ratio of inclusions of a form of an oxide or oxysulfide
of one or both of Ce or La on which MnS is precipitated becomes
less than 10%, in accordance with this, the number ratio of
MnS-based stretched inclusions becomes too large and the stretch
flange formability and the fatigue characteristics fall. For this
reason, the number ratio of inclusions of a form of an oxide or
oxysulfide of one or both of Ce or La on which MnS is precipitated
is made 10% or more. Further, the stretch flange formability and
the fatigue characteristics become better with a large amount of
MnS precipitated on oxides or oxysulfides of one or both of Ce or
La, so the upper limit value of the number ratio includes 100%.
[0069] Note that inclusions of a form of an oxide or oxysulfide of
one or both of Ce or La on which MnS is precipitated are resistant
to deformation even at the time of rolling, so the circle
equivalent diameter is not particularly limited, but may be 1 .mu.m
or more. However, if too large, the inclusions may form starting
points of cracking, so the upper limit is preferably 50 .mu.m or
so.
[0070] On the other hand, not only are the inclusions resistant to
deformation even at the time of rolling, but when the circle
equivalent diameter is less than 1 .mu.m, they will also not form
starting points of cracking, so the lower limit of the circle
equivalent diameter is not particularly defined.
[0071] Next, as a condition of presence of inclusions in the steel
plate of the present invention explained above, the number density
of inclusions per unit volume is defined.
[0072] The distribution of particle size of the inclusions was
obtained by SEM evaluation of the electrolyzed surface by the speed
method. "SEM evaluation of the electrolyzed surface by the speed
method" means polishing the surface of a sample piece, then
electrolyzing it by the speed method and directly evaluating the
sample surface by an SEM to evaluate the size and number density of
the inclusions. Note that the "speed method" is the method of using
10% acetyl acetone-1% tetramethyl ammonium chloride-methanol to
electrolyze the sample surface and extract the inclusions. As the
amount of electrolysis, 1 C per 1 cm.sup.2 area of the sample
surface was electrolyzed. An SEM image of the thus electrolyzed
surface was processed to find the distribution of frequency
(number) with respect to the circle equivalent diameter. From this
distribution of frequency of the particle size, the average circle
equivalent diameter was calculated. Further, the frequency was
divided by the depth found by the area of the observed field and
the amount of electrolysis to calculate the number density of
inclusions per volume.
[0073] The inventors evaluated the volume number density of
inclusions with a circle equivalent diameter of 1 .mu.m or more and
with a stretch ratio of 5 or more becoming starting points of
cracking and degrading the stretch flange formability and the
fatigue characteristics and as a result learned that if
1.0.times.10.sup.4/mm.sup.3 or less, the stretch flange formability
and the fatigue characteristics are improved. If the volume number
density of stretched inclusions with a circle equivalent diameter
of 1 .mu.m or more and with a stretch ratio of 5 or more is over
1.0.times.10.sup.4/mm.sup.3, the number density of the MnS-based
stretched inclusions easily becoming starting points of cracking
becomes too large and the and the stretch flange formability and
the fatigue characteristics fall, so the volume number density of
stretched inclusions with a circle equivalent diameter of 1 .mu.m
or more and with a stretch ratio of 5 or more is made
1.0.times.10.sup.4/mm.sup.3 or less. Further, the stretch flange
formability and the fatigue characteristics are better the smaller
the stretched MnS-based inclusions, so the lower limit value of the
volume number density with a circle equivalent diameter 1 .mu.m or
more and with a stretch ratio of 5 or more includes 0%.
[0074] Here, the lower limit value of the volume number density of
stretched inclusions with a circle equivalent diameter of 1 .mu.m
or more and with a stretch ratio of 5 or more being 0% means the
same as the above.
[0075] Further, in steel plate controlled to a form with a volume
number density of stretched inclusions with a diameter of 1 .mu.m
or more and with a stretch ratio of 5 or more of
1.0.times.10.sup.4/mm.sup.3 or less, in accordance with this, the
unstretched MnS-based inclusions become a form of an oxide or
oxysulfide of one or both of Ce or La on which MnS is precipitated.
The shape was substantially spherical inclusions.
[0076] The form of the inclusions, in the same way as the above, is
not particularly limited so long as it is an oxide or oxysulfide of
one or both of Ce or La on which MnS is precipitated, but usually
it is an oxide or oxysulfide of one or both of Ce or La as a core
around which MnS is precipitated.
[0077] Further, the "spherical inclusions" is not particularly
limited, but refers to inclusions in the steel plate with a stretch
ratio of 3 or less, preferably inclusions with a ratio of 2 or
less. Here, if completely spherical, the stretch ratio becomes 1,
so the lower limit of the stretch ratio is 1.
[0078] The inventors investigated the volume number density of such
inclusions and as a result learned that with steel plate controlled
in precipitation to give a volume number density of inclusions of a
form of an oxide or oxysulfide of one or both of Ce or La as a core
around which MnS is precipitated of 1.0.times.10.sup.3/mm.sup.3 or
more, the stretch flange formability and the fatigue
characteristics are improved. If the volume number density of
inclusions of a form of an oxide or oxysulfide of one or both of Ce
or La on which MnS is precipitated is less than
1.0.times.10.sup.3/mm.sup.3, in accordance with this, the number
ratio of the MnS-based stretched inclusions becomes too large and
the stretch flange formability and the fatigue characteristics
fall, so the volume number density of inclusions of a form of an
oxide or oxysulfide of one or both of Ce or La on which MnS is
precipitated is defined as 1.0.times.10.sup.3/mm.sup.3 or more.
Further, the stretch flange formability and the fatigue strength
become better the more the MnS precipitated around cores of an
oxide or oxysulfide of one or both of Ce or La, so the upper limit
value of the volume number density is not particularly defined.
[0079] Note that the circle equivalent diameter of inclusions of a
form of an oxide or oxysulfide of one or both of Ce or La on which
MnS is precipitated, in the same way as above, is not particularly
limited, but may be 1 .mu.m or more. However, if this circle
equivalent diameter is too large, the inclusions are liable to
become starting points of cracking, so the upper limit is
preferably 50 .mu.m or so.
[0080] On the other hand, when the circle equivalent diameter of
the inclusions is less than 1 .mu.m, there is no problem at all, so
the lower limit is not particularly defined.
[0081] Next, as a condition of presence of stretched inclusions in
the steel plate of the present invention described above, the upper
limit of the circle equivalent diameter is defined. Specifically,
the inventors evaluated the average circle equivalent diameter of
inclusions with a circle equivalent diameter of 1 .mu.m or more and
with a stretch ratio of 5 or more forming starting points of
cracking and degrading the stretch flange formability and fatigue
characteristics and as a result learned that if the average circle
equivalent diameter of the stretched inclusions is 10 .mu.m or
less, the stretch flange formability and fatigue characteristics
are improved. The inventors took note of the fact that along with
an increase in the number ratio of the stretched inclusions with a
circle equivalent diameter of 1 .mu.m or more and with a stretch
ratio of 5 or more, the average circle equivalent diameter of the
stretched inclusions becomes larger and defined the average circle
equivalent diameter of the stretched inclusions as an indicator.
They guessed that as the amount of Mn or S in the steel increases,
the number of MnS formed increases and the formed MnS becomes
coarser in size.
[0082] Therefore, if the stretched inclusions with a circle
equivalent diameter of 1 .mu.m or more and with a stretch ratio of
5 or more exceed 10 .mu.m, in accordance with this, the number
ratio of the stretched inclusions exceeds 20%, so the number ratio
of coarse MnS-based stretched inclusions easily becoming starting
points of cracking becomes too large and the stretch flange
formability and fatigue characteristics fall, therefore the average
circle equivalent diameter of the stretched inclusions with a
circle equivalent diameter of 1 .mu.m or more and with a stretch
ratio of 5 or more is made 10 .mu.m or less.
[0083] Note that defining the average circle equivalent diameter of
stretched inclusions with a circle equivalent diameter of 1 .mu.m
or more and with a stretch ratio of 5 or more as 10 .mu.m or less
means the case where inclusions with a circle equivalent diameter
of 1 .mu.m or more are present in the steel plate, so the lower
limit value of the circle equivalent diameter becomes 1 .mu.m.
[0084] On the other hand, as a condition of presence of inclusions
of a form of an oxide or oxysulfide of one or both of Ce or La on
which MnS is precipitated in the steel plate of the present
invention explained above, the content of the average composition
of Ce or La in the inclusions where MnS is precipitated is
defined.
[0085] Specifically, as explained above, in improving the stretch
flange formability and fatigue characteristics, it is important to
make MnS precipitate over an oxide or oxysulfide of one or both of
Ce or La and prevent stretching of the MnS.
[0086] The form of the inclusions, in the same way as the above, is
not particularly limited so long as MnS precipitates on an oxide or
oxysulfide of one or both of Ce or La, but in most cases it
comprises an oxide or oxysulfide of one or both of Ce or La as a
core around which MnS is precipitated.
[0087] Further, the spherical inclusions are not particularly
limited, but may be inclusions in the steel plate with a stretch
ratio of 3 or less, preferably inclusions with a ratio of 2 or
less. Here, if completely spherical, the stretch ratio is 1, so the
lower limit of the stretch ratio is 1.
[0088] Therefore, to clarify the composition effective for
suppressing stretching of the MnS-based inclusions, the inventors
analyzed the composition of inclusions of a form of an oxide or
oxysulfide of one or both of Ce or La on which MnS is
precipitated.
[0089] However, if the circle equivalent diameter of the inclusions
is 1 .mu.m or more, observation becomes easy, so for convenience
they covered a circle equivalent diameter of 1 .mu.m or more.
However, if observation is possible, inclusions with a circle
equivalent diameter of less than 1 .mu.m may also be included.
[0090] Further, inclusions of a form of an oxide or oxysulfide of
one or both of Ce or La on which MnS is precipitated do not
stretch, so it was confirmed that the stretch ratio was 3 or less
in all of the inclusions. Therefore, the inventors analyzed the
composition of inclusions with a circle equivalent diameter of 1
.mu.m or more and with a stretch ratio of 3 or less.
[0091] As a result, they learned that if inclusions with a circle
equivalent diameter of 1 .mu.m or more and with a stretch ratio of
3 or less contain, in average composition, a total of one or both
of Ce or La of 0.5 to 50%, the stretch flange formability and the
fatigue characteristics are improved. If the average content of the
total of one or both of Ce or La in the inclusions with a circle
equivalent diameter of 1 .mu.m or more and a stretch ratio of 3 or
less becomes less than 0.5 mass %, the number ratio of the
inclusions of a form of an oxide or oxysulfide of one or both of Ce
or La on which MnS is precipitated is greatly reduced and, in
accordance with this, the number ratio of MnS-based stretched
inclusions easily becoming starting points of cracking becomes too
large and the stretch flange formability and fatigue
characteristics fall.
[0092] On the other hand, if the average content of the total of
one or both of Ce or La in the inclusions with a circle equivalent
diameter of 1 .mu.m or more and with a stretch ratio of 3 or less
exceeds 50%, large amounts of cerium oxysulfides and lanthanum
oxysulfides are formed and coarse inclusions with a circle
equivalent diameter of 50 .mu.m or so or more are formed, so the
stretch flange formability and fatigue characteristics are
degraded.
[0093] Further, as a condition of presence of inclusions of a form
of an oxide or oxysulfide of one or both of Ce or La on which MnS
is precipitated in the steel plate of the present invention, the
chemical ingredient (Ce+La)/S ratio of the steel plate is
defined.
[0094] Specifically, as explained above, in improving the stretch
flange formability and fatigue characteristics, the ratio of
chemical ingredients for making MnS precipitate on an oxide or
oxysulfide of one or both of Ce or La and preventing stretching of
the MnS is important.
[0095] Therefore, to clarify the ratio of chemical ingredients
effective for suppressing stretching of MnS-based inclusions, the
inventors changed the (Ce+La)/S ratio of the steel plate and
evaluated the form of the inclusions, stretch flange formability,
and fatigue characteristics (FIG. 1). As a result, they learned
that when the (Ce+La)/S ratio is 0.1 to 70, the stretch flange
formability and the fatigue characteristics are improved. If the
(Ce+La)/S ratio becomes less than 0.1, the number ratio of
inclusions of a form of an oxide or oxysulfide of one or both of Ce
or La on which MnS is precipitated is greatly reduced, and, in
accordance with this, the number ratio of MnS-based stretched
inclusions easily becoming starting points of cracking becomes too
large and the stretch flange formability and fatigue
characteristics fall.
[0096] On the other hand, if the (Ce+La)/S ratio exceeds 70, cerium
oxysulfides and lanthanum oxysulfides are formed in large amounts
and form coarse inclusions with a circle equivalent diameter of 50
.mu.m or so or more, so the stretch flange formability and the
fatigue characteristics are degraded.
[0097] Next, the structure of the steel plate will be
explained.
[0098] The present invention improves the stretch flange
formability and fatigue characteristics by control of the MnS-based
inclusions. The microstructure of the steel plate is not
particularly limited. The effect of the present invention is
obtained in any steel plate of steel plate of a structure with
bainitic ferrite as a main phase, composite structure steel plate
having a ferrite phase as a main phase and having a martensite
phase or bainite phase as a second phase, and composite structure
steel plate comprised of ferrite, residual austenite, and a low
temperature transformed phase (martensite or bainite), but to
obtain a superior stretch flange formability, making the structure
one having bainitic ferrite as its main phase is preferred.
Preferably the bainitic ferrite or bainite phase is the largest
phase in terms of area ratio. The area rate of the bainitic ferrite
phase is preferably 50% or more, more preferably 80% or more, still
more preferably 100%. Further, the balance may be made a bainite
phase or polygonal ferrite phase contained in an amount of 20% or
more.
[0099] Next, the production conditions will be explained. In the
present invention, the molten steel is blow refined in a converter
to decarburize it and is further decarburized by using a vacuum
degassing apparatus to make the C concentration 0.03 to 0.1%. Si,
Mn, P, and other alloys are added to this molten steel for
deoxidation and adjustment of the ingredients. Along with this
either Al and Ti are not added or, when adjustment of the oxygen is
necessary, a small amount of Al or Ti of an extent whereby a small
amount of acid soluble Al or acid soluble Ti remains is added, then
one or both of Ce or La is added to adjust the composition. The
thus produced molten steel is continuously cast to produce a cast
slab.
[0100] Regarding the continuous casting, not only may the invention
be applied to continuous casting of slabs of an extent of the
usually 250 mm thickness, but it may also be sufficiently applied
to continuous casting of blooms or billets or of thin slabs
produced by slab continuous casting machine with thicknesses of the
casting molds thinner than usual, for example, 150 mm or less.
[0101] The hot rolling conditions for producing high strength hot
rolled steel plate will be explained next. The heating temperature
of the slabs before hot rolling is preferably 1150.degree. C. or
more for making the carbonitrides etc. in the steel enter solid
solution. By making these enter solid solution, the formation of
polygonal ferrite is suppressed in the cooling process after
rolling and a structure mainly comprised of a bainitic ferrite
phase preferable for the stretch flange formability is obtained. On
the other hand, if the heating temperature of the slab before hot
rolling exceeds 1250.degree. C., the oxidation of the slab surface
becomes remarkable. In particular, the grain boundaries are
selectively oxidized. Due to this, wedge-shaped surface defects
remain after descaling. This detracts from the surface quality
after rolling, so the upper limit is preferably made 1250.degree.
C.
[0102] After heating to the above temperature range, the usual hot
rolling is performed, but during this process, the finish rolling
end temperature is important when controlling the structure of the
steel plate. When the finish rolling end temperature is less than
the Ar.sub.3 point+30.degree. C., the crystal grains at the surface
layer easily become coarser. This is not preferable for the fatigue
characteristics. On the other hand, if over the Ar.sub.3
point+200.degree. C., a polygonal ferrite phase not preferable for
the stretch flange formability is easily formed, so the upper limit
is preferably made the Ar.sub.3 point+200.degree. C.
[0103] Further, making the average cooling rate of the steel plate
after finish rolling 40.degree. C./s or more and cooling in the
range up to 300 to 500.degree. C. is effective for suppressing the
formation of the polygonal ferrite phase and obtaining a structure
mainly comprised of a bainitic ferrite phase.
[0104] If the average cooling rate is less than 40.degree. C./s,
polygonal ferrite phase forms more easily, so this is not
preferred. On the other hand, for control of the structure, it is
not necessary to provide an upper limit for the cooling rate, but
too fast a cooling rate is liable to make the cooling of the steel
plate uneven. Further, construction of a facility enabling such
cooling requires tremendous costs. This is believed to invite a
rise in the price of steel plate. From such a viewpoint, the upper
limit of the cooling rate is preferably made 100.degree. C./s.
[0105] Further, if the cooling stop temperature becomes lower than
300.degree. C., a martensite phase not preferable for stretch
flange formability is formed, so the lower limit was made
300.degree. C. Therefore, the coiling temperature of the hot rolled
coil is preferably made 300.degree. C. or more for suppressing the
formation of a martensite phase causing extreme deterioration of
the stretch flange formability.
[0106] On the other hand, if over 500.degree. C., formation of a
polygonal ferrite phase cannot be suppressed. Further, in steel
containing Cu, Cu is liable to locally precipitate in the ferrite
phase and lower the effect of improvement of the fatigue
characteristics, so the coiling temperature is preferably made
500.degree. C. or less. Therefore, by coiling at 500.degree. C. or
less, carbonitrides are precipitated in the subsequent cooling
process so reduce the amounts of solid solution C and N in the
ferrite phase and cause an improvement in the stretch flange
formability.
EXAMPLES
[0107] Below, examples of the present invention will be explained
along with comparative examples.
[0108] Slabs having the chemical ingredients shown in Table 1 were
hot rolled under the conditions shown in Table 2 to obtain hot
rolled plates of a thickness of 3.2 mm.
TABLE-US-00001 TABLE 1 Acid Acid Steel sol. sol. No. C Si Mn P S N
Al Ti Cr Inv. Ex. 1 1 0.07 0.20 1.3 0.015 0.0050 0.0025 0.006 Comp.
Ex. 1 2 0.07 0.19 1.3 0.015 0.0050 0.0026 0.035 Inv. Ex. 2 3 0.065
0.18 1.5 0.012 0.0100 0.0022 0.004 0.005 Comp. Ex. 2 4 0.065 0.18
1.5 0.012 0.0100 0.0023 0.040 0.005 Inv. Ex. 3 5 0.095 1.00 2.8
0.010 0.0080 0.0030 0.002 0.002 Comp. Ex. 3 6 0.095 1.00 2.8 0.009
0.0080 0.0028 0.038 0.002 Inv. Ex. 4 7 0.035 1.00 1.4 0.010 0.0200
0.0020 0.003 Comp. Ex. 4 8 0.035 1.00 1.39 0.010 0.0200 0.0021
0.003 Inv. Ex. 5 9 0.06 0.68 1.38 0.010 0.0040 0.0020 0.003 0.002
Comp. Ex. 5 10 0.06 0.69 1.38 0.010 0.0040 0.0021 0.003 0.002 Inv.
Ex. 6 11 0.06 0.68 1.38 0.010 0.0007 0.0020 0.003 0.002 Comp. Ex. 6
12 0.06 0.69 1.38 0.010 0.0007 0.0021 0.003 0.002 Inv. Ex. 7 13 0.1
0.25 2 0.010 0.0030 0.0020 0.003 0.002 0.03 Comp. Ex. 7 14 0.1 0.25
2 0.010 0.0030 0.0021 0.003 0.002 0.03 Nb V Mo B Cu Ni Ce La (Ce +
La)/S Inv. Ex. 1 0.0010 0.2 Comp. Ex. 1 Inv. Ex. 2 0.02 0.1 0.05
0.0050 0.0030 0.8 Comp. Ex. 2 0.02 0.1 0.05 Inv. Ex. 3 0.0200 2.5
Comp. Ex. 3 Inv. Ex. 4 0.10 0.0250 1.25 Comp. Ex. 4 0.10 0.0003
0.0015 Inv. Ex. 5 0.0070 1.75 Comp. Ex. 5 0.0003 0.075 Inv. Ex. 6
0.0050 7.143 Comp. Ex. 6 Inv. Ex. 7 0.03 0.02 0.15 0.002 0.0050
0.0030 2.667 Comp. Ex. 7 0.03 0.02 0.15 0.002 0.0002 0.067
TABLE-US-00002 TABLE 2 Finish Cooling rate Heating rolling end
after finish Coiling Condi- temperature temperature rolling
temperature tions (.degree. C.) (.degree. C.) (.degree. C./s)
(.degree. C.) A 1250 845 75 450 B 1200 825 45 450
[0109] In this Table 1, Steel Numbers (hereinafter referred to as
"Steel Nos.") 1, 3, 5, 7, 9, 11, and 13 are made compositions in
the range of high strength steel plate according to the present
invention, while Steel Nos. 2, 4, 6, 8, 10, 12, and 14 are made
comparative steels outside the range of high strength steel plate
according to the present invention. Steel Nos. 2, 4, and 6 were
made slabs containing acid soluble Al in over 0.01%, while Steel
Nos. 8, 10, 12, and 14 were made slabs with the total of one or
both of Ce or La reduced to less than 0.0005.
[0110] In this regard, in Table 1, to enable the Steel No. 1 and
the Steel No. 2, the Steel No. 3 and the Steel No. 4, the Steel No.
5 and the Steel No. 6, and the Steel No. 7 and the Steel No. 8 to
be compared, they were made substantially the same in composition
and made different in acid soluble Al etc. Further, to enable the
Steel No. 9 and Steel No. 10, the Steel No. 11 and Steel No. 12,
and the Steel No. 13 and Steel No. 14 to be compared, they were
made substantially the same in composition and made different in
Ce+La etc.
[0111] Further, in this Table 2, the Conditions A were made a
heating temperature of 1250.degree. C., a finish rolling end
temperature of 845.degree. C., a cooling rate after finish rolling
of 75.degree. C./s, and a coiling temperature of 450.degree. C.,
while the Conditions B were made a heating temperature of
1200.degree. C., a finish rolling end temperature of 825.degree.
C., a cooling rate after finish rolling of 45.degree. C./s, and a
coiling temperature of 450.degree. C.
[0112] For the Steel No. 1 and the Steel No. 2, the Conditions A
were applied, further for the Steel No. 3 and the Steel No. 4, the
Conditions B were applied, for the Steel No. 5 and the Steel No. 6,
the Conditions A were applied, and for the Steel No. 7 and the
Steel No. 8, the Steel No. 9 and the Steel No. 10, the Steel No. 11
and the Steel No. 12, and the Steel No. 13 and the Steel No. 14,
the Conditions B were applied to enable the effects of the chemical
compositions to be compared under the same production
conditions.
[0113] As basic characteristics of the steel plates obtained in
this way, the inventors investigated the strength, ductility,
stretch flange formability, and fatigue strength ratio.
[0114] Further, as the state of presence of stretched inclusions in
the steel plate, the inventors investigated the number ratio,
volume number density, and average circle equivalent diameter of
inclusions having a stretch ratio of 5 or more for all inclusions
of 1 .mu.m or more.
[0115] Furthermore, as the state of presence of unstretched
inclusions in the steel plate, the inventors investigated the
number ratio and volume number density of inclusions comprised of
an oxide or oxysulfide of one or both of Ce or La on which MnS has
precipitated for all inclusions of 1 .mu.m or more and the average
value of contents of the total of one or both of Ce or La in the
inclusions with a stretch ratio of 3 or less.
[0116] Note that inclusions of 1 .mu.m or more were covered because
of the ease of observation and, in addition, the fact that
inclusions of less than 1 .mu.m do not have any effect on
deterioration of the stretch flange formability and fatigue
characteristics.
[0117] The results are shown in Table 3 for each combination of
steel and rolling conditions.
TABLE-US-00003 TABLE 3 Average circle Average content equivalent of
total of one diameter in or both of Ce or inclusions with La in
inclusions circle with circle equivalent equivalent diameter 1
.mu.m or Ce + Ce + MnS Stretched diameter 1 .mu.m or more and MnS
Stretched volume volume more and stretch stretch ratio 5 Hole
Fatigue number number number number ratio 3 or less or more
expansion strength Condition Strength Ductility ratio ratio density
density (%) (.mu.m) value ratio A 460 23 90 0 2.5 .times. 10.sup.4
0 2 6 160 0.67 A 458 20 0 75 0 2.8 .times. 10.sup.4 0 12 110 0.48 B
497 22 80 5 6.1 .times. 10.sup.4 4.1 .times. 10.sup.3 10 7 162 0.6
B 495 19 0 85 0 7.0 .times. 10.sup.4 0 22 105 0.46 A 1150 11 85 0
2.8 .times. 10.sup.4 0 30 5 80 0.64 A 1140 8 0 80 0 4.7 .times.
10.sup.4 0 18 45 0.45 B 810 22 87 7 9.6 .times. 10.sup.4 7.2
.times. 10.sup.3 33 9 100 0.61 B 805 20 1 97 9.6 .times. 10.sup.2
9.3 .times. 10.sup.4 0.4 24 62 0.44 B 605 25 83 6 8.8 .times.
10.sup.4 6.1 .times. 10.sup.3 29 8 90 0.68 B 605 25 1 95 8.4
.times. 10.sup.2 9.3 .times. 10.sup.4 0.4 23 38 0.49 B 605 25 87 0
9.5 .times. 10.sup.4 0 50 5 100 0.68 B 605 25 0 97 0 9.4 .times.
10.sup.4 0 23 34 0.49 B 1005 17 86 5 9.7 .times. 10.sup.4 5.9
.times. 10.sup.3 34 7 75 0.63 B 995 16 1 96 8.2 .times. 10.sup.2
9.4 .times. 10.sup.4 0.3 24 30 0.44
[0118] The strength and ductility were found by a tensile test of a
JIS No. 5 test piece taken in parallel with the rolling direction.
The stretch flange formability was evaluated by pushing open a
punched hole of a diameter of 10 mm made at the center of a 150
mm.times.150 mm steel plate by a 60.degree. conical punch,
measuring the hole diameter D (mm) when a crack occurs passing
through the plate thickness, and finding the hole expansion value
.lamda.=(D-10)/10. Further, the fatigue strength ratio used as an
indicator showing the fatigue characteristics was evaluated by the
value of the fatigue strength at 2.times.10.sup.6 cycles (.sigma.W)
found by the method based on JIS Z 2275 divided by the strength
(.sigma.B) of the steel plate (.sigma.W/.sigma.B).
[0119] Note that the test piece used was a No. 1 test piece defined
in the specification having a parallel part of 25 mm, a radius of
curvature R of 100 mm, and a thickness after equally grinding the
two surfaces of the original plate (hot rolled plate) of 3.0
mm.
[0120] Furthermore, the inclusions were observed under a SEM. Fifty
randomly selected inclusions with a circle equivalent diameter of 1
.mu.m or more were measured for their long axes and short axes.
Furthermore, the quantitative analysis function of an SEM was used
to analyze the composition of 50 randomly selected inclusions with
a circle equivalent diameter of 1 .mu.m or more. Using these
results, the number ratio of inclusions with a stretch ratio of 5
or more, the average circle equivalent diameter of inclusions with
a stretch ratio of 5 or more, the number ratio of inclusions
comprised of an oxide or oxysulfide of one or both of Ce or La on
which MnS has precipitated, and furthermore an average value of the
total of one or both of Ce or La in the inclusions with a stretch
ratio of 3 or less were found. Further, the volume number density
by type of inclusions was calculated by evaluation of the
electrolyzed surface by SEM evaluation by the speed method.
[0121] As clear from Table 3, in Steel Nos. 1, 3, 5, 7, 9, 11, and
13 applying the method of the present invention, by making MnS
precipitate at an oxide or oxysulfide of one or both of Ce or La,
it was possible to reduce the stretched MnS-based inclusions in the
steel plate. That is, by making the number ratio of inclusions
comprised of an oxide or oxysulfide of one or both of Ce or La on
which MnS is precipitated in the steel plate 10% or more, making
the volume number density of the inclusions
1.0.times.10.sup.3/mm.sup.3 or more, and making the average content
of the total of one or both of Ce or La in the inclusions with a
stretch ratio of 3 or less present in the steel plate 0.5% to 50%,
it was possible to make the number ratio of the stretched
inclusions with a circle equivalent diameter 1 .mu.m or more and
with a stretch ratio of 5 or more 20% or less, make the volume
number density of the inclusions 1.0.times.10.sup.4/mm.sup.3 or
less, and make the average circle equivalent diameter of the
inclusions 10 .mu.m or less. As a result, compared with the
comparative steels, in the invention steels of Steel Nos. 1, 3, 5,
7, 9, 11, and 13, steel plate superior in stretch flange
formability and fatigue characteristics could be obtained. However,
in the comparative steels (Steel Nos. 2, 4, 6, 8, 10, 12, and 14),
the state of distribution of the stretched MnS-based inclusions and
inclusions comprised of an oxide or oxysulfide of one or both of Ce
or La at which MnS has been precipitated differs from the state of
distribution prescribed in the present invention, so at the time of
working the steel plate, the stretched MnS-based inclusions formed
starting points of cracking and the stretch flange formability and
the fatigue characteristics dropped.
INDUSTRIAL APPLICABILITY
[0122] According to the method of the present invention, by making
fine MnS precipitate in the slab and making them disperse in the
steel plate as fine spherical inclusions not being deformed at the
time of rolling and not easily forming starting points of cracking,
high strength hot rolled steel plate superior in stretch flange
formability and fatigue characteristics can be obtained.
* * * * *