Technical Field
[0001] The present invention relates to a ferritic stainless steel sheet and a method for
manufacturing the same, and more particularly relates to a ferritic stainless steel
sheet having excellent toughness and excellent corrosion resistance, which is suitable
for use as a material for flanges, and a method for manufacturing the same.
Background Art
[0002] An automobile exhaust gas passage is composed of various components, such as an exhaust
manifold, a muffler, a catalyst, a flexible tube, a center pipe, and a front pipe.
When these components are connected, fastening components called flanges are frequently
used. Flanges used for such exhaust system components are required to have sufficient
rigidity. Therefore, thick flanges (e.g., with a sheet thickness of 5 mm or more)
are used for such exhaust system components.
[0003] Furthermore, flanges are manufactured by press forming and blanking or the like,
and plain steel has been used.
[0004] Moreover, in recent years, sufficient corrosion resistance has been required for
materials for flanges that are used for components exposed to high-temperature exhaust
gas in an exhaust gas recirculation (EGR) system or the like. Accordingly, studies
have been conducted on use of stainless steel which has better corrosion resistance
than plain steel, in particular, ferritic stainless steel which has a relatively low
coefficient of thermal expansion and in which thermal stress is unlikely to occur.
Consequently, there has been a strong demand for a ferritic stainless steel sheet
having a large thickness (e.g., a sheet thickness of 5 mm or more) that can be used
for thick flanges.
[0005] However, a ferritic stainless steel sheet having a large thickness has a problem
in low-temperature toughness. For example, breakage during manufacturing of flanges
frequently occurs in winter. For this reason, there has been a strong demand for improvement
in the toughness of a ferritic stainless steel sheet having a large thickness.
[0006] In response to the market demand, for example, Patent Literature 1 discloses a stainless
steel sheet having excellent toughness (with a Charpy impact value of 50 J/cm
2 or more at -40°C), the stainless steel sheet containing, in percent by mass, C: 0.02%
or less, N: 0.02% or less, Si: 0.005 to 1.0%, Ni: 0.1 to 1.0%, Mn: 0.1 to 3.0%, P:
0.04% or less, S: 0.0100% or less, Cr: 10% or more and less than 18%, and further
one or two of Ti: 0.05 to 0.30% and Nb: 0.01 to 0.50%, the sum of Ti and Nb being
8(C+N) to 0.75%, with the balance being Fe and inevitable impurities, in which γ
p is 70% or more, the ferrite grain size is 20 µm or less, and the amount of martensite
formation is 70% or less. Note that γ
p (%) is evaluated by using the formula (i) below (in Patent Literature 1, expressed
as formula (1)): γ
p = 420(%C) + 470(%N) + 23(%Ni) + 9(%Cu) + 7(%Mn) - 11.5(%Cr) - 11.5(%Si) - 12(%Mo)
- 23(%V) - 47(%Nb) - 49(%Ti) - 52(%Al) + 189 (i), where (%X) represents the mass ratio
of each element X.
Citation List
Patent Literature
[0007] PTL 1: Japanese Unexamined Patent Application Publication No.
2016-191150
Summary of Invention
Technical Problem
[0008] However, when the present inventors tried to form the stainless steel sheet described
in Patent Literature 1 into the shape of a thick flange having a burring portion,
in some cases, cracks occurred in the burring portion, and it was not possible to
obtain a predetermined flange shape, revealing that the stainless steel sheet was
not sufficient to be used for thick flanges.
[0009] The present invention has been made under the circumstances described above, and
it is an object of the present invention to provide a ferritic stainless steel sheet
which has more excellent toughness and excellent corrosion resistance, and a method
for manufacturing the same.
[0010] In the present invention, the term "more excellent toughness" means that the Charpy
impact value at -50°C is 100 J/cm
2 or more. Furthermore, in the present invention, the term "excellent corrosion resistance"
means that, after a cyclic salt spray test specified in JIS H 8502 is performed for
three cycles, the rusting area ratio is 25% or less.
Solution to Problem
[0011] In order to solve the problem, the present inventors have conducted detailed studies.
As a result, the following findings have been obtained.
[0012] In order to form a steel sheet into a thick flange having a burring portion without
occurrence of cracks, it is effective to refine the metal structure and to set the
Charpy impact value at -50°C to be 100 J/cm
2 or more. Specifically, by setting the average crystal grain size of the metal structure
to be 45 µm or less, occurrence of cracks in the burring portion can be effectively
prevented when worked into a thick flange having a burring portion, and the steel
sheet can be satisfactorily put into practical use for a thick flange having a burring
portion.
[0013] Furthermore, a method, in which after a slab having a steel composition including
appropriate steel elements, specifically, Si, Mn, Cr, Ni, and the like, that are controlled
in appropriate ranges is heated at 1,050 to 1,250°C, hot rolling is performed, and
hot-rolled sheet annealing is performed at an appropriate temperature, is effective
in refining the metal structure and obtaining a Charpy impact value of 100 J/cm
2 or more at -50°C.
[0014] The present invention has been made on the basis of the findings described above,
and the gist of the invention is as follows.
- [1] A ferritic stainless steel sheet having a composition containing, in percent by
mass, C: 0.001 to 0.020%, Si: 0.05 to 0.35%, Mn: 0.05 to 1.00%, P: 0.04% or less,
S: 0.01% or less, Al: 0.001 to 0.300%, Cr: 10.0 to 13.0%, Ni: 0.75 to 1.50%, Ti: 0.05
to 0.35%, and N: 0.001 to 0.020%, with the balance being Fe and inevitable impurities,
in which γI [%] represented by formula (1) below is 65% or more, and a metal structure has an
average crystal grain size of 45 µm or less:
where Ni, Mn, Cu, Si, Cr, and Mo represent contents of the respective elements (percent
by mass), and an element not contained represents 0.
- [2] The ferritic stainless steel sheet according to [1], in which the composition
further contains, in percent by mass, one or two or more selected from Cu: 0.01 to
1.00%, Mo: 0.01 to 1.00%, W: 0.01 to 0.20%, and Co: 0.01 to 0.20%.
- [3] The ferritic stainless steel sheet according to [1] or [2], in which the composition
further contains, in percent by mass, one or two or more selected from V: 0.01 to
0.20%, Nb: 0.01 to 0.10%, and Zr: 0.01 to 0.20%.
- [4] The ferritic stainless steel sheet according to any one of [1] to [3], in which
the composition further contains, in percent by mass, one or two or more selected
from REM: 0.001 to 0.100%, B: 0.0002 to 0.0025%, Mg: 0.0005 to 0.0030%, and Ca: 0.0003
to 0.0030%.
- [5] A method for manufacturing the ferritic stainless steel sheet according to any
one of [1] to [4], including a hot rolling process in which a steel slab having the
composition is heated at 1,050 to 1,250°C, and then subjected to hot rolling, and
a hot-rolled sheet annealing process in which a hot-rolled steel sheet obtained in
the hot rolling process is subjected to hot-rolled sheet annealing at 750 to 1,050°C.
Advantageous Effects of Invention
[0015] According to the present invention, it is possible to obtain a ferritic stainless
steel sheet having more excellent toughness and excellent corrosion resistance. The
ferritic stainless steel sheet of the present invention can be suitably used for thick
flanges and the like. Description of Embodiments
[0016] The present invention will be described in detail below.
[0017] The present inventors have investigated in detail the reason for the occurrence of
cracks when various ferritic stainless steel sheets with a sheet thickness of 5.0
mm are each formed into a flange having a burring portion in which a flange hole (30
mmφ) is raised by 10 mm from the surface of the steel sheet as blanked. The results
have shown that cracks do not occur in steel sheets having a Charpy impact value of
100 J/cm
2 or more at -50°C, and in steel sheets in which cracks occur, the Charpy impact value
at -50°C is less than 100 J/cm
2. In this way, it has been found that low toughness is a cause for cracks.
[0018] Furthermore, the present inventors have investigated in detail the relationship between
the low toughness and the metal structure. As a result, it has been found that as
the average crystal grain size of the steel sheet increases, toughness decreases.
Accordingly, by using various ferritic stainless steel sheets (sheet thickness: 5.0
mm), forming into the flange has been tried. As a result, it has been found that in
steel sheets having an average crystal grain size of more than 45 µm, toughness decreases
and cracks are likely to occur, and that when the average crystal grain size is 45
µm or less, toughness is excellent and blanking workability of the steel sheet is
good.
[0019] Therefore, in the present invention, the average crystal grain size is set to be
45 µm or less, and the Charpy impact value at -50°C is set to be 100 J/cm
2 or more. Note that the average crystal grain size can be measured by a measurement
method used in examples which will be described later. Furthermore, the Charpy impact
value is a value measured in accordance with JIS Z 2242 (2005) as will be described
later.
[0020] The composition of the ferritic stainless steel sheet according to the present invention
will be described below. Hereinafter, unless otherwise stated, "%", which is the unit
of measure for the content of each element, means "percent by mass".
C: 0.001 to 0.020%
[0021] When the C content exceeds 0.020%, deterioration in workability and corrosion resistance
becomes conspicuous. A lower C content is more desirable from the viewpoint of corrosion
resistance and workability. However, in order to set the C content to be less than
0.001%, it takes a long time to perform refining, which is undesirable in terms of
manufacturing. Therefore, the C content is set in a range of 0.001% to 0.020%. The
C content is preferably 0.003% or more, and more preferably 0.004% or more. Furthermore,
the C content is preferably 0.015% or less, and more preferably 0.012% or less.
Si: 0.05 to 0.35%
[0022] Si is an element that has an effect of improving corrosion resistance of welds by
being concentrated in an oxide film formed during welding and is also effective as
a deoxidizing element in the steelmaking process. These effects are obtained at a
Si content of 0.05% or more and increase with increasing its content. On the other
hand, Si has an effect of accelerating ferrite phase formation. When the Si content
exceeds 0.35%, a predetermined amount of austenite phase is not formed sufficiently
during heating in the hot rolling process. Accordingly, even when hot rolling and
hot-rolled sheet annealing are performed under the conditions specified in the present
invention, a desired metal structure cannot be obtained. Therefore, the Si content
is set to be 0.05% or more and 0.35% or less. The Si content is preferably 0.10% or
more. Furthermore, the Si content is preferably 0.30% or less.
Mn: 0.05 to 1.00%
[0023] Mn has an effect of accelerating austenite phase formation. In order to obtain such
an effect, a Mn content of 0.05% or more is necessary. However, when the Mn content
exceeds 1.00%, precipitation of MnS serving as a starting point of corrosion is accelerated,
resulting in deterioration in corrosion resistance. Therefore, the Mn content is set
to be 0.05% or more and 1.00% or less. The Mn content is preferably 0.20% or more.
Furthermore, the Mn content is preferably 0.80% or less, and more preferably 0.70%
or less.
P: 0.04% or less
[0024] P is an element that is inevitably contained in steel. Since P is an element detrimental
to corrosion resistance and workability, it is desirable to decrease the amount of
P as much as possible. When the P content exceeds 0.04%, workability markedly deteriorates
by solid solution strengthening. Therefore, the P content is set to be 0.04% or less.
The P content is preferably 0.03% or less.
S: 0.01% or less
[0025] S, similar to P, is an element that is inevitably contained in steel. Since S is
an element detrimental to corrosion resistance and workability, it is desirable to
decrease the amount of S as much as possible. In particular, when the S content exceeds
0.01%, corrosion resistance markedly deteriorates. Therefore, the S content is set
to be 0.01% or less. The S content is preferably 0.008% or less, and more preferably
0.003% or less.
Al: 0.001 to 0.300%
[0026] Al is an effective deoxidizer. Furthermore, since Al has higher affinity for nitrogen
than Cr, in the case where nitrogen enters a weld, by precipitating nitrogen as Al
nitrides instead of Cr nitrides, Al has an effect of suppressing sensitization. These
effects can be obtained at an Al content of 0.001% or more. However, when the Al content
exceeds 0.300%, weld penetration deteriorates, resulting in deterioration in weldability,
which is undesirable. Therefore, the Al content is set in a range of 0.001% to 0.300%.
The Al content is preferably 0.010% or more. Furthermore, the Al content is preferably
0.200% or less, more preferably 0.100% or less, and still more preferably 0.050% or
less.
Cr: 10.0 to 13.0%
[0027] Cr is the most important element for securing corrosion resistance. When the Cr content
is less than 10.0%, corrosion resistance required for automobile exhaust components
cannot be obtained. On the other hand, when the Cr content exceeds 13.0%, even if
the steel composition is adjusted so as to satisfy γ
I represented by the predetermined formula (1) which will be described later, a predetermined
amount of austenite phase is not formed during heating in the hot rolling process.
Consequently, even when hot rolling and hot-rolled sheet annealing are performed under
the conditions specified in the present invention, a desired metal structure cannot
be obtained. Therefore, the Cr content is set in a range of 10.0% to 13.0%. The Cr
content is preferably 10.5% or more. Furthermore, the Cr content is preferably 12.0%
or less, and more preferably 11.7% or less.
Ni: 0.75 to 1.50%
[0028] Ni is an austenite-forming element and has an effect of increasing the amount of
austenite formed during heating before rolling in the hot rolling process. In the
present invention, by adjusting the steel composition, a dual-phase structure of ferrite
phase + austenite phase, which includes 70% or more, in volume ratio, of austenite
phase, is formed during heating the slab in the hot rolling process. In the case where
the metal structure is formed into a dual-phase structure of ferrite phase + austenite
phase, the interface between different phases, i.e., between the ferrite phase and
the austenite phase, functions as an obstacle to growth of crystal grains, and therefore,
the metal structure before hot rolling is refined. Then, working strain acting as
recrystallization sites is accumulated by a predetermined hot rolling operation, and
recrystallization is caused by hot-rolled sheet annealing in the subsequent process.
Thus, a fine metal structure is obtained, and excellent toughness is exhibited. These
effects can be obtained at a Ni content of 0.75% or more. On the other hand, when
the Ni content exceeds 1.50%, the improvement effect due to refinement of crystal
grains is saturated, and workability deteriorates. Moreover, stress corrosion cracking
is likely to occur. Therefore, the Ni content is set to be 0.75% or more and 1.50%
or less. The Ni content is preferably 0.80% or more. Furthermore, the Ni content is
preferably 1.20% or less, and more preferably 1.00% or less.
Ti: 0.05 to 0.35%
[0029] Ti preferentially combines with C and N, suppresses precipitation of Cr carbonitrides,
and lowers the recrystallization temperature. Ti also has an effect of suppressing
deterioration of corrosion resistance caused by sensitization due to precipitation
of Cr carbonitrides. In order to obtain these effects, a Ti content of 0.05% or more
is necessary. On the other hand, when the Ti content exceeds 0.35%, formation of coarse
TiN causes marked deterioration in toughness, and even if the technique of the present
invention is applied, predetermined toughness cannot be obtained. Furthermore, when
the Ti content exceeds 0.35%, coarse Ti carbonitrides are formed in the casting process,
resulting in surface defects, which is undesirable in terms of manufacturing. Therefore,
the Ti content is set to be 0.05% or more and 0.35% or less. The Ti content is preferably
0.10% or more. Furthermore, the Ti content is preferably 0.30% or less, and more preferably
0.15% or less.
N: 0.001 to 0.020%
[0030] When the N content exceeds 0.020%, deterioration in workability and corrosion resistance
becomes conspicuous. A lower N content is more desirable from the viewpoint of workability
and corrosion resistance. However, in order to decrease the N content to less than
0.001%, it is necessary to perform refining for a long time, resulting in an increase
in manufacturing costs and a decrease in productivity, which are undesirable. Therefore,
the N content is set in a range of 0.001% to 0.020%. The N content is preferably 0.005%
or more, and more preferably 0.007% or more. Furthermore, the N content is preferably
0.015% or less, and more preferably 0.012% or less.
γI [%] : 65% or more
[0031] When γ
I represented by formula (1) below is less than 65%, because of an insufficient amount
of austenite in the metal structure, a fine metal structure cannot be obtained at
a slab heating temperature before starting hot rolling. Therefore, γ
I [%] is set to be 65% or more. Note that γ
I [%] is obtained by using formula (1) below, which evaluates the stability of austenite
phase.
where Ni, Mn, Cu, Si, Cr, and Mo represent contents of the respective elements (percent
by mass), and an element not contained represents 0. In the formula (1), an austenite-forming
element has a positive factor, and a ferrite-forming element has a negative factor.
The values were experimentally obtained with reference to the Castro formula.
[0032] In the present invention, the balance other than the above is Fe and inevitable impurities.
Examples of the inevitable impurities include oxygen (O), and an O content of 0.01%
or less is permissible.
[0033] In addition to the essential elements described above, as necessary, the ferritic
stainless steel sheet can further contain one group or two or more groups selected
from groups A to C described below.
(Group A) one or two or more selected from Cu: 0.01 to 1.00%, Mo: 0.01 to 1.00%, W:
0.01 to 0.20%, and Co: 0.01 to 0.20%
(Group B) one or two or more selected from V: 0.01 to 0.20%, Nb: 0.01 to 0.10%, and
Zr: 0.01 to 0.20%
(Group C) one or two or more selected from REM: 0.001 to 0.100%, B: 0.0002 to 0.0025%,
Mg: 0.0005 to 0.0030%, and Ca: 0.0003 to 0.0030%
Cu: 0.01 to 1.00%
[0034] Cu is a particularly effective element in improving corrosion resistance in an aqueous
solution or when weakly acidic water drops adhere to the steel sheet. Furthermore,
Cu has an effect of accelerating austenite phase formation. This effect can be obtained
at a Cu content of 0.01% or more and increases with increasing Cu content. However,
when the Cu content exceeds 1.00%, hot workability deteriorates, which may induce
surface defects in some cases. Furthermore, descaling after annealing may become difficult
in some cases. Therefore, when Cu is contained, the Cu content is set in a range of
0.01% to 1.00%. When Cu is contained, the Cu content is preferably 0.10% or more.
Furthermore, when Cu is contained, the Cu content is preferably 0.50% or less.
Mo: 0.01 to 1.00%
[0035] Mo is an element that markedly improves the corrosion resistance of stainless steel.
This effect is obtained at a Mo content of 0.01% or more and improves with increasing
content. On the other hand, Mo has an effect of accelerating ferrite phase formation.
When the Mo content exceeds 1.00%, a predetermined amount of austenite phase is not
formed sufficiently during heating in the hot rolling process. Accordingly, even when
hot rolling and hot-rolled sheet annealing are performed under the conditions specified
in the present invention, a desired metal structure cannot be obtained. Therefore,
when Mo is contained, the Mo content is set to be 0.01% or more and 1.00% or less.
When Mo is contained, the Mo content is preferably 0.10% or more, and more preferably
0.30% or more. Furthermore, when Mo is contained, the Mo content is preferably 0.80%
or less, and more preferably 0.50% or less.
W: 0.01 to 0.20%
[0036] W, similar to Mo, has an effect of improving corrosion resistance. This effect is
obtained at a W content of 0.01% or more. On the other hand, when the W content exceeds
0.20%, strength increases, which may cause deterioration in productivity due to an
increase in the rolling load and the like in some cases. Therefore, when W is contained,
the W content is set in a range of 0.01% to 0.20%. When W is contained, the W content
is preferably 0.05% or more. Furthermore, when W is contained, the W content is preferably
0.15% or less.
Co: 0.01 to 0.20%
[0037] Co is an element that improves toughness. This effect is obtained at a Co content
of 0.01% or more. On the other hand, when the Co content exceeds 0.20%, workability
may deteriorate in some cases. Therefore, when Co is contained, the Co content is
set in a range of 0.01% to 0.20%.
V: 0.01 to 0.20%
[0038] V, together with C and N, forms carbonitrides, and by suppressing sensitization during
welding, improves corrosion resistance of welds. This effect is obtained at a V content
of 0.01% or more. On the other hand, when the V content exceeds 0.20%, workability
and toughness may markedly deteriorate in some cases. Therefore, when V is contained,
the V content is set to be 0.01% or more and 0.20% or less. When V is contained, the
V content is preferably 0.02% or more. Furthermore, when V is contained, the V content
is preferably 0.10% or less.
Nb: 0.01 to 0.10%
[0039] Nb has an effect of refining crystal grains. This effect is obtained at a Nb content
of 0.01% or more. On the other hand, Nb also has an effect of increasing the recrystallization
temperature. When the Nb content exceeds 0.10%, there may be a case where the annealing
temperature required to cause sufficient recrystallization in hot-rolled sheet annealing
becomes excessively high, and a metal structure with an average crystal grain size
of 45 µm or less cannot be obtained. Therefore, when Nb is contained, the Nb content
is set in a range of 0.01% to 0.10%. When Nb is contained, the Nb content is preferably
0.05% or less.
Zr: 0.01 to 0.20%
[0040] Zr has an effect of suppressing sensitization by combining with C and N. This effect
is obtained at a Zr content of 0.01% or more. On the other hand, when the Zr content
exceeds 0.20%, workability may markedly deteriorate in some cases. Therefore, when
Zr is contained, the Zr content is set in a range of 0.01% to 0.20%. When Zr is contained,
the Zr content is preferably 0.10% or less.
REM: 0.001 to 0.100%
[0041] Since REM (Rare Earth Metals) has an effect of improving oxidation resistance, it
suppresses formation of an oxide film (welding temper color) in welds, and suppresses
formation of a Cr-depleted region immediately below the oxide film. This effect is
obtained at an REM content of 0.001% or more. On the other hand, when the REM content
exceeds 0.100%, productivity, such as picklability during cold-rolled annealing, may
deteriorate in some cases. Therefore, when REM is contained, the REM content is set
in a range of 0.001% to 0.100%. When REM is contained, the REM content is preferably
0.050% or less.
B: 0.0002 to 0.0025%
[0042] B is an element effective in improving resistance to secondary work embrittlement
after deep drawing. This effect is obtained at a B content of 0.0002% or more. On
the other hand, when the B content exceeds 0.0025%, workability and toughness may
deteriorate in some cases. Therefore, when B is contained, the B content is set in
a range of 0.0002% to 0.0025%. When B is contained, the B content is preferably 0.0003%
or more. Furthermore, when B is contained, the B content is preferably 0.0012% or
less.
Mg: 0.0005 to 0.0030%
[0043] In steel containing Ti as in the present invention, when Ti carbonitrides coarsen,
toughness may deteriorate in some cases. In this respect, Mg has an effect of suppressing
coarsening of Ti carbonitrides. This effect is obtained at a Mg content of 0.0005%
or more. On the other hand, when the Mg content exceeds 0.0030%, surface properties
of steel may deteriorate in some cases. Therefore, when Mg is contained, the Mg content
is set in a range of 0.0005 to 0.0030%. When Mg is contained, the Mg content is preferably
0.0010% or more. Furthermore, when Mg is contained, the Mg content is preferably 0.0020%
or less.
Ca: 0.0003 to 0.0030%
[0044] Ca is an element effective in preventing nozzle blockage due to crystallization of
Ti-based inclusions which is likely to occur during continuous casting. This effect
is obtained at a Ca content of 0.0003% or more. On the other hand, when the Ca content
exceeds 0.0030%, corrosion resistance may deteriorate by formation of CaS in some
cases. Therefore, when Ca is contained, the Ca content is set in a range of 0.0003%
to 0.0030%. When Ca is contained, the Ca content is preferably 0.0005% or more. Furthermore,
when Ca is contained, the Ca content is preferably 0.0015% or less, and more preferably
0.0010% or less.
[0045] A method for manufacturing a ferritic stainless steel sheet according to the present
invention will be described below. The present inventors have performed thorough studies
on a technique of improving toughness in a ferritic stainless steel sheet. As a result,
it has been found that after a steel slab having an appropriate steel composition
is heated preferably at 1,050 to 1,250°C, by performing hot rolling preferably with
three or more passes, and subjecting the resulting hot-rolled steel sheet to hot-rolled
sheet annealing at 750 to 1,050°C, a metal structure with an average crystal grain
size of 45 µm or less can be obtained, and toughness is greatly improved to a Charpy
impact value of 100 J/cm
2 or more at -50°C. Furthermore, it has been found that desired corrosion resistance
can be obtained.
[0046] The reason why a hot-rolled and annealed steel sheet having a fine metal structure
can be obtained by the above technique will be described below. In ferritic stainless
steel, dynamic recrystallization hardly occurs during hot rolling, and recovery of
working strain due to rolling tends to occur. Therefore, in hot rolling according
to existing techniques, excessive recovery of the working strain introduced by rolling
occurs, and the working strain cannot be effectively maintained after hot rolling.
Consequently, recrystallization sites become insufficient, and a fine recrystallized
structure cannot be obtained in the subsequent hot-rolled sheet annealing process.
[0047] Under the circumstances, the present inventors have performed thorough studies on
an effective technique for obtaining a fine structure after hot-rolled sheet annealing
from the viewpoint of both the steel composition and the hot rolling method. As a
result, it has been found that it is effective to control the contents of steel elements,
in particular, Si, Mn, Cr, and Ni, in appropriate ranges and to perform hot rolling
after performing heating of the slab at an appropriate temperature in the hot rolling
process so as to form a dual-phase structure of ferrite phase + austenite phase.
[0048] In the case where the metal structure is formed into a dual-phase structure of ferrite
phase + austenite phase, the interface between different phases, i.e., between the
ferrite phase existing before heating and the austenite phase formed during heating,
suppresses coarsening of crystal grains, and therefore, a fine equiaxed structure
can be obtained in the stage before hot rolling. Then, by performing a suitable hot
rolling operation, working strain acting as recrystallization sites in the subsequent
hot-rolled sheet annealing process is sufficiently accumulated. Thus, a fine metal
structure is obtained in the subsequent hot-rolled sheet annealing process, and excellent
toughness can be exhibited.
[0049] Specifically, regarding steel which is adjusted so as to satisfy the formula (1)
in which the contents of Ni and Mn, i.e., austenite-forming elements, are multiplied
by a positive factor for each of Ni and Mn and the contents of Si and Cr, i.e., ferrite-forming
elements, are multiplied by a negative factor for each of Si and Cr, so that 65% or
more, in volume ratio, of austenite phase is formed during heating before hot rolling,
a method has been devised in which the steel, after being heated as a slab at 1,050
to 1,250°C, is subjected to hot rolling.
[0050] Furthermore, the present inventors have performed thorough studies on the suitable
conditions for the subsequent hot-rolled sheet annealing process. The hot-rolled sheet
annealing process is a process of recrystallizing the worked structure formed by hot
rolling. Therefore, it is necessary to perform annealing at a temperature at which
sufficient recrystallization occurs. However, when hot-rolled sheet annealing is performed
at an excessively high temperature, although recrystallization occurs, recrystallized
grains markedly coarsen. Therefore, a desired fine structure cannot be obtained.
[0051] Accordingly, the present inventors have investigated in detail the relationship between
the grain size of recrystallized grains and the annealing temperature. As a result,
it has been found that by controlling the hot-rolled sheet annealing temperature to
1,050°C or lower, it is possible to suppress formation of recrystallized grains that
are coarse to such an extent that toughness deteriorates.
[0052] The manufacturing conditions will be described in detail below.
[0053] First, molten steel having the composition described above is melted by a known method
using a converter, an electric furnace, a vacuum melting furnace, or the like and
is formed into a steel (slab) by a continuous casting process or an ingot casting-blooming
process.
Steel slab heating temperature: 1,050 to 1,250°C
[0054] The steel slab is heated at 1,050 to 1,250°C and subjected to hot rolling. The heating
time at the heating temperature is not particularly limited, but preferably, heating
is performed for 1 to 24 hours. When the heating temperature is lower than 1,050°C,
the austenite phase formation rate decreases, a fine metal structure cannot be obtained,
and thus excellent toughness cannot be obtained. On the other hand, when the heating
temperature increases excessively, the oxidation mass increases resulting in an increase
in scale loss. Therefore, the steel slab heating temperature is set to be 1,250°C
or lower. However, when a steel slab is subjected to hot rolling, in the case where
the steel slab after casting is in a temperature range of 1,050°C or higher, the steel
may be, without being heated, directly subjected to rolling.
[0055] The rough rolling conditions are not particularly limited. In the case where the
cast structure is effectively destroyed before finish hot rolling, the refinement
effect caused by heating of the slab is further accelerated in subsequent processes.
Therefore, the cumulative rolling reduction in rough rolling is preferably set to
be 65% or more. Then, finish hot rolling is performed until a predetermined sheet
thickness is reached.
Hot-rolled sheet annealing temperature: 750 to 1,050°C
[0056] In the present invention, after the hot rolling is finished, hot-rolled sheet annealing
is performed. In hot-rolled sheet annealing, the rolled structure formed in the hot
rolling process is recrystallized. In the present invention, by effectively imparting
rolling strain in the hot rolling process so that the number of recrystallization
sites increases, coarsening of recrystallization grains in hot-rolled sheet annealing
is suppressed. In order to obtain this effect, it is necessary to perform hot-rolled
sheet annealing at a temperature in a range of 750 to 1,050°C. When the annealing
temperature is lower than 750°C, because of insufficient recrystallization, residual
stress caused by hot-rolling strain remains, and flatness of the steel sheet after
hot-rolling and annealing cannot be maintained. On the other hand, when the annealing
temperature exceeds 1,050°C, recrystallized grains markedly coarsen, and a desired
metal structure cannot be obtained. Therefore, the hot-rolled sheet annealing temperature
is set in a range of 750°C to 1,050°C. Preferably, the hot-rolled sheet annealing
temperature is in a range of 750°C to 900°C. Note that the holding time and the technique
of hot-rolled sheet annealing are not particularly limited, and either box annealing
(batch annealing) or continuous annealing may be performed.
[0057] The ferritic stainless steel sheet thus obtained may be subjected, as necessary,
to a descaling treatment by shotblasting or pickling. Furthermore, in order to improve
surface properties, the steel sheet may be subjected to grinding, polishing, or the
like. Moreover, the steel sheet may be further subjected to cold rolling and cold-rolled
sheet annealing.
[0058] In this way, a ferritic stainless steel sheet having excellent toughness and excellent
corrosion resistance according to the present invention is manufactured.
[0059] The metal structure of the ferritic stainless steel sheet obtained in the present
invention includes a ferrite single phase or includes 3% or less (in volume ratio)
in total of one or both of a martensite phase and a retained austenite phase with
the balance being a ferrite phase.
[0060] The ferritic stainless steel sheet of the present invention has a Charpy impact value
of 100 J/cm
2 or more at -50°C. Because of such excellent low-temperature toughness, occurrence
of cracks in the burring portion can be effectively prevented when worked into a thick
flange having a burring portion, and the steel sheet can be satisfactorily put into
practical use for a thick flange having a burring portion.
[0061] The sheet thickness is not particularly limited, but is desirably a sheet thickness
that can be used for a thick flange. Therefore, the sheet thickness is preferably
5.0 mm or more, and more preferably 8.0 mm or more. Furthermore, the sheet thickness
is preferably 15.0 mm or less, and more preferably 13.0 mm or less.
EXAMPLE 1
[0062] The present invention will be described in more detail below on the basis of examples.
[0063] Molten stainless steels having the compositions shown in Table 1 were each formed
into a 100-kg steel slab by vacuum induction melting. Subsequently, by performing
hot rolling under the manufacturing conditions shown in Table 2, a hot-rolled steel
sheet with the finished sheet thickness shown in Table 2 was obtained. By subjecting
the hot-rolled steel sheet to hot-rolled sheet annealing, a hot-rolled and annealed
steel sheet was obtained. Note that hot-rolled sheet annealing was performed by holding
the steel sheet at the hot-rolled sheet annealing temperature shown in Table 2 for
8 hours. The following evaluations were made on the resulting hot-rolled and annealed
steel sheet.
(1) Evaluation of average crystal grain size
[0064] The average crystal grain size was measured by an EBSD (Electron Back Scattering
Diffraction) method. The measurement conditions were as follows: a magnification,
for measurement, of 500 times, with a step size of 0.4 µm. The obtained data were
analyzed by OIM (Orientation Imaging Microscopy) analysis software developed by TSL
Solutions Ltd., an orientation difference of 15° or more was defined as a grain boundary,
and circle equivalent diameters were calculated. A value calculated from the average
of the circle equivalent diameters was defined as an average crystal grain size.
(2) Evaluation of Charpy impact value
[0065] A V-notch Charpy specimen according to JIS Z 2242 (2005) was taken from the central
part in the sheet width direction of each of the hot-rolled and annealed steel sheets,
without changing the thickness of the steel sheet, such that the rolling direction
corresponded to the longitudinal direction of the specimen. The specimen was tested
in accordance with JIS Z 2242 (2005) to measure a Charpy impact value at -50°C. Specimens
with a Charpy impact value of 100 J/cm
2 or more at -50°C were evaluated as "pass", and specimens with a Charpy impact value
of less than 100 J/cm
2 at -50°C were evaluated as "rejection".
(3) Evaluation of corrosion resistance
[0066] A specimen of 60 × 80 mm was taken from each of the hot-rolled and annealed steel
sheets. After a front surface of the specimen was polish-finished with #600 emery
paper, end face portions and a back surface of the specimen were sealed. Then, the
specimen was subjected to a cyclic salt spray test specified in JIS H 8502. In the
cyclic salt spray test, three cycles were performed, each cycle including salt spraying
(5% by mass NaCl, 35°C, spraying for 2 hours) → drying (60°C, 4 hours, relative humidity:
40%) → wetting (50°C, 2 hours, relative humidity ≥ 95%). After the cyclic salt spray
test was conducted for three cycles, the front surface of the specimen was photographed,
and a rusting area in the front surface of the specimen was measured by image analysis.
From the ratio of the rusting area to the area of a portion in which the rusting area
is measured, the rusting area ratio (rusting area/area of portion in which rusting
area is measured in specimen) × 100[%]) was calculated. The portion in which the rusting
area is measured refers to a portion excluding an outer peripheral portion with a
width of 15 mm of the specimen. Note that the rusting area includes areas of a rusting
portion and a portion subjected to flow rust. Specimens with a rusting area ratio
of 10% or less were evaluated as "pass" (⊙) with particularly excellent corrosion
resistance, specimens with a rusting area ratio of more than 10% and 25% or less were
evaluated as "pass" (○), and specimens with a rusting area ratio of more than 25%
were evaluated as "rejection" (×).
[0067] The test results thus obtained together with manufacturing conditions are shown in
Table 2.
[Table 1]
Steel symbol |
Chemical composition (mass%) |
γI [%] |
Remarks |
C |
Si |
Mn |
P |
S |
Al |
Cr |
Ni |
Ti |
N |
Others |
A1 |
0.007 |
0.26 |
0.25 |
0.03 |
0.002 |
0.03 |
11.7 |
0.85 |
0.24 |
0.009 |
- |
66 |
Example |
A2 |
0.006 |
0.22 |
0.38 |
0.02 |
0.003 |
0.03 |
11.1 |
1.15 |
0.21 |
0.007 |
- |
83 |
Example |
A3 |
0.008 |
0.25 |
0.34 |
0.03 |
0.005 |
0.02 |
11.4 |
1.45 |
0.15 |
0.011 |
- |
86 |
Example |
A4 |
0.005 |
0.17 |
0.38 |
0.01 |
0.002 |
0.02 |
10.8 |
0.77 |
0.13 |
0.011 |
- |
78 |
Example |
A5 |
0.006 |
0.17 |
0.98 |
0.04 |
0.005 |
0.04 |
11.5 |
0.80 |
0.19 |
0.011 |
- |
78 |
Example |
A6 |
0.008 |
0.11 |
0.07 |
0.03 |
0.004 |
0.03 |
10.9 |
0.83 |
0.23 |
0.011 |
- |
76 |
Example |
A7 |
0.006 |
0.33 |
0.45 |
0.04 |
0.005 |
0.04 |
11.3 |
0.82 |
0.15 |
0.011 |
- |
72 |
Example |
A8 |
0.006 |
0.07 |
0.20 |
0.04 |
0.003 |
0.03 |
11.7 |
0.84 |
0.24 |
0.012 |
- |
69 |
Example |
A9 |
0.009 |
0.12 |
0.76 |
0.03 |
0.002 |
0.04 |
12.4 |
1.20 |
0.11 |
0.011 |
- |
75 |
Example |
A10 |
0.010 |
0.21 |
0.38 |
0.04 |
0.005 |
0.04 |
10.3 |
0.79 |
0.13 |
0.007 |
- |
84 |
Example |
A11 |
0.008 |
0.16 |
0.40 |
0.03 |
0.003 |
0.02 |
11.5 |
1.45 |
0.33 |
0.009 |
- |
87 |
Example |
A12 |
0.005 |
0.29 |
0.41 |
0.03 |
0.004 |
0.04 |
10.9 |
0.98 |
0.07 |
0.007 |
- |
80 |
Example |
A13 |
0.008 |
0.15 |
0.39 |
0.01 |
0.004 |
0.02 |
10.2 |
0.76 |
0.22 |
0.011 |
- |
86 |
Example |
A14 |
0.012 |
0.05 |
0.97 |
0.03 |
0.001 |
0.03 |
12.5 |
0.75 |
0.25 |
0.016 |
Cu:0.15 |
68 |
Example |
A15 |
0.009 |
0.14 |
0.25 |
0.03 |
0.004 |
0.04 |
10.5 |
1.40 |
0.14 |
0.011 |
Mo:0.13, Zr:0.16 |
94 |
Example |
A16 |
0.008 |
0.12 |
0.44 |
0.04 |
0.004 |
0.02 |
12.6 |
1.47 |
0.23 |
0.009 |
- |
75 |
Example |
A17 |
0.007 |
0.14 |
0.37 |
0.01 |
0.005 |
0.03 |
11.0 |
1.16 |
0.12 |
0.008 |
Cu:0.95 |
92 |
Example |
A18 |
0.005 |
0.17 |
0.40 |
0.02 |
0.002 |
0.03 |
10.9 |
1.00 |
0.21 |
0.008 |
Mo:0.88 |
72 |
Example |
A19 |
0.005 |
0.26 |
0.42 |
0.01 |
0.002 |
0.03 |
10.9 |
1.17 |
0.11 |
0.010 |
W:0.08, Mg:0.0017 |
85 |
Example |
A20 |
0.006 |
0.19 |
0.45 |
0.03 |
0.004 |
0.03 |
11.0 |
0.99 |
0.09 |
0.011 |
Co:0.11 |
82 |
Example |
A21 |
0.005 |
0.11 |
0.41 |
0.02 |
0.003 |
0.02 |
11.2 |
0.91 |
0.18 |
0.007 |
V:0.10 |
79 |
Example |
A22 |
0.005 |
0.10 |
0.25 |
0.03 |
0.006 |
0.03 |
11.1 |
0.81 |
0.13 |
0.009 |
V:0.04, Nb:0.06 |
75 |
Example |
A23 |
0.006 |
0.21 |
0.42 |
0.03 |
0.004 |
0.04 |
11.0 |
0.85 |
0.26 |
0.011 |
Zr:0.06, B:0.0011 |
78 |
Example |
A24 |
0.010 |
0.11 |
0.42 |
0.03 |
0.002 |
0.04 |
11.0 |
0.86 |
0.13 |
0.008 |
REM:0.007 |
79 |
Example |
A25 |
0.006 |
0.17 |
0.32 |
0.02 |
0.004 |
0.03 |
10.9 |
0.88 |
0.19 |
0.011 |
Co:0.013, B:0.0009 |
79 |
Example |
A26 |
0.010 |
0.13 |
0.30 |
0.03 |
0.005 |
0.02 |
10.8 |
0.78 |
0.11 |
0.010 |
W:0.013, Nb:0.02, Ca:0.0008 |
78 |
Example |
A27 |
0.007 |
0.28 |
0.29 |
0.04 |
0.003 |
0.04 |
11.6 |
0.75 |
0.22 |
0.011 |
- |
65 |
Example |
B1 |
0.013 |
0.28 |
0.32 |
0.04 |
0.003 |
0.04 |
11.8 |
0.77 |
0.10 |
0.010 |
- |
64 |
Comparative Example |
B2 |
0.003 |
0.34 |
0.25 |
0.02 |
0.003 |
0.03 |
12.1 |
0.84 |
0.21 |
0.008 |
- |
60 |
Comparative Example |
B3 |
0.015 |
0.33 |
0.25 |
0.03 |
0.005 |
0.02 |
12.3 |
1.08 |
0.18 |
0.007 |
- |
63 |
Comparative Example |
B4 |
0.009 |
0.08 |
0.73 |
0.04 |
0.004 |
0.04 |
13.3 |
1.25 |
0.21 |
0.009 |
- |
66 |
Comparative Example |
B5 |
0.012 |
0.29 |
1.64 |
0.03 |
0.009 |
0.03 |
10.3 |
0.81 |
0.18 |
0.009 |
- |
98 |
Comparative Example |
B6 |
0.008 |
0.13 |
0.35 |
0.03 |
0.004 |
0.03 |
11.3 |
0.81 |
0.10 |
0.010 |
Nb:0.16 |
74 |
Comparative Example |
B7 |
0.008 |
0.45 |
0.42 |
0.04 |
0.002 |
0.03 |
10.9 |
0.83 |
0.10 |
0.007 |
- |
74 |
Comparative Example |
B8 |
0.008 |
0.16 |
0.39 |
0.04 |
0.003 |
0.03 |
11.7 |
1.30 |
0.42 |
0.011 |
- |
81 |
Comparative Example |
B9 |
0.009 |
0.19 |
0.36 |
0.02 |
0.002 |
0.03 |
11.0 |
0.76 |
- |
0.010 |
- |
75 |
Comparative Example |
B10 |
0.008 |
0.24 |
0.31 |
0.02 |
0.003 |
0.04 |
11.3 |
0.65 |
0.26 |
0.008 |
|
67 |
Comparative Example |
The balance other than the elements in the chemical composition described above consists
of Fe and inevitable impurities. Underlined items are outside the range of the present
invention. |
[Table 2]
No. |
Steel symbol |
Steel slab temperature [°C] |
Finished sheet thickness [mm] |
Hot-rolled sheet annealing temperature [°C] |
average crystal grain size [µm] |
Charpy impact value (-50°C) [J/cm2] |
Corrosion resistance |
Remarks |
1 |
A1 |
1060 |
5.1 |
806 |
43 |
104 |
○ |
Example |
2 |
A2 |
1071 |
5.1 |
820 |
16 |
230 |
○ |
Example |
3 |
A3 |
1063 |
5.1 |
784 |
15 |
233 |
○ |
Example |
4 |
A4 |
1055 |
5.2 |
773 |
37 |
118 |
○ |
Example |
5 |
A5 |
1094 |
5.0 |
824 |
22 |
202 |
○ |
Example |
6 |
A6 |
1114 |
5.2 |
1020 |
31 |
136 |
○ |
Example |
7 |
A7 |
1066 |
5.1 |
753 |
39 |
108 |
○ |
Example |
8 |
A8 |
1096 |
5.2 |
804 |
42 |
114 |
○ |
Example |
9 |
A9 |
1074 |
5.0 |
803 |
32 |
129 |
○ |
Example |
10 |
A10 |
1056 |
5.1 |
812 |
18 |
209 |
○ |
Example |
11 |
A11 |
1098 |
5.1 |
848 |
15 |
247 |
○ |
Example |
12 |
A12 |
1084 |
5.1 |
842 |
21 |
221 |
○ |
Example |
13 |
A13 |
1094 |
5.1 |
788 |
22 |
198 |
○ |
Example |
14 |
A14 |
1106 |
5.2 |
775 |
43 |
105 |
○ |
Example |
15 |
A15 |
1102 |
5.0 |
775 |
10 |
321 |
○ |
Example |
16 |
A16 |
1075 |
5.1 |
838 |
32 |
139 |
○ |
Example |
17 |
A17 |
1055 |
5.0 |
850 |
11 |
297 |
⊙ |
Example |
18 |
A18 |
1117 |
5.1 |
832 |
44 |
110 |
⊙ |
Example |
19 |
A19 |
1114 |
5.1 |
846 |
16 |
238 |
○ |
Example |
20 |
A20 |
1084 |
5.2 |
793 |
23 |
202 |
○ |
Example |
21 |
A21 |
1106 |
5.2 |
823 |
24 |
181 |
○ |
Example |
22 |
A22 |
1132 |
5.2 |
808 |
33 |
131 |
○ |
Example |
23 |
A23 |
1086 |
5.1 |
828 |
26 |
165 |
○ |
Example |
24 |
A24 |
1053 |
5.1 |
811 |
24 |
183 |
○ |
Example |
25 |
A25 |
1087 |
5.1 |
793 |
16 |
241 |
○ |
Example |
26 |
A26 |
1056 |
5.1 |
765 |
25 |
175 |
○ |
Example |
27 |
A27 |
1051 |
5.1 |
760 |
45 |
101 |
○ |
Example |
28 |
A1 |
1077 |
5.2 |
772 |
15 |
220 |
○ |
Example |
29 |
A1 |
1087 |
5.0 |
795 |
8 |
341 |
○ |
Example |
30 |
A1 |
1077 |
5.2 |
761 |
11 |
288 |
○ |
Example |
31 |
A1 |
1148 |
5.1 |
764 |
19 |
221 |
○ |
Example |
32 |
A1 |
1055 |
5.1 |
802 |
45 |
102 |
○ |
Example |
33 |
A1 |
1270 |
5.2 |
827 |
85 |
32 |
○ |
Comparative Example |
34 |
A2 |
1270 |
5.2 |
838 |
60 |
53 |
○ |
Comparative Example |
35 |
A1 |
1056 |
5.2 |
1065 |
141 |
16 |
○ |
Comparative Example |
36 |
A2 |
1082 |
5.1 |
1062 |
110 |
26 |
○ |
Comparative Example |
37 |
B1 |
1133 |
5.2 |
898 |
46 |
96 |
○ |
Comparative Example |
38 |
B2 |
1098 |
5.0 |
810 |
56 |
70 |
○ |
Comparative Example |
39 |
B3 |
1115 |
5.1 |
843 |
48 |
88 |
○ |
Comparative Example |
40 |
B4 |
1095 |
5.2 |
846 |
84 |
32 |
○ |
Comparative Example |
41 |
B5 |
1120 |
5.0 |
847 |
32 |
121 |
× |
Comparative Example |
42 |
B6 |
1147 |
5.1 |
807 |
87 |
15 |
○ |
Comparative Example |
43 |
B7 |
1148 |
5.1 |
843 |
50 |
83 |
○ |
Comparative Example |
44 |
B8 |
1103 |
5.2 |
827 |
47 |
97 |
○ |
Comparative Example |
45 |
B9 |
1086 |
5.1 |
817 |
92 |
10 |
○ |
Comparative Example |
46 |
A1 |
1096 |
12.5 |
765 |
44 |
101 |
○ |
Example |
47 |
B10 |
1101 |
5.2 |
807 |
47 |
95 |
○ |
Comparative Example |
Underlined items are outside the range of the present invention. |
[0068] According to Tables 1 and 2, in Nos. 1 to 32 and No. 46 in which the steel composition,
hot rolling conditions, and hot-rolled sheet annealing conditions are within the ranges
of the present invention, fine metal structures with an average crystal grain size
of 45 µm or less were obtained, and desired Charpy impact values were obtained. Furthermore,
as a result of evaluation of corrosion resistance of the resulting hot-rolled and
annealed sheets, it was confirmed that the hot-rolled and annealed sheets each have
a rusting area ratio of 25% or less, indicating sufficient corrosion resistance. In
particular, in No. 17 which used steel A17 with a Cu content of 0.95% and No. 18 which
used steel A18 with a Mo content of 0.88%, the rusting area ratio was 10% or less,
and thus more excellent corrosion resistance was obtained.
[0069] Furthermore, regarding Nos. 1 to 32 and No. 46 of Examples, when working into the
shape of a thick flange having a burring portion was tried, no cracks occurred, and
it was possible to obtain a predetermined flange shape. Note that structure observation
on the hot-rolled and annealed steel sheets of Examples showed that each of the steel
sheets had a ferrite single phase structure or a structure including 3% or less (in
volume ratio) in total of one or both of a martensite phase and a retained austenite
phase with the balance being a ferrite phase.
[0070] In No. 33 and No. 34 which used steel A1 and steel A2, respectively, and in which
the slab heating temperature was higher than the range of the present invention, although
a required amount of austenite phase was formed during heating in the hot rolling
process and rolling was performed with a required cumulative rolling reduction, since
the rolling temperature was excessively high, recovery of working strain occurred,
and introduction of recrystallization sites was insufficient. Therefore, in the hot-rolled
sheet annealing process, recrystallized grains were likely to be coarsened, and a
predetermined Charpy impact value was not obtained.
[0071] In No. 35 and No. 36 which used steel A1 and steel A2, respectively, and in which
the hot-rolled sheet annealing temperature was higher than the range of the present
invention, formed recrystallized grains markedly coarsened, and consequently, a desired
Charpy impact value was not obtained.
[0072] In Nos. 37, 38, and 39 using steel B1, B2, and B3, respectively, in which the steel
satisfied the composition ranges, but γ
I was lower than the range of the present invention, although hot rolling and hot-rolled
sheet annealing were performed within the ranges of the present invention, as a result
of insufficient formation of austenite phase during heating in the hot rolling process,
the metal structure was not refined sufficiently in the hot-rolled sheet annealing
process, and a predetermined Charpy impact value was not obtained.
[0073] In No. 40 using steel B4 in which the Cr content was higher than the range of the
present invention, although hot rolling and hot-rolled sheet annealing were performed
within the ranges of the present invention, as a result of insufficient formation
of austenite phase during heating in the hot rolling process, the metal structure
was not refined sufficiently in the hot-rolled sheet annealing process, and a desired
Charpy impact value was not obtained.
[0074] In No. 41 using steel B5 in which the Mn content was higher than the range of the
present invention, although hot rolling and hot-rolled sheet annealing were performed
within the ranges of the present invention, MnS serving as a starting point of corrosion
was excessively precipitated. As a result, predetermined corrosion resistance was
not obtained.
[0075] In No. 42 using steel B6 in which the Nb content was higher than the range of the
present invention, since the recrystallization temperature increased, the metal structure
was not refined sufficiently, and a desired Charpy impact value was not obtained.
[0076] In No. 43 using steel B7 in which the Si content was higher than the range of the
present invention, the average crystal grain size of the metal structure exceeded
45 µm, and a desired Charpy impact value was not obtained.
[0077] In No. 44 using steel B8 in which the Ti content was higher than the range of the
present invention, coarse TiN was formed by the excessive Ti content, and a desired
Charpy impact value was not obtained.
[0078] In No. 45 using steel B9 in which Ti was not contained, since the recrystallization
temperature increased, the metal structure was not refined sufficiently, and a desired
Charpy impact value was not obtained.
[0079] In No. 47 using steel B10 in which the Ni content was lower than the range of the
present invention, although hot rolling and hot-rolled sheet annealing were performed
within the ranges of the present invention, as a result of insufficient formation
of austenite phase during heating in the hot rolling process, the metal structure
was not refined sufficiently in the hot-rolled sheet annealing process, and a desired
Charpy impact value was not obtained.
Industrial Applicability
[0080] The ferritic stainless steel sheet obtained in the present invention is suitable
for application requiring excellent toughness, for example, particularly suitable
for use in a flange or the like.