TECHNICAL FIELD
[0001] This disclosure relates to a steel plate that is suitable for structural steel used
in an extremely low-temperature environment such as a storage tank of liquefied gas,
in particular, a steel plate excellent in corrosion resistance in a salinity corrosive
environment, and a method for manufacturing the same.
BACKGROUND
[0002] In using a hot-rolled steel plate in a structure for a storage tank of liquefied
gas, the operating environment is at extremely low temperatures. Therefore, the hot-rolled
steel plate needs to have not only high strength but also toughness at extremely low
temperatures. For example, for a hot-rolled steel plate used for a storage tank of
liquefied natural gas, excellent toughness needs to be guaranteed at the boiling point
of liquefied natural gas, that is, -164 °C or lower. When a steel material has poor
low-temperature toughness, the safety as a structure for an extremely low-temperature
storage tank may not be maintained. Thus, there is a growing demand for steel materials
with improved low-temperature toughness that are applied to such a structure. In view
of the demand, austenitic stainless steel which has an austenite microstructure exhibiting
no brittleness at extremely low temperatures, 9 % Ni steel, or five thousand series
aluminum alloys have been conventionally used. However, the alloy cost and manufacturing
cost of those metal materials are high, and thus there is a demand for steel plates
which are inexpensive and excellent in extremely low-temperature toughness. As new
steel plates replacing conventional steel for extremely low temperatures, high-Mn
steel added with a large amount of Mn which is a relatively inexpensive austenite-stabilizing
element to form an austenite microstructure is considered to be used as a structural
steel plate used in an extremely low-temperature environment.
[0003] However, when a steel plate having an austenite microstructure is placed in a corrosive
environment, austenite crystal grain boundaries are eroded by corrosion and when a
tensile stress is added, stress corrosion cracking easily occurs, which is a problem
of high-Mn steel. In manufacturing a structure for a storage tank of liquefied gas
and the like, a steel substrate of a steel plate may be exposed, and when the exposed
steel material surface contacts with water vapor containing corrosive substances including
salinity, water, and oil, the steel material would be corroded. In the corrosion reaction
on a steel plate surface, oxide (rust) is formed from iron by an anodic reaction.
Meanwhile, hydrogen is generated by a cathodic reaction of water to enter into the
steel, causing hydrogen embrittlement. When residual stress generated by bending or
welding during manufacturing or load stress in an operating environment is exerted
thereon, stress corrosion cracking may be caused, leading to rupture of a structure.
Conventional high-Mn steel may be inferior in terms of corrosion resistance to not
only austenitic stainless steel but also 9 % Ni steel and normal low-alloy steel.
Therefore, from the viewpoint of safety, it is important that the steel material to
be used has not only high strength and toughness at extremely low temperatures but
also excellent corrosion resistance.
[0004] For example,
JP 2015-508452 A (PTL 1) describes a steel material having improved machinability by cutting and Charpy
impact properties at -196 °C of a weld heat-affected zone (HAZ) through addition of
Mn in an amount of 15 % to 35 %, Cu in an amount of 5 % or less, and C and Cr in a
suitable amount.
[0005] JP 2016-84529 A (PTL 2) describes a high-Mn steel material having improved low temperature toughness
through addition of C: 0.25 % to 0.75 %; Si: 0.05 % to 1.0 %; Mn: more than 20 % to
35 % or less; Ni: 0.1 % or more and less than 7.0 %; and Cr: 0.1 % or more and less
than 8.0 %.
[0006] JP 2016-196703 A (PTL 3) describes a high-Mn steel material having a base metal and a welded portion
with improved extremely low-temperature toughness through addition of C in an amount
of 0.001 % to 0.80 % and Mn in an amount of 15 % to 35 %, and addition of elements
such as Cr, Ti, Si, Al, Mg, Ca, and REM.
CITATION LIST
Patent Literature
SUMMARY
(Technical Problem)
[0008] However, there is room for consideration in the steel materials described in PTL
1, PTL 2, and PTL 3 from the viewpoint of manufacturing cost for obtaining strength
and low-temperature toughness and corrosion resistance when the austenite steel material
is placed in a salinity corrosive environment.
[0009] It could thus be helpful to provide high-Mn steel excellent in corrosion resistance,
in particular corrosion resistance in a salinity corrosive environment.
(Solution to Problem)
[0010] To achieve the aforementioned object, the inventors conducted extensive study on
high-Mn steel as to various factors determining the chemical composition and manufacturing
conditions to discover the following.
[0011] a. In adding Cr to high-Mn steel, the addition amount of Cr and the amount of dissolved
Cr is properly controlled to thereby make it possible to delay an initial corrosion
reaction on a steel plate surface in a salinity corrosive environment. In this way,
the hydrogen amount entering into steel can be reduced to suppress the stress corrosion
cracking of austenite steel.
[0012] b. Further, a measure of improving crystal grain boundary strength is valid for effectively
suppressing rupture of austenite originating from crystal grain boundaries. In particular,
P is an element which is easily segregated, as with Mn, during a solidification process
of a slab and lowers the crystal grain boundary strength of a portion crossing such
a segregation portion. Therefore, impurity elements such as P need to be reduced.
[0013] This disclosure is based on the above discoveries and further investigation conducted
by the inventors. The primary features of this disclosure are as follows.
- 1. A steel plate comprising a chemical composition containing (consisting of), in
mass%,
C: 0.20 % or more and 0.70 % or less,
Si: 0.05 % or more and 1.00 % or less,
Mn: 15.0 % or more and 35.0 % or less,
P: 0.030 % or less,
S: 0.0200 % or less,
Al: 0.010 % or more and 0.100 % or less,
Cr: 0.5 % or more and 8.0 % or less, and
N: 0.0010 % or more and 0.0300 % or less, with the balance being Fe and inevitable
impurities,
wherein at least 60 % of the contained Cr is solute Cr.
- 2. The steel plate according to 1., wherein the chemical composition further contains,
in mass%, at least one selected from the group consisting of
Nb: 0.003 % or more and 0.030 % or less,
V: 0.01 % or more and 0.10 % or less, and
Ti: 0.003 % or more and 0.040 % or less.
- 3. The steel plate according to 1. or 2., wherein the chemical composition further
contains, in mass %, at least one selected from the group consisting of
Cu: 0.01 % or more and 0.50 % or less,
Ni: 0.01 % or more and 0.50 % or less,
Sn: 0.01 % or more and 0.30 % or less,
Sb: 0.01 % or more and 0.30 % or less,
Mo: 0.01 % or more and 2.0 % or less, and
W: 0.01 % or more and 2.0 % or less.
- 4. The steel plate according to 1., 2., or 3., wherein the chemical composition further
contains, in mass %, at least one selected from the group consisting of
Ca: 0.0005 % or more and 0.0050 % or less,
Mg: 0.0005 % or more and 0.0100 % or less, and
REM: 0.0010 % or more and 0.0200 % or less.
- 5. A method for manufacturing a steel plate, comprising: heating a steel raw material
having the chemical composition according to any of 1. to 4. to 1000 °C or higher
and 1300 °C or lower; subsequently hot rolling the steel raw material with a rolling
reduction ratio of 3 or more and 30 or less, a finish rolling temperature of 750 °C
or higher, and a time for which a material to be rolled resides within a temperature
range of 600 °C to 950 °C of 30 minutes or less to obtain a hot-rolled steel plate;
and then, cooling the hot-rolled steel plate at an average cooling rate of 3 °C/s
or more within a temperature range of 600 °C to 700 °C.
[0014] In this disclosure, "excellent in corrosion resistance" means a fracture stress of
400 MPa or more when a test in accordance with the Slow Strain Rate Test Method based
on NACE Standard TM0111-2011 is performed by immersing in artificial seawater (chloride
ion concentration of 18000 ppm) at 23 °C and performing a constant-rate tensile test
at a strain rate of 4 × 10
-7 inch/s.
(Advantageous Effect)
[0015] According to this disclosure, it is possible to provide a steel plate excellent in
corrosion resistance, in particular, corrosion resistance in a salinity corrosive
environment. Therefore, when our steel plate is used for a steel structure used in
an extremely low-temperature environment such as a tank for a storage tank of liquefied
gas, the safety and the service life of the steel structure is significantly improved,
thus producing significantly advantageous effects in industrial terms. Further, our
steel plate is inexpensive compared with conventional materials, and thus excellent
in economic efficiency.
DETAILED DESCRIPTION
[0016] Our steel plate will be described in detail hereinafter. Note that this disclosure
is not limited to the following examples.
[Chemical composition]
[0017] The chemical composition of our steel plate and the reasons for the limitations thereof
are described first. In this disclosure, to ensure excellent corrosion resistance,
the chemical composition of the steel plate is defined as follows. In the description
of the chemical composition, "%" denotes "mass%" unless otherwise noted.
C: 0.20 % or more and 0.70 % or less
[0018] C, which is effective for increasing strength and an inexpensive austenite-stabilizing
element, is an important element to obtain austenite. To obtain this effect, the C
content needs to be 0.20 % or more. On the other hand, a C content beyond 0.70 % promotes
excessive precipitation of Cr carbides and Nb, V, and Ti based carbides, and thus
lowers low-temperature toughness and becomes a corrosion origin. Therefore, the C
content is set to be 0.20 % or more and 0.70 % or less, and preferably 0.25 % or more
and 0.60 % or less.
Si: 0.05 % or more and 1.00 % or less
[0019] Si acts as a deoxidizer, is necessary for steelmaking, and is effective at increasing
the strength of a steel plate by solid solution strengthening when dissolved in steel.
To obtain such an effect, the Si content needs to be 0.05 % or more. On the other
hand, a Si content beyond 1.00 % may deteriorate weldability and surface characteristics,
lowering stress corrosion cracking resistance. Therefore, the Si content is set to
0.05 % or more and 1.00 % or less, and preferably 0.07 % or more and 0.50 % or less.
Mn: 15.0 % or more and 35.0 % or less
[0020] Mn is a relatively inexpensive austenite-stabilizing element. In this disclosure,
Mn is an important element for achieving both high strength and extremely low-temperature
toughness. To obtain those effects, the Mn content needs to be 15.0 % or more. On
the other hand, the Mn content beyond 35.0 % causes saturation of the effect of improving
the extremely low-temperature toughness, increasing alloy costs. Further, such a high
Mn content deteriorates weldability and cuttability, and further promotes segregation
as well as the occurrence of stress corrosion cracking. Therefore, the Mn content
is set to 15.0 % or more and 35.0 % or less, and preferably 18.0 % or more and 28.0
% or less.
P: 0.030 % or less
[0021] When the P content is beyond 0.030 %, P segregates to grain boundaries to lower grain
boundary strength and becomes an origin of stress corrosion cracking. Therefore, the
upper limit of the P content is 0.030 %, and desirably, the P content is kept as small
as possible. Properties are improved as the P content is lower, and thus, the P content
is preferably set to 0.024 % or less, and more preferably 0.020 % or less. On the
other hand, reducing the P content to less than 0.001 % involves high steelmaking
costs and impairs economic efficiency. Thus, the content of 0.001 % or more is allowable.
S: 0.0200 % or less
[0022] S deteriorates the low-temperature toughness and ductility of the base metal. Therefore,
the upper limit of the S content is 0.0200 %, and desirably, the S content is kept
as small as possible. Therefore, the S content is set to 0.0200 % or less, and preferably
0.0180 % or less. On the other hand, reducing the S content to less than 0.0001 %
involves high steelmaking costs and impairs economic efficiency. Thus, the content
of 0.0001 % or more is allowable.
Al: 0.010 % or more and 0.100 % or less
[0023] Al acts as a deoxidizer and is used most commonly in molten steel deoxidizing processes
to obtain a steel plate. Al also has an effect of fixing solute N in steel to form
AlN, thus suppressing coarsening of crystal grains. Additionally, Al has an effect
of suppressing deterioration of toughness caused by decrease in solute N. To obtain
such an effect, the Al content needs to be 0.010 % or more. On the other hand, a Al
content beyond 0.100 % may form coarse nitrides which would become an origin of corrosion
and fracture, thus lowering stress corrosion cracking resistance. Further, Al diffuses
to a weld metal portion during welding to deteriorate toughness of the weld metal.
Thus, the Al content is set to 0.100 % or less, and preferably 0.020 % or more and
0.070 % or less.
Cr of 0.5 % or more and 8.0 % or less and at least 60 % of the contained Cr being
solute Cr
[0024] Cr is an important element because it is contained in a suitable amount to thereby
produce an effect of delaying an initial corrosion reaction on a steel plate surface
in a salinity corrosive environment to decrease the amount of hydrogen entering a
steel plate and improve stress corrosion cracking resistance. When the Cr content
is increased, corrosion resistance can be improved. On the other hand, Cr inevitably
precipitates in the form of, for example, a nitride, a carbide, or a carbonitride
during rolling and those precipitates may become an origin of corrosion and fracture
to deteriorate stress corrosion cracking resistance. Therefore, the Cr content is
set to 0.5 % or more and 8.0 % or less.
[0025] Examining in detail the Cr effect which delays an initial corrosion reaction on a
steel plate surface in a salinity corrosive environment, it has been found that the
amount of solute Cr is important to ensure this effect, and when Cr exists in a solid
solution state in an amount of 0.3 % or more, the effect is surely exhibited. On the
other hand, it is necessary to devise manufacturing conditions to make Cr solid solution
state and since the lower limit of Cr solid dissolution ratio which can be stably
ensured by a minor change of manufacturing conditions is 60 %, the Cr content needs
to be at least 0.5 % to obtain solute Cr in an amount of 0.3 % or more. The amount
of solute Cr is preferably 1.0 % or more and 6.0 % or less, and more preferably 1.2
% or more and 5.5 % or less. The solid solution state refers to a state in which solute
atoms exist as atoms without forming precipitates.
N: 0.0010 % or more and 0.0300 % or less
[0026] N is an austenite-stabilizing element and an element which is effective for improving
extremely low-temperature toughness. Further, N has an effect of bonding with Nb,
V, and Ti to finely precipitate as nitrides or carbonitrides and serving as a diffusible
hydrogen trapping site to suppress stress corrosion cracking. To obtain such an effect,
the N content needs to be 0.0010 % or more. On the other hand, a N content beyond
0.0300 % promotes the formation of excessive nitrides or carbonitrides to reduce the
solute element amount, lowering not only corrosion resistance but also toughness.
Therefore, the N content is set to 0.0010 % or more and 0.0300 % or less, and preferably
0.0020 % or more and 0.0150 % or less.
[0027] In this disclosure, to further improve corrosion resistance, in addition to the above
essential elements, the following elements can be contained as necessary:
Nb: 0.003 % or more and 0.030 % or less and V: 0.01 % or more and 0.10 % or less,
and Ti: 0.003 % or more and 0.040 % or less.
Nb: 0.003 % or more and 0.030 % or less
[0028] Nb precipitates as carbonitrides and the formed carbonitrides serve as a diffusible
hydrogen trapping site. Thus, Nb is an element which has an effect of suppressing
stress corrosion cracking. To obtain such an effect, Nb is preferably contained in
an amount of 0.003 % or more. On the other hand, when the Nb content is more than
0.030 %, coarse carbonitrides may precipitate to become an origin of fracture. Further,
the precipitates may be coarsened to deteriorate base metal toughness. Therefore,
when Nb is contained, the Nb content is preferably set to 0.003 % or more and 0.030
% or less, more preferably 0.005 % or more and 0.025 % or less, and further preferably
0.007 % or more and 0.022 % or less.
V: 0.01 % or more and 0.10 % or less
[0029] V precipitates as carbonitrides and the formed carbonitrides serve as a diffusible
hydrogen trapping site. Thus, V is an element which has an effect of suppressing stress
corrosion cracking. To obtain such an effect, V is preferably contained in an amount
of 0.01 % or more. On the other hand, when the V content is more than 0.10 %, coarse
carbonitrides may precipitate to become an origin of fracture. Further, the precipitates
may be coarsened to deteriorate base metal toughness. Therefore, when V is contained,
the V content is preferably set to 0.01 % or more and 0.10 % or less, more preferably
0.02 % or more and 0.09 % or less, and further preferably 0.03 % or more and 0.08
% or less.
Ti: 0.003 % or more and 0.040 % or less
[0030] Ti precipitates as nitrides or carbonitrides and the formed nitrides or carbonitrides
serve as a diffusible hydrogen trapping site. Thus, Ti is an element which has an
effect of suppressing stress corrosion cracking. To obtain such an effect, Ti is preferably
contained in an amount of 0.003 % or more. On the other hand, when the Ti content
is more than 0.0040 %, the precipitates may be coarsened to deteriorate base metal
toughness. Further, coarse carbonitrides may precipitate to become an origin of fracture.
When Ti is contained, the Ti content is preferably set to 0.003 % or more and 0.040
% or less, more preferably 0.005 % or more and 0.035 % or less, and further preferably
0.007 % or more and 0.032 % or less.
[0031] In this disclosure, to further improve corrosion resistance, the chemical composition
may optionally contain at least one selected from the group of Cu: 0.01 % or more
and 0.50 % or less, Ni: 0.01 % or more and 0.50 % or less, Sn: 0.01 % or more and
0.30 % or less, Sb: 0.01 % or more and 0.30 % or less, Mo: 0.01 % or more and 2.0
% or less, and W: 0.01 % or more and 2.0 % or less.
[0032] Cu, Ni, Sn, Sb, Mo, and W are elements which are added with Cr to thereby improve
corrosion resistance of high-Mn steel in a salinity corrosive environment. Cu, Sn,
and Sb have an effect of increasing hydrogen overvoltage in a steel material to thereby
suppress a hydrogen evolution reaction corresponding to the cathodic reaction. Ni
forms a precipitation layer on a steel material surface and physically suppresses
permeation of corrosive anions such as Cl
- into a steel substrate. Further, Cu, Ni, Sn, Sb, Mo, and W are liberated as a metal
ion from a steel material surface during corrosion and densify corrosion products,
thereby suppressing permeation of corrosive anions into a steel interface (interface
between a rust layer and a steel substrate). Mo and W are liberated as MO
42- and WO
42-, respectively, and adsorbed in the corrosive products or to the steel plate surface,
thereby imparting cation selective permeability and electrically suppressing permeation
of corrosive anions into the steel substrate.
[0033] The above effects become apparent when those elements coexist with Cr in high-Mn
steel and are exerted when those elements are contained in an amount not lower than
the respective lower limits listed above. However, large contents of those elements
deteriorate weldability and toughness and are disadvantageous in terms of costs.
[0034] Therefore, preferred contents are: a Cu content of 0.01 % or more and 0.50 % or less;
a Ni content of 0.01 % or more and 0.50 % and less; a Sn content of 0.01 % or more
and 0.30 % or less; a Sb content of 0.01 % or more and 0.30 % or less; a Mo content
of 0.01 % or more and 2.0 % or less; and a W content of 0.01 % or more and 2.0 % or
less.
[0035] More preferred contents are: a Cu content of 0.02 % or more and 0.40 % or less; a
Ni content of 0.02 % or more and 0.40 % or less; a Sn content of 0.02 % or more and
0.25 % or less; a Sb content of 0.02 % or more and 0.25 % or less; a Mo content of
0.02 % or more and 1.9 % or less; and a W content of 0.02 % or more and 1.9 % or less.
[0036] Similarly, in this disclosure, to further improve corrosion resistance, the chemical
composition may optionally contain at least one selected from the group of Ca: 0.0005
% or more and 0.0050 % or less, Mg: 0.0005 % or more and 0.0100 % or less, and REM:
0.0010 % or more and 0.0200 % or less.
[0037] Ca, Mg, and REM are elements useful for morphological control of inclusions and can
be contained as necessary. As used herein, the morphological control of inclusions
means granulating elongated sulfide-based inclusions. The morphological control of
inclusions improves ductility, toughness, and sulfide stress corrosion cracking resistance.
To obtain such effects, Ca and Mg are preferably contained in an amount of 0.0005
% or more and REM is preferably contained in an amount of 0.0010 % or more. On the
other hand, when these elements are contained in a large amount, not only the amount
of nonmetallic inclusions may be increased, ending up deteriorating ductility, toughness,
and sulfide stress corrosion cracking resistance, but also an economic disadvantage
may be entailed.
[0038] Therefore, when Ca is contained, the Ca content is preferably set to 0.0005 % or
more and 0.0050 % or less, when Mg is contained, the Mg content is preferably set
to 0.0005 % or more and 0.0100 % or less, and when REM is contained, the REM content
is preferably set to 0.0010 % or more and 0.0200 % or less. A Ca content of 0.0010
% or more and 0.0040 % or less, a Mg content of 0.0010 % or more and 0.0040 % or less,
and a REM content is 0.0020 % or more and 0.0150 % or less are more preferable.
[0039] The following describes manufacturing conditions in this disclosure. In the following
description, temperatures (°C) refer to the temperature of the mid-thickness part
of a steel plate.
[Reheating temperature of a steel raw material: 1000 °C or higher and 1300 °C or lower]
[0040] Heating a steel raw material to 1000 °C or higher is for dissolving carbonitrides
in the microstructure to make the crystal grain size and the like uniform. Specifically,
when the heating temperature is lower than 1000 °C, carbonitrides are not sufficiently
dissolved and thus desired properties cannot be obtained. Further, heating at a temperature
higher than 1300 °C deteriorates material properties due to coarsening of crystal
grain size and needs excessive energy, lowering productivity. Thus, the upper limit
of the heating temperature is set to 1300 °C, preferably 1050 °C or higher and 1250
°C or lower, and more preferably 1070 °C or higher and 1250 °C or lower.
[Rolling reduction ratio: 3 or more and 30 or less]
[0041] Since in hot rolling with a rolling reduction ratio of less than 3, an effect of
promoting recrystallization and homogenizing a grain size cannot be obtained, coarse
austenite grains remain and a part having the coarse austenite grains is preferentially
oxidized, thereby deteriorating corrosion resistance. Therefore, the rolling reduction
ratio in hot rolling is limited to 3 or more. On the other hand, the upper limit of
the rolling reduction ratio needs to be 30 for the reasons given below. As used herein,
the rolling reduction ratio is defined by a plate thickness of a material to be rolled
/ a plate thickness of a steel plate after hot rolling.
[Finish rolling temperature: 750 °C or higher]
[0042] When the finish rolling temperature is lower than 750 °C, the amount of carbide precipitates
during rolling is significantly increased, and even when the time for which a material
to be rolled resides within a temperature range of 600 °C to 950 °C is 30 minutes
or less, a sufficient amount of solute Cr may not be obtained, lowering corrosion
resistance. Further, when rolling is performed at a temperature of lower than 750
°C, deformation resistance is increased to apply an excessive load to a manufacturing
apparatus. Thus, the finish rolling temperature is set to 750 °C or higher. From the
viewpoint of suppressing significant coarsening of crystal grain size, the upper limit
of the finish rolling temperature is preferably 1050 °C or lower.
[Time for which a material to be rolled resides within a temperature range of 600
°C to 950 °C: 30 minutes or less]
[0043] In hot rolling, if the time for which a material to be rolled resides within a temperature
range of 600 °C to 950 °C (residence time) is more than 30 minutes, a large amount
of carbonitrides and carbides precipitate during rolling and the necessary amount
of solute Cr cannot be obtained, lowering corrosion resistance and extremely-low temperature
toughness. Therefore, the time for which a material to be rolled resides within a
temperature range of 600 °C to 950 °C is limited to 30 minutes or less. The time for
which a material to be rolled resides within a temperature range of 600 °C to 950
°C is preferable as short as possible, and thus, no lower limit is placed thereon.
[0044] To set the time for which a material to be rolled resides within a temperature range
of 600 °C to 950 °C to 30 minutes or less, the length of the material to be rolled
is made to be 5000 mm or less and the rolling reduction ratio of the material to be
rolled is limited to 30 or less as described above. This is because when the length
of the material to be rolled is more than 5000 mm or the rolling reduction ratio is
more than 30, the rolling time becomes long and as a result, the time for which a
material to be rolled resides within a temperature range of 600 °C to 950 °C exceeds
30 minutes.
[Average cooling rate within a temperature range of 600 °C to 700 °C: 3 °C/s or more]
[0045] Since when the average cooling rate within a temperature range of 600 °C to 700 °C
is less than 3 °C/s, a large amount of precipitates such as Cr carbides are formed,
the average cooling rate is limited to 3 °C/s or more. The average cooling rate is
preferable as fast as possible, and thus, no upper limit is placed thereon.
EXAMPLES
[0046] Steels of Nos. 1 to 28 listed in Table 1 were produced by steelmaking to obtain slabs,
subsequently the slabs were formed into steel plates of sample Nos. 1 to 34 having
a plate thickness of 6 mm to 50 mm under the manufacturing conditions listed in Table
2, and the steel plates were subjected to the following test.
[0047] The corrosion resistance test was performed in accordance with the Slow Strain Rate
Test Method based on NACE Standard TM0111-2011 (hereinafter, referred to as "SSRT
test"). Test pieces having a shape of notched Type A round bar were used. The test
pieces were immersed in artificial seawater (having chloride ion concentration of
18000 ppm) at 23 °C and subjected to a constant-rate tensile test at a strain rate
of 4 × 10
-7 inch/s. In this disclosure, a test piece having a fracture stress of 400 MPa or more
was considered as having excellent stress corrosion cracking resistance. The results
thus obtained are listed in Table 2.
Table 2
Sample No. |
Material No. |
Material length (mm) |
Manufacturing conditions |
Base metal properties |
Stress corrosion cracking resistance |
Remarks |
Product thickness (mm) |
Heating temperature (°C) |
Rolling reduction ratio |
Finish rolling temperature (°C) |
Cooling start (°C) |
Cooling stop (°C) |
Average cooling rate* 1 (° C/s) |
Residence time (min) |
Solute Cr ratio (%) |
Fracture stress (MPa) |
1 |
1 |
4500 |
30 |
1100 |
5 |
850 |
800 |
500 |
30 |
10 |
85 |
559 |
|
2 |
2 |
5000 |
50 |
1200 |
3 |
900 |
850 |
550 |
15 |
5 |
95 |
529 |
|
3 |
3 |
1200 |
6 |
1200 |
30 |
760 |
700 |
550 |
130 |
25 |
75 |
518 |
|
4 |
4 |
4000 |
30 |
1150 |
7 |
850 |
800 |
500 |
40 |
15 |
80 |
573 |
|
5 |
5 |
2000 |
12 |
1200 |
15 |
850 |
750 |
500 |
75 |
20 |
90 |
580 |
|
6 |
6 |
4000 |
30 |
1250 |
6 |
850 |
800 |
600 |
30 |
10 |
75 |
554 |
|
7 |
7 |
3000 |
12 |
1150 |
10 |
850 |
780 |
550 |
70 |
20 |
85 |
569 |
|
9 |
9 |
1800 |
12 |
1200 |
15 |
900 |
750 |
550 |
30 |
30 |
70 |
502 |
|
8 |
8 |
5000 |
50 |
1200 |
4 |
900 |
800 |
550 |
15 |
8 |
90 |
581 |
Example |
10 |
10 |
5000 |
50 |
1280 |
3 |
900 |
750 |
550 |
10 |
5 |
75 |
503 |
|
11 |
11 |
4000 |
30 |
1150 |
5 |
800 |
750 |
500 |
30 |
8 |
85 |
495 |
|
12 |
12 |
2000 |
12 |
1050 |
15 |
750 |
700 |
500 |
70 |
15 |
80 |
481 |
|
13 |
13 |
2500 |
12 |
1150 |
10 |
800 |
750 |
600 |
75 |
10 |
85 |
590 |
|
14 |
14 |
1200 |
6 |
1250 |
25 |
750 |
700 |
450 |
140 |
30 |
65 |
483 |
|
15 |
15 |
1500 |
6 |
1150 |
20 |
750 |
700 |
400 |
140 |
30 |
70 |
521 |
|
16 |
16 |
5000 |
50 |
1200 |
4 |
950 |
900 |
550 |
15 |
5 |
90 |
546 |
|
17 |
17 |
2500 |
12 |
1150 |
10 |
800 |
750 |
500 |
75 |
15 |
80 |
536 |
|
18 |
18 |
1000 |
6 |
1050 |
30 |
800 |
700 |
500 |
70 |
30 |
60 |
335 |
|
19 |
19 |
2000 |
12 |
1050 |
15 |
750 |
700 |
500 |
70 |
*2 |
*2 |
*2 |
|
20 |
20 |
5000 |
50 |
1280 |
4 |
850 |
800 |
600 |
10 |
15 |
90 |
380 |
|
21 |
21 |
2000 |
12 |
1100 |
15 |
800 |
750 |
550 |
65 |
*2 |
*2 |
*2 |
|
22 |
22 |
3000 |
30 |
1200 |
5 |
850 |
800 |
550 |
30 |
20 |
85 |
351 |
|
23 |
23 |
1000 |
6 |
1100 |
30 |
750 |
700 |
450 |
70 |
30 |
60 |
305 |
|
24 |
24 |
2000 |
12 |
1050 |
15 |
800 |
750 |
500 |
70 |
20 |
85 |
378 |
|
25 |
25 |
1200 |
6 |
1150 |
30 |
900 |
850 |
550 |
35 |
30 |
60 |
352 |
Comparative Example |
26 |
26 |
1000 |
6 |
1200 |
30 |
800 |
700 |
500 |
130 |
25 |
65 |
358 |
27 |
27 |
2000 |
12 |
1100 |
15 |
800 |
750 |
550 |
30 |
25 |
50 |
329 |
28 |
28 |
2000 |
12 |
1150 |
15 |
750 |
700 |
500 |
35 |
20 |
70 |
345 |
|
29 |
9 |
4000 |
30 |
975 |
6 |
850 |
800 |
600 |
35 |
10 |
45 |
303 |
|
30 |
9 |
2000 |
12 |
1200 |
15 |
600 |
500 |
400 |
- |
30 |
50 |
294 |
|
31 |
9 |
2000 |
6 |
1200 |
30 |
800 |
naturally cooled |
naturally cooled |
2 |
50 |
40 |
285 |
|
32 |
9 |
2000 |
6 |
1100 |
40 |
800 |
750 |
500 |
5 |
40 |
40 |
292 |
|
33 |
9 |
5000 |
50 |
1200 |
3 |
850 |
800 |
600 |
15 |
45 |
45 |
292 |
|
34 |
9 |
5500 |
30 |
1200 |
7 |
850 |
800 |
600 |
30 |
40 |
45 |
322 |
|
Note: Underlines represent out of the scope of this disclosure.
*1 indicates an average cooling rate within a temperature range of700 °C to 600 °C.
*2 Measurement was omitted because an austenite microstructure was not obtained. |
[0048] Examples (sample Nos. 1 to 17) according to this disclosure were confirmed to have
corrosion resistance satisfying 400 MPa or more for the fracture stress of the SSRT
test. In contrast, comparative examples (sample Nos. 18 to 34) outside the scope of
this disclosure did not satisfy the above-described target performance in terms of
stress corrosion cracking resistance.
1. A steel plate comprising a chemical composition containing, in mass%,
C: 0.20 % or more and 0.70 % or less,
Si: 0.05 % or more and 1.00 % or less,
Mn: 15.0 % or more and 35.0 % or less,
P: 0.030 % or less,
S: 0.0200 % or less,
Al: 0.010 % or more and 0.100 % or less,
Cr: 0.5 % or more and 8.0 % or less, and
N: 0.0010 % or more and 0.0300 % or less, with the balance being Fe and inevitable
impurities,
wherein at least 60 % of the contained Cr is solute Cr.
2. The steel plate according to claim 1, wherein the chemical composition further contains,
in mass%, at least one selected from the group consisting of
Nb: 0.003 % or more and 0.030 % or less,
V: 0.01 % or more and 0.10 % or less, and
Ti: 0.003 % or more and 0.040 % or less.
3. The steel plate according to claim 1 or 2, wherein the chemical composition further
contains, in mass %, at least one selected from the group consisting of
Cu: 0.01 % or more and 0.50 % or less,
Ni: 0.01 % or more and 0.50 % or less,
Sn: 0.01 % or more and 0.30 % or less,
Sb: 0.01 % or more and 0.30 % or less,
Mo: 0.01 % or more and 2.0 % or less, and
W: 0.01 % or more and 2.0 % or less.
4. The steel plate according to claim 1, 2, or 3, wherein the chemical composition further
contains, in mass %, at least one selected from the group consisting of
Ca: 0.0005 % or more and 0.0050 % or less,
Mg: 0.0005 % or more and 0.0100 % or less, and
REM: 0.0010 % or more and 0.0200 % or less.
5. A method for manufacturing a steel plate, comprising:
heating a steel raw material having the chemical composition according to any of claims
1 to 4 to 1000 °C or higher and 1300 °C or lower; subsequently hot rolling the steel
raw material with a rolling reduction ratio of 3 or more and 30 or less, a finish
rolling temperature of 750 °C or higher, and a time for which a material to be rolled
resides within a temperature range of 600 °C to 950 °C of 30 minutes or less to obtain
a hot-rolled steel plate; and then, cooling the hot-rolled steel plate at an average
cooling rate of 3 °C/s or more within a temperature range of 600 °C to 700 °C.