U.S. patent application number 11/637273 was filed with the patent office on 2008-05-01 for high-strength steel sheets with excellent formability and method for manufacturing the same.
This patent application is currently assigned to Hyundai Motor Company. Invention is credited to Chel Min Park.
Application Number | 20080099109 11/637273 |
Document ID | / |
Family ID | 39265014 |
Filed Date | 2008-05-01 |
United States Patent
Application |
20080099109 |
Kind Code |
A1 |
Park; Chel Min |
May 1, 2008 |
High-strength steel sheets with excellent formability and method
for manufacturing the same
Abstract
Disclosed is a high-strength ferrite-martensite steel sheet with
excellent formability comprising: 0.05-0.15 weight % of C; 0.15
weight % or less of Si; 0.5-2.7 weight % of Mn; 0.1-0.7 weight % of
Al; 0.005-0.03 weight % of P; 0.01-0.3 weight % of Sb; 0.002-0.02
weight % of S; at least one element selected from the group
consisting of 0.01-0.6 weight % of Mo and 0.0005-0.0035 weight % of
B; and the balance Fe and incidental impurities.
Inventors: |
Park; Chel Min;
(Gyeonggi-do, KR) |
Correspondence
Address: |
EDWARDS ANGELL PALMER & DODGE LLP
P.O. BOX 55874
BOSTON
MA
02205
US
|
Assignee: |
Hyundai Motor Company
Seoul
KR
|
Family ID: |
39265014 |
Appl. No.: |
11/637273 |
Filed: |
December 11, 2006 |
Current U.S.
Class: |
148/649 ;
420/8 |
Current CPC
Class: |
C21D 2211/008 20130101;
C21D 2211/005 20130101; C22C 38/04 20130101; C22C 38/12 20130101;
C21D 9/48 20130101; C21D 8/0473 20130101; C22C 38/02 20130101; C22C
38/60 20130101; C22C 38/06 20130101 |
Class at
Publication: |
148/649 ;
420/8 |
International
Class: |
C22C 38/00 20060101
C22C038/00; C21D 8/00 20060101 C21D008/00 |
Foreign Application Data
Date |
Code |
Application Number |
Oct 31, 2006 |
KR |
10-2006-0106092 |
Claims
1. A high-strength ferrite-martensite steel sheet with excellent
formability and superior contraction property, comprising:
0.05-0.15 weight % of C; 0.15 weight % or less of Si; 0.5-2.7
weight % of Mn; 0.1-0.7 weight % of Al; 0.005-0.03 weight % of P;
0.01-0.3 weight % of Sb; 0.002-0.02 weight % of S; at least one
element selected from the group consisting of 0.01-0.6 weight % of
Mo and 0.0005-0.0035 weight % of B; and the balance Fe and
incidental impurities.
2. The high-strength steel sheet as recited in claim 1 further
comprising: 0.15 weight % or less of at least one element selected
from the group consisting of Ti, Nb and V in accordance with a
target tensile strength.
3. The high-strength steel sheet as recited in claim 1, wherein
.gamma.-Fiber orientation ((111)H/RD orientation) of the ferrite
matrix is 0.35 volume % or more and cube orientation
((100)<001>) of the ferrite matrix is 0.2 volume % or
less.
4. A method for manufacturing a high-strength steel sheet with
excellent formability and superior contraction property comprising
the steps of: providing a slab comprising: 0.05-0.15 weight % of C;
0.15 weight % or less of Si; 0.5-2.7 weight % of Mn; 0.1-0.7 weight
% of Al; 0.005-0.03 weight % of P; 0.01-0.3 weight % of Sb;
0.002-0.02 weight % of S; at least one element selected from the
group consisting of 0.01-0.6 weight % of Mo and 0.0005-0.0035
weight % of B; and the balance Fe and incidental impurities,
reheating the slab at 1,050-1,250.degree. C.; hot rolling the slab
to adjust a reduction ratio at the last stand to be 10% or less;
winding the hot rolled steel sheet at 600-750.degree. C. and then
cold rolling the wound steel sheet; and recrystallization-annealing
the cold rolled steel sheet and then quenching the
recrystallization-annealed steel sheet.
5. The method as recited in claim 4, wherein the recrystallization
annealing is performed at 750-850.degree. C. for 30-180 seconds and
the quenching is carried out at a rate of 15-2,000.degree.
C./s.
6. The method as recited in claim 4, wherein 0.15 weight % or less
of at least one element selected from the group consisting of Ti,
Nb and V in accordance with a target tensile strength is added to
provide a slap.
7. A method for manufacturing a high-strength steel sheet of a dual
phase structure that has excellent formability and superior
contraction property even with one cycle of cold rolling and
annealing process, comprising the step of adding an effective
amount of Sb so as to suppress the development of cube orientation
and rotated cube orientation ((100)<011>) and increase the
development of (111)//RD orientation.
8. The method as recited in claim 7, wherein the amount of Sb is
0.3 weight % or less.
9. The method as recited in claim 8, wherein the amount of the
amount of Sb is 0.01-0.3 weight %.
10. A motor vehicle comprising the steel sheet of claim 1.
Description
CROSS-REFERENCE TO RELATED APPLICATION
[0001] This application claims the benefit of Korean Patent
Application No. 10-2006-0106092 filed with the Korean Intellectual
Property Office on Oct. 31, 2006, the entire disclosure of which is
hereby incorporated by reference.
BACKGROUND OF THE INVENTION
[0002] 1. Field of the Invention
[0003] The present invention relates to a high-strength steel sheet
and a method for manufacturing the same, and more particularly, to
high-strength steel sheets with excellent formability and
galvanizability, which can be used as a steel material for an
automotive application and a method for manufacturing the same.
[0004] 2. Background
[0005] Numerous researchers in the automotive industries have
intensively studied to reduce automotive body weight to meet the
standards required by environmental regulations and to cope with
resource exhaustion problems.
[0006] For example, great efforts have been made to provide
high-strength steel sheets to suppress exhaust gas and improve fuel
efficiency as well as to reduce automotive body weight.
[0007] While higher strength steel materials are preferred for the
purpose of vehicle users safety, they have a lower formability. For
the products with complicated form, the formability is much
lowered.
[0008] This can be readily inferred from the fact that the higher
the strength of the steel sheet is, the more the yield stress is
increased and the more the drawing formability represented by
r-value falls sharply.
[0009] To overcome such problems, various attempts have been made
to achieve both high-strength and high ductility of these steel
materials. For example, numerous studies have provided multiphase
steels with high-strength and high ductility, including TRIP steel
using a transformation induced plasticity phenomenon, dual phase
(DP) steel with martensite-ferrite matrix, and TWIP steel using a
twin phenomenon.
[0010] Among them, the DP steel has been considered as a preferred
material in terms of the press formability. Especially, the DP
steel fabricated through continuous annealing followed by gas jet
cooling line (GCL) shows low yield stress, high ductility and
excellent bake hardening (BH).
[0011] However, while the DP steels have good formability, they
have the drawback that their r-values are relatively low, meaning
that their deep drawing properties are not excellent.
[0012] Currently, high strength steels are required to have both
high ductility and superior contraction (i.e., high r-value). This
is true even for high-strength steel sheets having a tensile
strength of 440 MPa, 490 Mpa, 590 Mpa or more.
[0013] Various attempts have been made to increase the r-values of
DP steels and improve the contraction property. For example,
Japanese Patent Publication Nos. 1991-097812, 1991-097813 and
1993-209228 disclose methods for increasing r-values of cold rolled
steel sheets for deep drawing, which employs two cold rolling
processes and two annealing processes.
[0014] However, the methods disclosed in the above patents are not
suitable for the high-strength cold rolled steel sheets having a
tensile strength of more than 440 Mpa. Moreover, due to the cold
rolling and annealing processes, each of which is required to be
performed twice, the methods also exhibit low productivity and
requires increased material cost. Accordingly, such methods are not
suitable for mass production.
[0015] The information disclosed in this Background of the
Invention section is only for enhancement of understanding of the
background of the invention and should not be taken as an
acknowledgement or any form of suggestion that this information
forms the prior art that is already known to a person skilled in
the art.
SUMMARY OF THE INVENTION
[0016] In one aspect, the present invention provides a
high-strength DP steel sheet that can have excellent formability
and contraction property even with one cycle of cold rolling and
annealing process and can be fabricated through a hot dip
galvanization process. This advantage can be achieved by using
effective amounts of certain elements including Sb.
[0017] In a preferred embodiment, the present invention provides a
high-strength ferrite-martensite steel sheet with excellent
formability and contraction property, comprising: 0.05-0.15 weight
% C; 0.15 weight % or less Si; 0.5-2.7 weight % Mn; 0.1-0.7 weight
% Al; 0.005-0.03 weight % P; 0.01-0.3 weight % Sb; 0.002-0.02
weight % S; at least one element selected from the group consisting
of 0.01-0.6 weight % Mo and 0.0005-0.0035 weight % B; and the
balance Fe and incidental impurities.
[0018] Preferably, such steel sheet may further comprise 0.15
weight % or less of at least one element selected from the group
consisting of Ti, Nb and V in accordance with a target tensile
strength.
[0019] Suitably, .gamma.-Fiber orientation ((111)//RD orientation)
of the ferrite matrix may be 0.35 volume % or more and cube
orientation ((100)<001>) may be 0.2 volume % or less.
[0020] In another aspect, the present invention provides a method
for manufacturing a high-strength steel sheet of a dual phase
structure that has excellent formability and contraction property
even with one cycle of cold rolling and annealing process,
comprising the step of adding effective amount of Sb so as to
suppress the development of cube orientation and rotated cube
orientation ((100)<011>) and increase the development of
(111)//RD orientation.
[0021] In such a method, the amount of Sb is preferably 0.3 weight
% or less, and more preferably, 0.01-0.3 weight %.
[0022] In still another aspect, the present invention provides a
method for manufacturing a high-strength steel sheet with excellent
formability and superior contraction property, comprising the steps
of: (a) providing a slab comprising: 0.05-0.15 weight % C; 0.15
weight % or less Si; 0.5-2.7 weight % Mn; 0.1-0.7 weight % Al;
0.005-0.03 weight % P; 0.01-0.3 weight % Sb; 0.002-0.02 weight % S;
at least one element selected from the group consisting of 0.01-0.6
weight % Mo and 0.0005-0.0035 weight % B; and the balance Fe and
incidental impurities; (b) reheating the slab at
1,050-1,250.degree. C.; (c) hot rolling the slab to adjust a
reduction ratio at the last (final) stand to be 10% or less; (d)
winding the hot rolled steel sheet at 600-750.degree. C. and then
cold rolling the wound steel sheet; and (e)
recrystallization-annealing the cold rolled steel sheet and then
quenching the recrystallization-annealed steel sheet.
[0023] Preferably, recrystallization annealing may be performed at
750-850.degree. C. for 30-180 seconds. Also preferably, quenching
may be carried out at a rate of 15-2,000.degree. C./s.
[0024] Suitably, 0.15 weight % or less of at least one element
selected from the group consisting of Ti, Nb and V in accordance
with a target tensile strength may be added to provide a slap.
[0025] In a further aspect, motor vehicles are provided that
comprise a described high-strength steel sheet.
[0026] It is understood that the term "vehicle" or "vehicular" or
other similar term as used herein is inclusive of motor vehicles in
general such as passenger automobiles including sports utility
vehicles (SUV), buses, trucks, various commercial vehicles,
watercraft including a variety of boats and ships, aircraft, and
the like. The present high-strength steel sheets will be
particularly useful with a wide variety of motor vehicles.
[0027] Other aspects of the invention are discussed infra.
BRIEF DESCRIPTION OF THE DRAWINGS
[0028] The present invention will be described with reference to
certain exemplary embodiments thereof illustrated in the attached
drawings in which:
[0029] FIG. 1 is a graph showing volume fractions of .gamma.-Fiber
orientation in accordance with added amount of antimony in Examples
and Comparative Examples;
[0030] FIG. 2 is a graph showing volume fractions of cube
orientation in accordance with added amount of antimony in Examples
and Comparative Examples; and
[0031] FIG. 3 is a graph showing r-values in accordance with added
amount of antimony in Examples and Comparative Examples.
DETAILED DESCRIPTION
[0032] Hereinafter, preferred embodiments of the present invention
will now be described in detail with reference to the attached
drawings.
[0033] As discussed above, in one aspect, the present invention
provides a high-strength DP steel sheet that has excellent
formability and contraction property.
[0034] A preferred example of the steel sheet of the present
invention is a high-strength ferrite-martensite steel sheet with
excellent formability and superior contraction property, which
comprises: 0.05-0.15 weight % C; 0.15 weight % or less Si; 0.5-2.7
weight % Mn; 0.1-0.7 weight % Al; 0.005-0.03 weight % P; 0.01-0.3
weight % Sb; 0.002-0.02 weight % S; at least one element selected
from the group consisting of 0.01-0.6 weight % Mo and 0.0005-0.0035
weight % B; and the balance Fe and incidental impurities. Such
steel sheet is composed of a dual phase structure of ferrite and
martensite.
[0035] The inventor of the present invention has examined the
development of microstructure, recrystallization and development of
phase transformation according to the kinds of alloying elements in
cold rolled steel sheets and the conditions of manufacturing
process in order to solve the problems associated with the
conventional art. While conducting such researches, the present
inventor confirmed that the development of .gamma.-Fiber
orientation ((111//RD) that has a direct effect on the r-value is
influenced primarily by the amount of solid solution carbon C among
the alloying components.
[0036] A certain amount of carbon (C) is required for formation of
the martensite necessary for obtaining a target tensile strength.
Accordingly, the amount of solid solution carbon can be reduced
with the generation of carbides by utilizing titanium (Ti),
vanadium (V), niobium (Nb), etc. against the solid solution carbons
not necessary for formation of such martensite.
[0037] It is possible to develop recrystallization texture of final
product obtained after recrystallization-annealing process be a
method known in the art. However, the method still has limitations
in controlling the texture due to the reduction of the solid
solution carbon amount.
[0038] Accordingly, in order to overcome these restrictive
limitations, the present inventor has conducted researches on an
optimum design of alloying components and a control of texture with
the addition of components, which requires no additional
process.
[0039] Through his intensive studies, the present inventor has
discovered that a high r-value can be obtained when 0.3 weight % or
less of antimony (Sb) is used. This limited amount of Sb can
suppress the developments of .alpha.-Fiber orientation ((110)H/RD)
and cube orientation ((100)<001>) and increase the
development of (111)//RD orientation.
[0040] Moreover, it has been well known that, when antimony (Sb) is
added to the steel material in which 10 ppm or less of sulfur (S)
exists as an impurity, the cube orientation develops, thereby
improving physical properties of the steel sheet.
[0041] Based on these facts, the present inventor has discovered
that the developments of cube orientation and rotated cube
orientation ((100)<011>) can be suppressed and the
development of (111)//RD orientation can increase, if 10 ppm or
more of sulfur (S) and 0.3 weight % or less of antimony (Sb) are
contained in the steel material.
[0042] Based on this principle, in another aspect, the present
invention provides a method for manufacturing a high-strength steel
sheet of a dual phase structure that has excellent formability and
superior contraction property even with one cycle of cold rolling
and annealing process, comprising the step of adding effective
amount of Sb so as to suppress the development of cube orientation
and rotated cube orientation ((100)<011>) and increase the
development of (111)//RD orientation.
[0043] In a preferred embodiment, accordingly, the amount of S may
be 10 ppm or more and the amount of Sb may be 0.3 weight % or less.
More preferably, the amount of S may be 0.002-0.02 weight % and the
amount of Sb may be 0.01-0.3 weight %.
[0044] In particular, a slab comprising the alloying elements as
described above is subjected to a hot rolling process having a
reduction ratio in the final stand of a hot strip finishing mill
adjusted to of 10% or less. The hot rolled sheet is subjected to a
box annealing process at 600-750.degree. C. The resulting annealed
sheet is then subjected to a winding process.
[0045] The thus-obtained hot rolled steel sheet is subjected to a
pickling process and a cold rolling process of 65-75%.
Subsequently, the cold rolled steel sheet is subjected to a
degreasing process, a recrystallization annealing at
750-850.degree. C. for 30-180 seconds and a quenching process at a
rate of 15-2,000.degree. C./s based on the characteristics of the
quenching line.
[0046] The basic phase of the DP cold rolled steel sheet prepared
in the above-described method is composed of ferrite matrix, and
bainite and martensite structures co-exist in a ratio over a
certain level in accordance with a target tensile strength and a
cooling rate of the annealing line.
[0047] In a more preferred embodiment, a high-strength steel sheet
cab be fabricated in the following manner. A slab comprising:
0.05-0.15 weight % C; 0.15 weight % or less Si; 0.5-2.7 weight %
Mn; 0.1-0.7 weight % Al; 0.005-0.03 weight % P; 0.01-0.3 weight %
Sb; 0.002-0.02 weight % S; at least one element selected from the
group consisting of 0.01-0.6 weight % Mo, 0.0005-0.0035 weight % B;
and, optionally, 0.15 weight % Ti, Nb or V; and the balance Fe and
incidental impurities is subjected to a reheating process at
1,050-1,250.degree. C. and a hot rolling process at a reduction
ratio of 10% or less in the last stand of the hot strip finishing
mill in consideration of the strip flatness and crown control. The
hot rolled steel sheet is wound up at 600-750.degree. C. The
resultant hot rolled steel sheet is subjected to a cold rolling
process at a reduction ratio of 65-75% in thickness of 1.4 mm. The
cold rolled steel sheet is subjected to a recrystallization
annealing process at 750-850.degree. C. for 30-180 seconds.
Finally, the recrystallization annealed steel sheet is quenched at
a rate of 15-2,000.degree. C./s.
[0048] In the reheating process of the slab, heating at less than
1,050.degree. C. can increase the roll force caused by the rolling
resistance due to the low temperature, deteriorating the hot
rolling workability by By contrast, heating at more than
1,250.degree. C. can make it difficult to control the
microstructures, volume fractions and texture controls of the end
product due to micro-precipitations contained in quantities by the
increased recreation of solid solution.
[0049] The hot rolling process includes a front rolling method in
that the front stand of the hot strip finishing mill executes the
rolling process and a rear rolling method in that the rear stand of
the hot strip finishing mill executes the rolling process, and both
methods affect the development of the texture of the end
product.
[0050] In both rolling methods, the reduction ratio in the last
(final) stand commonly influences the strip flatness of hot rolled
steel sheets, which has a close relation with the productivity.
Accordingly, the reduction ratio in the last hot rolling step is
limited to 10% or less.
[0051] Furthermore, as described above, the hot rolled steel sheet
is wound up (coiled) at 600-750.degree. C. A temperature below
600.degree. C. can cause a problem in that the transformation
structure generated during the hot rolling process is not
completely recrystallized. In contrast, a temperature over
750.degree. C. can cause a problem in pickling due to an oxide film
of a dense structure formed on the surface of hot rolled steel
sheet.
[0052] In addition, it is desirable that the recrystallization
annealing process be carried out at 750-850.degree. C., since it is
difficult to control the ratio of martensite phase required for a
certain level of tensile strength, if the recrystallization
annealing process is performed outside the above range.
[0053] Moreover, it is desirable that the annealing time be limited
to 30-180 seconds. An annealing for less than 30 seconds can
prohibit the cold rolled structure from being completely annealed
and can affect the phase transformation temperature. On the other
hand, annealing for more than 180 seconds can reduce overall
productivity although it may reach an ideal temperature.
[0054] Furthermore, the cooling process is carried out at a rate of
15-2,000.degree. C./s after the recrystallization annealing
process. A cooling rate lower than the above range can make it
difficult to ensure the driving energy required for the martensite
transformation. By contrast, a cooling rate higher than the above
range can make it impossible to achieve a commercially and
practically available result.
[0055] The steel sheet fabricated through the above processes has a
matrix structure composed of ferrite and martensite and has
characteristics in that .gamma.-Fiber orientation ((111//RD) of
ferrite matrix is controlled to 0.35 volume % or more and cube
orientation ((100)<001>) is suppressed to 0.2 volume % or
less.
[0056] Next, the reasons for limiting the content of the respective
alloying elements to a specific range will be described.
[0057] C: 0.05-0.15 Weight %
[0058] Carbon can affect the formability of steel. Excessive amount
of carbon deteriorates the formability.
[0059] Moreover, it moves from the inside of ferrite to the
austenite phase in the temperature range of phase transformation,
thus stabilizing the austenite phase.
[0060] However, since an amount exceeding 0.15 weight % affects the
formation of the dual phase and deteriorates the weldability, it is
desirable that the carbon content be 0.15 weight % or less.
[0061] On the other hand, an amount less than 0.05 weight % cannot
ensure the necessary strength.
[0062] Si: 0.15 Weight % or Less
[0063] Silicon is a ferrite stabilizing element that suppresses the
precipitation of cementite and increases the ferrite fraction to
improve the elongation and increases the strength by strengthening
solid solution.
[0064] Excessive amount of Si causes a defective surface texture
and deteriorate the weldability. It also lowers the paintability
due to the generation of oxides.
[0065] Accordingly, 0.15 weight % or less is preferred.
[0066] Mn: 0.5-2.7 Weight %
[0067] Manganese is an austenite stabilizing element that increases
the strength with the generation of low temperature phase
transformation such as acicular ferrite, bainite or martensite.
[0068] Moreover, despite the phase transformation by the
diffusional transformation, it causes a texture memory phenomenon
to occur by decreasing the ferrite region.
[0069] If the amount added is less than 0.5 weight %, it is
difficult to control the cooling rate for suppressing the formation
of ferrite, whereas, if it is more than 2.7 weight %, it causes the
formation of segmentation on the sheet during the hot rolling
process, the deterioration of weldability and the hydrogen induced
embrittlement.
[0070] Accordingly, it is desirable that the manganese content be
maintained at 0.5-2.7 weight %.
[0071] Al: 0.1-0.7 Weight %
[0072] Aluminum, like silicon, suppresses the precipitation of
cementite to delay the transformation process.
[0073] It increases the ferrite fraction to improve the elongation
and does not deteriorate the chemical conversion coating property
and the hot dip galvanizability; however, it provides a cause of
the embrittlement.
[0074] Moreover, it lowers the actual yield by the solution
strengthening along with silicon added during the cold rolling
process.
[0075] Accordingly, it is desirable that the aluminum content be
limited to the range of 0.1-0.7 weight %.
[0076] P: 0.005-0.03 Weight %
[0077] Phosphorus increases the strength of steel sheet by the
solid strengthening and plays a role of stabilizing the remaining
austenite by the increase of solid solution carbon caused by the
suppression of oxide formation.
[0078] If added excessively, it causes the deterioration of
weldability and local ductility due to the grain boundary
segregation of P, promotes the development of cube orientation and
inhibits the development of (111)//RD orientation.
[0079] Accordingly, it is desirable that the phosphorus content be
limited to the range of 0.005-0.03 weight %.
[0080] Sb: 0.01-0.3 Weight %
[0081] Antimony promotes the formation of (111)//RD orientation
that is an advantageous textile for r-value and inhibits the
formation of cube orientations and rotated cube orientations. These
effects are increased if silicon (S) is contained in an appropriate
range.
[0082] If added excessively, it affects the steel manufacture and
the hot rolling. Accordingly, it is desirable that the antinomy
content be limited to the range of 0.01-0.3 weight %.
[0083] S: 0.002-0.02 Weight %
[0084] If sulfur is added in an appropriate range, its effect is
increased. However, if added excessively, it forms rough MnS on the
hot rolled steel sheet, which results in cracks. Accordingly, it is
desirable that sulfur content be limited to the range of 0.002-0.02
weight %.
[0085] Mo: 0.01-0.6 Weight %
[0086] Molybdenum, like Mn, is an element that stabilizes the low
temperature phase transformation. If added excessively, it
deteriorates the formability. Accordingly, it is desirable that
molybdenum content be limited to the range of 0.01-0.6 weight
%.
[0087] B: 0.0005-0.0035 Weight %
[0088] Boron, like Mn, is an element that stabilizes the low
temperature phase transformation. Outside the range of
0.0005-0.0003 weight %, the above effect cannot be obtained. In
particular, if added excessively, it has a bad effect on the
plating adhesion. Accordingly, it is desirable that boron content
be limited to the range of 0.0005-0.0035 Weight %.
[0089] Ti, Nb and V: 0.15 Weight % or Less
[0090] Titanium (Ti), niobium (Nb) and vanadium (V) are grain
refining elements. If added excessively, each of them decreases the
overall productivity. Accordingly, it is desirable that their
contents be limited to 0.15 weight % or less.
[0091] Subsequently, the present invention will be described in
more detail with reference to Examples and Comparative Examples.
The following examples are presented to illustrate further various
aspects of the present invention, but are not intended to limit the
scope of the invention in any aspect.
EXAMPLES 1 TO 6 AND COMPARATIVE EXAMPLES 1 TO 3
[0092] Steel slabs having the compositions listed in the following
Table 1 were heated at 1,200.degree. C. and then subjected to hot
rolling, winding (coiling), pickling, cold rolling processes in
turn, thus fabricating steel sheets of 1.0 mm in thickness.
Subsequently, a recrystallization annealing process was carried out
for the steel sheets under the conditions as listed in Table 2.
[0093] The reduction ratio in the last hot rolling step was set at
10%, the coiling temperature was set at 650.degree. C., the
reduction ratio in the cold rolling step was set at 65% and the
cooling rate after the recrystallization annealing process was set
at 20.degree. C./s.
[0094] Tensile strengths, yield strengths and r-values were
measured for the steel sheets fabricated through the
recrystallization annealing process in Examples 1 to 6 and
Comparative Examples 1 to 3. In addition, (111)//RD orientations
and (100)<001>orientations by volume weight were calculated
using an EBSD technique. The data are shown in the following Table
2.
TABLE-US-00001 TABLE 1 Composition (weight %) Class C Si Mn P Al S
Sb Mo B Ti Nb V Example 1 Invented 0.055 0.15 2.1 0.012 0.42 0.003
0.035 0.15 0.002 -- -- -- Steel Example 2 Invented 0.068 0.13 1.69
0.011 0.95 0.0045 0.045 -- 0.002 -- -- -- Steel Example 3 Invented
0.076 0.04 1.90 0.023 1.2 0.008 0.04 0.08 -- -- 0.01 -- Steel
Example 4 Invented 0.08 0.07 2.0 0.057 1.7 0.007 0.06 0.18 -- 0.03
-- -- Steel Example 5 Invented 0.08 0.11 1.34 0.01 1.0 0.005 0.05
0.25 0.002 -- -- -- Steel Example 6 Invented 0.09 0.12 1.56 0.056
0.7 0.003 0.08 0.25 0.002 -- -- -- Steel Comparative Compared 0.03
0.18 1.42 0.041 0.88 0.001 0.055 0.11 0.001 -- 0.01 -- Example 1
Steel Comparative Compared 0.06 0.18 1.69 0.011 0.94 0.0045 -- --
0.002 -- -- -- Example 2 Steel Comparative Compared 0.15 0.1 1.54
0.013 1.16 0.009 0.65 0.9 -- -- 0.01 0.05 Example 3 Steel
TABLE-US-00002 TABLE 2 Tensile Annealing Annealing Strength
Elongation (111)//RD (100)<001> Class Temp (.quadrature.)
Time (s) (MPa) (%) (vol %) (vol %) R-value Example 1 Invented 790
60 586 31 0.45 0.1 1.45 Steel Example 2 Invented 790 60 635 29.4
0.38 0.13 1.33 Steel Example 3 Invented 790 60 623 30 0.375 0.12
1.31 Steel Example 4 Invented 820 60 652 28 0.36 0.16 1.3 Steel
Example 5 Invented 820 60 671 27 0.35 0.16 1.3 Steel Example 6
Invented 820 60 734 26 0.35 0.19 1.28 Steel Comparative Compared
790 60 682 23 0.29 0.23 1.1 Example 1 Steel Comparative Compared
790 60 630 28 0.34 0.22 1.05 Example 2 Steel Comparative Compared
850 60 950 18 0.22 0.3 0.75 Example 3 Steel
[0095] As shown in Table 2, it was possible to manufacture
high-strength steel sheets with high r-values and excellent
formability by adding antimony (Sb) in an optimum amount.
[0096] Moreover, FIGS. 1 and 2 depict volume fractions (volume %)
of (111)//RD orientation and (100)<001>orientation in
accordance with the addition of antimony (Sb), and FIG. 3 depicts
r-values in accordance with the addition of antimony (Sb).
[0097] The steel sheets according to the present invention, as
shown in FIG. 1, showed the (111)//RD orientation as an orientation
distribution of 0.035%. Referring to FIG. 2, the orientation
density was lowered. In contrast, the orientation density is
increased for comparative examples.
[0098] Moreover, referring to FIG. 3, high r-values were obtained
if the added amount of antimony is satisfied with the condition of
the present invention.
[0099] As described above, the present invention can provide a dual
phase high-strength steel sheet for a hop dip galvanization that
has a high revalue and excellent formability and contraction,
manufactured by adding antimony (Sb) in an appropriate range to
alloying components and carrying out hot rolling, coiling, cold
rolling and recrystallization annealing processes under optimum
process conditions.
[0100] Particularly, it is possible to manufacture a dual phase
high-strength steel sheet with high tensile strength with one cycle
of cold rolling and annealing process, thereby increasing
productivity, reducing manufacturing cost and facilitating mass
production.
[0101] The present invention has been described in detail with
reference to preferred embodiments thereof. However, it will be
appreciated by those skilled in the art that changes may be made in
these embodiments without departing from the principles and spirit
of the invention, the scope of which is defined in the appended
claims and their equivalents.
* * * * *