[Technical Field]
[0001] The present invention relates to a technology of manufacturing a steel plate for
pipelines having excellent hydrogen-induced crack resistance for use as materials
for oil pipelines, and more particularly, to a steel plate for pipelines, which does
not suffer from significant reduction in impact toughness and has excellent yield
ratio and hydrogen-induced crack resistance, and a method for manufacturing the same.
[Background Art]
[0002] Recently, with recent trend of oil production from deep sea and cryogenic sites,
oil pipelines are increasing in diameter and thus materials for oil pipelines require
excellent mechanical and chemical properties.
[0003] To fulfill such requirement, there is an increasing need for development of a high
strength/high toughness steel plate for pipelines that have excellent hydrogen-induced
crack resistance. Such a steel plate for pipelines is generally produced through a
rolling process.
[0004] Rolling generally includes slab reheating, hot rolling, cooling, and coiling.
[0005] In slab reheating operation, a half-steel product, that is, a steel slab is reheated.
[0006] In hot rolling operation, the reheated slab is subjected to hot rolling at a predetermined
reduction rate using rolling rolls.
[0007] In cooling operation, the hot-rolled steel plate is cooled.
[0008] In coiling operation, the steel plate is coiled at a predetermined temperature.
[0009] For example, such a steel plate for pipelines is disclosed in Korean Patent Publication
No.
10-2001-0060763A.
[Disclosure]
[Technical Problem]
[0010] An aspect of the present invention is to provide a steel plate for pipelines, which
has a low yield ratio and a tensile strength of 450 MPa or more and exhibits excellent
hydrogen-induced crack resistance to be applied to materials for oil pipelines and
the like.
[0011] Another aspect of the present invention is to provide a method of manufacturing a
steel plate for pipelines having excellent hydrogen-induced crack resistance by controlling
process conditions while optimizing a composition ratio of chromium (Cr) and other
alloy components excluding copper (Cu).
[Technical Solution]
[0012] In accordance with one embodiment of the present invention, a steel plate for pipelines
having excellent hydrogen-induced crack resistance includes: carbon (C): 0.03 - 0.05
wt%, silicon (Si): 0.2 - 0.3 wt%, manganese (Mn): 0.5 - 1.3 wt%, phosphorous (P):
0.010 wt% or less, sulfur (S): 0.005 wt% or less, aluminum (Al): 0.02 - 0.05 wt%,
nickel (Ni): 0.2 - 0.5 wt%, chromium (Cr): 0.2 - 0.3 wt%, niobium (Nb): 0.03 - 0.05
wt%, vanadium (V): 0.02 - 0.05 wt%, titanium (Ti): 0.01 - 0.02 wt%, calcium (Ca):
0.001 - 0.004 wt%, and the balance of iron (Fe) and other unavoidable impurities,
and has a tensile strength of 450 MPa or more.
[0013] In accordance with another embodiment of the present invention, a method of manufacturing
a steel plate for pipelines having excellent hydrogen-induced crack resistance includes:
(A) reheating a steel slab, the steel slab including carbon (C): 0.03 - 0.05 wt%,
silicon (Si): 0.2 - 0.3 wt%, manganese (Mn): 0.5 - 1.3 wt%, phosphorous (P): 0.010
wt% or less, sulfur (S): 0.005 wt% or less, aluminum (Al): 0.02 - 0.05 wt%, nickel
(Ni): 0.2 - 0.5 wt%, chromium (Cr): 0.2 - 0.3 wt%, niobium (Nb): 0.03 - 0.05 wt%,
vanadium (V): 0.02 - 0.05 wt%, titanium (Ti): 0.01 - 0.02 wt%, calcium (Ca): 0.001
- 0.004 wt% and the balance of iron (Fe) and other unavoidable impurities; (B) hot
rolling the reheated steel slab; and (C) cooling the hot-rolled steel plate.
[Advantageous Effects]
[0014] The steel plate for pipelines according to one embodiment contains a suitable amount
of chromium and is free from copper (Cu), which is generally used in manufacture of
steel plates, thereby providing advantages such as insignificant reduction of impact
toughness and excellent hydrogen-induced crack resistance.
[0015] The method of manufacturing a steel plate for pipelines according to another embodiment
provides a steel plate which exhibits excellent hydrogen-induced crack resistance
and allows insignificant reduction in impact toughness even without containing copper
(Cu) by controlling rolling and cooling conditions while optimizing a composition
ratio of the steel plate.
[Description of Drawings]
[0016]
Fig. 1 is a schematic flowchart of a method of manufacturing a steel plate for pipelines
in accordance with one embodiment of the present invention.
Fig. 2 is a graph depicting yield strength and tensile strength of specimens prepared
in inventive examples and comparative examples.
Fig. 3 is a graph depicting impact resistance according to temperature of the specimens
prepared in inventive examples and comparative examples.
Fig. 4 depicts pictures showing occurrence of cracking of specimens prepared in inventive
examples and comparative examples upon HIC testing.
[Best Mode]
[0017] The above and other aspects, features, and advantages of the present invention will
become apparent from the detailed description of the following embodiments in conjunction
with the accompanying drawings. It should be understood that the present invention
is not limited to the following embodiments and may be embodied in different ways,
and that the embodiments are provided for complete disclosure and a thorough understanding
of the present invention by those skilled in the art. The scope of the present invention
is defined only by the claims. Like components will be denoted by like reference numerals
throughout the specification.
[0018] Now, a steel plate for pipelines in accordance with one embodiment of the invention
and a method for manufacturing the same will be described in more detail with reference
to the accompanying drawings.
Steel plate for pipelines having excellent hydrogen-induced crack resistance
[0019] A steel plate for pipelines having excellent hydrogen-induced crack resistance according
to one embodiment includes: carbon (C) : 0.03 - 0.05 wt%, silicon (Si): 0.2 - 0.3
wt%, manganese (Mn): 0.5 - 1.3 wt%, phosphorous (P): 0.010 wt% or less, sulfur (S):
0.005 wt% or less, aluminum (Al): 0.02 - 0.05 wt%, nickel (Ni): 0.2 - 0.5 wt%, chromium
(Cr): 0.2 - 0.3 wt%, niobium (Nb): 0.03 - 0.05 wt%, vanadium (V): 0.02 - 0.05 wt%,
titanium (Ti): 0.01 - 0.02 wt%, calcium (Ca): 0.001 - 0.004 wt%, and the balance of
iron (Fe) and other unavoidable impurities.
[0020] Next, functions and amounts of the respective components of the steel plate for pipelines
having excellent hydrogen-induced crack resistance according to the embodiment will
be described in more detail.
Carbon (C)
[0021] Carbon (C) is an element for improving strength and hardness of steel.
[0022] A higher content of carbon can provide higher strength, but can cause deterioration
in toughness of steel. In addition, processibility of the steel increase with increasing
content of carbon, causing increase in tensile strength and yield point while decreasing
elongation.
[0023] If the carbon content exceeds 0.05 wt% in the steel plate, the steel plate can be
deteriorated in hydrogen-induced crack resistance. On the other hand, if the carbon
content is less than 0.03 wt% in the steel plate, there can be difficulty in securing
strength of the steel plate.
[0024] Thus, advantageously, carbon is present in an amount of 0.03 - 0.05 wt% in the steel
plate according to the present invention.
Silicon (Si)
[0025] Silicon (Si) acts as an effective deoxidization element and reinforces ferrite structure
in steel while improving yield strength.
[0026] Such effects of silicon can be sufficiently exhibited when the silicon content is
0.2 wt% or more. If the silicon content exceeds 0.3 wt% in the steel, toughness of
the steel is deteriorated, reducing formability and causing difficulty in forging
and processing.
[0027] Thus, advantageously, silicon is present in an amount of 0.2 - 0.3 wt% in the steel
plate according to the present invention.
Manganese (Mn)
[0028] Manganese (Mn) serves to improve quenching properties and strength while increasing
plasticity at high temperature to improve casting properties. In particular, manganese
is likely to bind with an unfavorable component, that is, sulfur (S), thereby forming
MnS inclusions.
[0029] If manganese is added in an excessive amount exceeding 1.3 wt%, a steel slab can
suffer from central segregation, which promotes occurrence of hydrogen induced cracking
at a segregated portion of the steel slab. If the manganese content is less than 0.5
wt%, it is difficult to secure strength of the steel.
[0030] Thus, advantageously, manganese is present in an amount of 0.5 - 1.3 wt% in the steel
plate according to the present invention.
Phosphorous (P)
[0031] Phosphorous (P) is an element that is segregated into a grain boundary, reducing
toughness and impact resistance of steel, and causes hydrogen-induced cracking in
the steel.
[0032] Thus, advantageously, the phosphorous content is limited to 0.010 wt% or less in
the steel plate according to the present invention.
Sulfur (S)
[0033] Sulfur (S) is an essential element coupled to manganese (Mn) to form MnS inclusions,
thereby improving steel machinability. However, if sulfur is present in an excessive
amount in the steel, sulfur deteriorates hot processibility of the steel, causes fracture,
and forms coarse inclusions, causing defects upon surface treatment.
[0034] Thus, advantageously, sulfur is present in an amount of 0.005 wt% or less in the
steel plate according to the present invention.
Aluminum (Al)
[0035] Aluminum (Al) is a strong deoxidization element and is coupled to nitrogen for grain
refinement. However, if the aluminum content exceeds 0.05 wt% in the steel, there
can be problems of deterioration in impact toughness and hydrogen-induced crack resistance.
Further, if the aluminum content is less than 0.02 wt%, insufficient deoxidization
can be obtained. Thus, advantageously, aluminum is present in an amount of 0.02~0.05
wt% in the steel plate according to the present invention.
Nickel (Ni)
[0036] In this invention, the content of nickel (Ni) is suitably adjusted to obtain desired
yield strength and a yield ratio of 80% or less even in the absence of copper (Cu).
If the nickel content is less than 0.2 wt%, it is difficult for the steel to have
a yield strength of 450 MPa or more. If the nickel content exceeds 0.5 wt%, the steel
has a yield ratio exceeding 80%. Thus, advantageously, nickel is present in an amount
of 0.2 - 0.5 wt% in the steel plate according to the present invention.
Chromium (Cr)
[0037] According to the present invention, the steel plate includes chromium and is free
from copper (Cu), which is generally used in manufacture of existing steel plates.
Copper can cause deterioration of weldability and surface quality of the steel plate.
Thus, the steel plate of the invention does not contain copper and contains an optimal
amount of chromium.
[0038] Through addition of chromium, it is possible to manufacture a steel plate, which
does not suffer from significant reduction in impact toughness and has a low yield
ratio and excellent hydrogen-induced crack resistance. Here, if the chromium content
exceeds 0.3 wt%, the steel plate can suffer from deterioration in hydrogen-induced
crack resistance. If the chromium content is less than 0.2 wt%, the steel plate cannot
obtain desired strength. Thus, advantageously, chromium is present in an amount of
0.2 - 0.3 wt% in the steel plate according to the present invention.
Niobium (Nb)
[0039] Niobium (Nb) prevents grains of steel from being coarsened at high temperature and
promotes refinement of the grains to improve ductility and toughness of the steel.
[0040] To obtain strength improvement, niobium is desirably added in an amount of 0.03 wt%
or more. Since secondary phases containing niobium can act as sites for initiation
of hydrogen-induced cracking, an upper niobium limit is set to 0.05 wt%.
[0041] Thus, advantageously, niobium is present in an amount of 0.03∼0.05 wt% in the steel
plate according to the present invention.
Vanadium (V)
[0042] Vanadium (V) serves to improve resistance to hydrogen-induced cracking.
[0043] Advantageously, vanadium is present in an amount of 0.02 - 0.05 wt% in steel. If
the vanadium content is less than 0.02 wt%, the effect of vanadium is not sufficiently
exhibited. On the contrary, if the vanadium content exceeds 0.05 wt%, the steel can
suffer from deterioration in toughness and hydrogen-induced crack resistance.
Titanium (Ti)
[0044] Titanium is an element which forms carbide or nitride in steel, and serves to improve
both strength and low temperature toughness through grain refinement.
[0045] Titanium precipitates reduces a diffusion coefficient of hydrogen and increases hydrogen-induced
crack resistance. If the titanium content exceeds 0.02 wt%, the steel can be deteriorated
in hydrogen-induced crack resistance, and if the titanium content is less than 0.01
wit%, it is difficult to obtain desired strength. Thus, advantageously, titanium is
present in an amount of 0.01∼0.02 wt% in the steel plate according to the present
invention.
Calcium (Ca)
[0046] Calcium is an element for spheroidizing MnS inclusions. MnS inclusions have a low
melting point and are elongated upon rolling to act as starting point of hydrogen-induced
cracking. The added calcium reacts with MnS to surround the MnS inclusions, thereby
obstructing elongation of the MnS inclusions.
[0047] For efficient spheroidization of the MnS inclusions, calcium is advantageously present
in an amount of 0.001 wt% or more. On the other hand, if the calcium content is excessive,
an excess of oxide inclusions acting as starting points of hydrogen-induced cracking
can be created. Thus, advantageously, an upper limit of the calcium content is set
to 0.004 wt%.
[0048] Advantageously, the steel plate for pipelines according to the present invention
has a yield ratio (YS)/(TS) of 80% or less.
[0049] In addition, advantageously, the microstructure of the steel plate comprises a composite
structure consisting of acicular ferrite and bainite structures. Here, advantageously,
a composite structure consisting of acicular ferrite and bainite structures occupies
30% or more of the entirety of the microstructure in terms of cross-sectional area
ratio, and a composite structure consisting of ferrite and pearlite structures occupies
70% or less of the entirety of the microstructure in terms of cross-sectional area
ratio.
[0050] If the composite structure consisting of acicular ferrite and bainite structures
occupies 30% or less of the entirety of the microstructure in terms of cross-sectional
area ratio, it is difficult to achieved desired strength.
Method of manufacturing a steel plate for pipelines having excellent hydrogen-induced
crack resistance
[0051] Fig. 1 is a schematic flowchart of a method of manufacturing a steel plate for pipelines
in accordance with one embodiment of the present invention.
[0052] Referring to Fig. 1, the method of manufacturing the steel plate for pipelines includes:
(A) reheating a steel slab, the steel slab including carbon (C) : 0.03 ∼ 0.05 wt%,
silicon (Si): 0.2 - 0.3 wt%, manganese (Mn): 0.5 - 1.3 wt%, phosphorous (P): 0.010
wt% or less, sulfur (S): 0.005 wt% or less, aluminum (Al): 0.02 - 0.05 wt%, nickel
(Ni): 0.2 - 0.5 wt%, chromium (Cr): 0.2 - 0.3 wt%, niobium (Nb): 0.03 - 0.05 wt%,
vanadium (V): 0.050 ∼ 0.095 wt%, titanium (Ti): 0.01 ∼ 0.02 wt%, calcium (Ca): 0.001
- 0.004 wt%, and the balance of iron (Fe) and other unavoidable impurities; (B) hot
rolling the reheated steel slab; and (C) cooling the hot-rolled steel plate.
[0053] The method of manufacturing the steel plate for pipelines according to the invention
reduces fractions of polygonal ferrite and band structures relatively vulnerable to
hydrogen-induced cracking, and includes finish-rolling to be performed at an Ar
3 transformation temperature or less to induce generation of mobile dislocations, which
are advantageous for reduction of yield ratio. As the generation of mobile dislocations
is induced by this method, the steel plate is reduced in yield strength, thereby lowering
the yield ratio. That is, the steel plate according to the present invention has a
low yield ratio, thereby providing excellent plastic deformation and anti-vibration
effects. Further, in the manufacturing method of the steel plate according to the
invention, the cooling rate is controlled to form acicular ferrite and bainite structures
in a fraction of 30% or more.
[0054] The manufacturing method of the steel plate according to the present invention will
be described in more detail.
(A) Slab reheating (S110)
[0055] In continuous casting of a steel slab, elements such as Mn, P, S, and the like are
likely to be segregated in the steel slab, so that the steel slab has a higher concentration
in a central region than in peripheral regions. Since such central segregation provides
a propagation passage of hydrogen-induced cracking, it is desirable to suppress central
segregation. During slab reheating, such elements causing central segregation diffuse
into peripheral regions, thereby relieving central segregation.
[0056] Advantageously, reheating is performed at temperatures of 1000°C or more in order
to relieve central segregation.
[0057] Further, Nb and V can be sufficiently dissolved in the steel during reheating of
the steel slab and can be finely precipitated to increase strength of the steel during
rolling. Thus, advantageously, the steel slab may be reheated at a temperature from
1100°C to 1250°C to achieve sufficient dissolution of Nb and V in the steel slab.
(B) Hot rolling (S120)
(Finish-rolling finishing temperature: 750∼850°C)
[0058] As mentioned above, in the method of manufacturing the steel plate according to the
invention, finish-rolling is performed at an Ar
3 transformation temperature or less to induce generation of mobile dislocations which
are favorable to reduction of the yield ratio.
[0059] The finish-rolling finishing temperature may be set to 750°C or more to ensure that
the steel plate has excellent hydrogen-induced crack resistance and the acicular ferrite
and bainite structures are formed in a fraction of 30% or more.
[0060] Although the pearlite fraction is decreased with increasing finish-rolling finishing
temperature before initiation of quenching, the strength of the steel is also decreased.
Thus, advantageously, the finish-rolling finishing temperature is set to 850°C or
less to prevent the decrease in strength of the steel plate.
(Finish-rolllng reduction rate: 50% to 70% based on a reduction rate of 100 at an
Ar3 transformation temperature or less)
[0061] Advantageously, the reduction rate of hot rolling is set in the range of 50% to 70%
based on a reduction rate of 100 at an Ar
3 transformation temperature or less in order to restrict an average grain size of
acicular ferrite microstructure in a final product of the steel plate according to
the present invention.
(C) Cooling (S130)
(Cooling finishing temperature: 300∼450°C)
[0062] In order to improve hydrogen-induced crack resistance, the cooling finishing temperature
may be restricted in the cooling stage.
[0063] An excess of ferrite and pearlite microstructures can cause deterioration not only
in hydrogen-induced crack resistance but also in low temperature toughness. Thus,
the cooling finishing temperature may be set to 300°C.
[0064] However, since a cooling finishing temperature exceeding 450°C can cause increase
in pearlite fraction in the microstructure of the steel plate, the cooling finishing
temperature may be sent to 450°C or less.
(Cooling rate: 15∼25°C/sec)
[0065] By controlling the cooling rate in the cooling stage, it is possible to control central
microstructure and hardness of the steel plate according to the invention.
[0066] A cooling rate of less than 15°C/sec makes it difficult for the steel plate to obtain
sufficient hardness. In addition, a cooling rate exceeding 25°C/sec can cause deterioration
in hydrogen-induced crack resistance.
[0067] Advantageously, the cooling rate is set in the range of 15∼25°C/sec.
Example
[0068] Next, constitution and operation of the present invention will be described in more
detail with reference to some inventive examples. It should be noted that the following
examples are provided for illustration only and should not be construed in any way
as limiting the scope of the present invention.
[0069] Descriptions of details apparent to those skilled in the art will be omitted.
1. Preparation of specimens
[0070] Table 1 shows compositions of steel specimens prepared in examples and comparative
examples.
[0071] In Table 1, steel specimens prepared in Comparative Examples 1 to 3 are conventional
steel plates for pipelines, and steel specimens prepared in Examples 1 to 3 are inventive
steel plates for pipelines in which chromium and other alloy components are present
in a suitable composition ratio without adding copper.
Table 1
No. |
C |
Si |
Mn |
P |
S |
Cr |
Ni |
Al |
Cu |
Ti |
Nb |
V |
Ca |
Ca/S |
Ceq |
CE 1 |
0.04 |
0.25 |
1.20 |
0.005 |
0.0012 |
- |
- |
0.021 |
- |
0.013 |
0.04 |
0.027 |
0.0018 |
1.4 |
0.245 |
CE 2 |
0.04 |
0.25 |
1.20 |
0.005 |
0.0012 |
- |
0.23 |
0.020 |
0.16 |
0.014 |
0.039 |
0.031 |
0.0019 |
1.6 |
0.272 |
CE 3 |
0.04 |
0.25 |
1.21 |
0.005 |
0.0011 |
0.24 |
0.24 |
0.022 |
0.20 |
0.013 |
0.038 |
0.028 |
0.0017 |
1.5 |
0.325 |
Ex. 1 |
0.04 |
0.25 |
1.20 |
0.005 |
0.0012 |
0.23 |
0.21 |
0.021 |
- |
0.014 |
0.040 |
0.029 |
0.0019 |
1.6 |
0.302 |
Ex. 2 |
0.04 |
0.24 |
1.21 |
0.006 |
0.0011 |
0.24 |
0.40 |
0.021 |
- |
0.014 |
0.040 |
0.030 |
0.0018 |
1.6 |
0.332 |
Ex. 3 |
0.04 |
0.26 |
1.20 |
0.006 |
0.0012 |
0.25 |
0.23 |
0.020 |
- |
0.014 |
0.039 |
0.027 |
0.0018 |
1.5 |
0.311 |
[0072] The steel specimens prepared in Comparative Examples 1 to 3 are conventional steel
plates for pipelines, and the steel specimens prepared in Examples 1 to 3 are inventive
steel plates for pipelines in which chromium and other alloy components are present
in a suitable composition ratio without adding copper.
2. Measurement and evaluation of physical properties
[0073] Each of the specimens prepared in the comparative examples and the inventive examples
was subjected to tensile testing, impact testing and HIC (hydrogen-induced cracking)
testing to observe occurrence of cracking.
[0074] Fig. 2 is a graph depicting yield strength and tensile strength of each of the specimens
prepared in the inventive examples and the comparative examples. In the bar graph,
left-side bars indicate yield strength (YS) and right-side bars indicate tensile strength
(TS).
[0075] The specimens of Examples 1 to 3 did not contain copper (Cu), which is included in
conventional steel plates for pipelines. It can be confirmed that these steel specimens
have a tensile strength of 450 MPa or more even without containing Cu.
[0076] Since the specimens of the inventive examples did not undergo significant reduction
in impact toughness even without containing Cu, the specimens of the inventive examples
had similar results to the specimens of the comparative examples in impact testing.
Fig. 3 is a graph depicting results of impact testing with respect to the respective
specimens of the inventive examples and the comparative examples.
[0077] Results of tensile testing and impact testing are summarized in Table 2.
Table 2
Specimen |
Tensile testing |
Impact testing |
YS (MPa) |
TS (MPa) |
EL (%) |
0°C |
-80°C |
Comparative Example 1 |
452 |
531 |
35 |
357 |
302 |
Comparative Example2 |
484 |
560 |
30 |
375 |
302 |
Comparative Example3 |
512 |
610 |
25 |
324 |
305 |
Example 1 |
455 |
580 |
27 |
337 |
304 |
Example2 |
533 |
651 |
29 |
362 |
327 |
Example3 |
480 |
640 |
27 |
359 |
292 |
[0078] Fig. 4 shows results of hydrogen-induced cracking testing.
[0079] Pictures of the specimens before and after HIC testing are provided in this drawing.
[0080] It can be seen that the specimens of Examples 1 to 3 undergo no cracking and have
excellent hydrogen-induced crack resistance.
[0081] In Table 3, results of HIC testing with respect to the respective specimens are summarized.
Table 3
Specimen |
Total length of crack (mm) |
Total thickness of crack (mm) |
CLR |
CTR |
CSR |
Comparative Example1 |
3.4 |
0.07 |
5.7 % |
0.23 % |
0.04 % |
Comparative Example2 |
1.8 |
0.2 |
3 % |
0.67 % |
0.06 % |
Comparative Example3 |
0 |
0 |
0 |
0 |
0 |
Example1, 2, 3 |
0 |
0 |
0 |
0 |
0 |
CLR: Crack length ratio, CTR: Crack thickness ratio, CSR: Crack sensitivity ratio |
[0082] Although some embodiments have been described herein, it will be understood by those
skilled in the art that these embodiments are provided for illustration only, and
various modifications, changes, alterations and equivalent embodiments can be made
without departing from the scope of the present invention. Therefore, the scope and
sprit of the present invention should be defined only by the accompanying claims and
equivalents thereof.
1. A steel plate comprising:
carbon (C), 0.03 ∼ 0.05 wt%; silicon (Si), 0.2 - 0.3 wt%; manganese (Mn), 0.5 - 1.3
wt%; phosphorous (P), 0.010 wt% or less; sulfur (S), 0.005 wt% or less; aluminum (Al),
0.02 - 0.05 wt%; nickel (Ni), 0.2 - 0.5 wt%; chromium (Cr), 0.2 ∼ 0.3 wt%; niobium
(Nb), 0.03 - 0.05 wt%; vanadium (V), 0.02 - 0.05 wt%; titanium (Ti), 0.01 - 0.02 wt%;
calcium (Ca), 0.001 - 0.004 wt%; and the balance of iron (Fe) and other unavoidable
impurities,
the steel plate having a tensile strength of 450 MPa or more.
2. The steel plate according to claim 1, wherein the steel plate has a yield ratio (yield
strength/tensile strength) of 80% or less.
3. The steel plate according to claim 1, wherein microstructure of the steel plate is
a composite structure including acicular ferrite and bainite structures.
4. The steel plate according to claim 3, wherein the composite structure including acicular
ferrite and bainite structures occupies 30% or more of the entirety of the microstructure
in terms of cross-sectional area ratio.
5. The steel plate according to claim 4, wherein a composite structure including ferrite
and pearlite structures occupies 70% or less of the entirety of the microstructure
in terms of cross-sectional area ratio.
6. A method of manufacturing a steel plate, comprising:
(A) reheating a steel slab including: carbon (C), 0.03 - 0.05 wt%; silicon (Si), 0.2
- 0.3 wt%; manganese (Mn), 0.5 - 1.3 wt%; phosphorous (P), 0.010 wt% or less; sulfur
(S), 0.005 wt% or less; aluminum (Al), 0.02 - 0.05 wt%; nickel (Ni), 0.2 - 0.5 wt%;
chromium (Cr), 0.2 - 0.3 wt%; niobium (Nb), 0.03 - 0.05 wt%; vanadium (V), 0.02 -
0.05 wt%; titanium (Ti), 0.01 ∼ 0.02 wt%; calcium (Ca), 0.001 - 0.004 wt%; and the
balance of iron (Fe) and other unavoidable impurities;
(B) hot rolling the reheated steel slab; and
(C) cooling the hot-rolled steel plate.
7. The method according to claim 6, wherein the reheating (A) is performed at a temperature
of 1100 ∼ 1250°C.
8. The method according to claim 6, wherein the hot rolling (B) is performed at a reduction
rate of 50% to 70% based on the whole reduction rate of 100 at an Ar3 temperature or less.
9. The method according to claim 6, wherein the hot rolling (B) has a rolling finishing
temperature of 750∼850°C.
10. The method according to claim 6, wherein the cooling (C) has a cooling finishing temperature
of 300∼450°C.
11. The method according to claim 6, wherein the cooling (C) is performed at a cooling
rate of 15∼25 °C /sec.